LATEST2 Programme Grant Final Report July 2010 - April 2016

PROGRAMME GRANT FINAL REPORT

latest2@manchester.ac.uk www.manchester.ac.uk/latest2

LATEST2 ProgrAmmE grAnT

The LATEST2 Vision The LATEST2 Programme was aimed at providing the underpinning fundamental research required to facilitate a step change in the application of high-performance, light alloy and multi-material solutions in the transport sector that would lead to a reduction in energy consumption and CO2 emissions. The programme was carefully tailored to meet the needs of industry and provide the supporting research needed to maintain UK global competitiveness in the realignment of manufacturing towards more sustainable transport technologies.

Visibility and reputation The EPSRC LATEST2 Programme Team strived to build the visibility and reputation of the research group, on both the national and international stage. We developed clear and consistent branding across all our communication media and the EPSRC LATEST2 Programme is now internationally recognised. The team hosted a large number of events that have been well-attended with delegates from countries around the world and we will continue to develop the UK’s reputation for research in this field.

Knowledge Transfer and research Translation For the EPSRC LATEST2 Programme to be a successful and sustainable research activity, the team worked hard to develop wider engagement with academic institutions, research organisations and industrial companies across the transport sector supply chain. Since launch, the Programme has been very successful at leveraging additional funding from UK and European Research Councils and industrial companies and the team continues to be committed, both to knowledge transfer and research translation.

Programme management The EPSRC LATEST2 Programme was led by the Programme Director (Professor Phil Prangnell), and supported by the LATEST2 Management Team consisting of the Programme Co-Investigators, the administrative team led by the LATEST2 Programme Manager which included the Programme Administrative Assistant and Science Communication Officer.

The Management Team has been advised by its International Advisory Panel.

conTEnT LATEST2 Programme Grant

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Welcome

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Research Context

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The Research Programme

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Theme 1: Conquering Low Formability for Optimised Design Architectures

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Research Article: Understanding Formability by Observing Deformation at the Microstructural Scale Research Article: Developing Titainum Alloys with Higher Strength and Improved Ductility Research Article: The Assessment and Quantitative Measurement of Formability in Aluminium Alloys Using Digital Image Correlation (DIC) Research Article: Near-Net-Shape and Property Tailoring in Rolled Aerospace Products Research Article: Improving the Quality of Magnesium Castings using Modelling and 3-Dimensional Imaging Research Article: Control of Twinning in Magnesium Alloys Using Precipitates Research Article: Warm Forming of High Strength Aluminium Alloys for Automotive Applications Research Article: Understanding and Improving Formability in Magnesium Alloys

Research Article: Thermomechanical Processing of α+β Titanium Alloy – TIMETAL407

Theme 2: Joining Advanced Alloys and Dissimilar Materials

Research Article: Optimisation of Ultra-Short Cycle Friction Stir Spot Welding for Thin Automotive Sheet Research Article: Critical Assessment of Welding Techniques for Dissimilar Joining of Aluminium to Steel Research Article: Coating Design for Controlling IMC Formation in Dissimilar Al-Mg Metal Welding Research Article: Assessment of the Advantages of Static Shoulder FSW for Joining Aluminium Aerospace Alloys Research Article: Laser Welding of Advanced Aerospace Aluminium Alloys Research Article: Surface Engineering Metal - Composite Hyperjoints Research Article: Understanding Defects in Additive Manufacturing Research Article: Understanding Heterogeneity in Additive Manufacturing with Titanium Research Article: Integration of In-Process Deformation with Additive Manufacture of Ti-6Al-4V Components for improved β Grain Structure Refinement and Texture Control

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Research Article: Environmentally Friendly Surface Treatment for New Generation Aluminium-Lithium Aerospace Alloys

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Research Article: Nanotomography Coupled with RF-GDOES for Evaluation of the Corrosion Performance of Processed Aluminium Alloys

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Research Article: Effects of Sulphur Impurity in Chromic Acid Anodizing of Aluminium

Research Article: Plasma Electrolytic Oxidation of Coupled Light Metals

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Research Article: Electrochemical Testing Coupled with Real Time Imaging Provides a New Tool for Practical Assessment of Anticorrosion Performance

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Research Article: Understanding the Influence of Alloying Elements/Impurity on Corrosion Property of Magnesium Alloys

Research Project List

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Publications and Conference Proceedings

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Prestige, Awards and Invited Lectures

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Human Capital Impact

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IMPACT – Science Communication

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Collaborators

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Management Team

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International Advisory Panel

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LATEST2 Team Members

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Theme 3: Surface Engineering for Low Environmental Impact

Research Article: Impact of Shot Peening Forming on Surface Integrity of Aluminum Alloys Research Article: New Insights into Pore Initiation in Anodic Alumina

Research Article: Anodic Film Formation on a Magnesium Alloy Using a Glycerol-based Electrolyte Research Article: Formation of Electroless Nickel-Boron on Magnesium and AZ91D Alloy Research Article: X-ray Computed Tomographic Investigation of the Porosity of Plasma Electrolytic Oxidation Coatings

wELcomE

Dear All, On behalf of the Management Team, it gives me great pleasure to introduce the final ‘Showcase’ Report for LATEST2 (Light Alloys Towards Environmentally Sustainable Transport: 2nd Generation), a project funded by an EPSRC Programme Grant (EP/H020047/1) from July 2010 – July 2016. Since its inception, LATEST2 has grown organically to become a world renowned centre in Light Metals research. The LATEST2 Team have strived for research excellence and successful knowledge transfer to the academic and industrial communities, as well as to provide a high quality training environment. This report reflects the extensive research undertaken across the breadth of LATEST2’s interdisciplinary themes.

LATEST2 has delivered on all its key objectives and performance indicators. Progress has been beyond expectation, with 110 projects initiated at PhD/RA level (including associated projects), conducted with 43 collaborating organisations (including 33 companies). The total value of £10.95M (£8.1 direct, £2.85 in-kind support) in leveraged funding reflects the importance of research within this field. Over its life time the project has published 391 journal and 99 conference papers, and team members have given 70 invited lectures.

In addition, the Programme has attracted 34 scientific visitors from more than 11 countries. While the project was expanded to include new associated topics, only small modifications were made to the original work plan. In particular, Theme 1 was refocused more towards understanding the fundamental material factors that limit formability in HCP metals and high strength aluminium alloys, and to be less technology driven.

Through fundamental research, in key ‘enabling’ topics, LATEST2 has aimed to provide the underpinning science that will accelerate the introduction of more mass efficient solutions in the transport sector under the three themes of i) Conquering Low Formability, ii) Joining Advanced Light Alloys and Dissimilar Materials, and iii) Advanced Surface Engineering, the main outcomes of which are detailed in this report.

Knowledge transfer has been actively facilitated through workshops and directly to our industrial collaborators’. The impact from the work is focused on manufacturing industries in the aerospace and automotive sectors, defence, and their related supply chains, both in the UK and internationally. LATES2 research is already contributing to the competitiveness of international and UK-based companies involved in producing high-value-added products and will result in a lower future environmental impact from transport.

LATEST2 has also executed a comprehensive “IMPACT� Science Communication strategy through which the Programme engaged with a wide range of audiences to increase awareness of the importance of the research and its industrial application. The Team achieved strong growth in contact numbers, year-on-year, across all target audiences with events designed for schools, the community, industry and academia.

We hope that you enjoy reading this report, and find something of interest. We encourage you to visit our website and join our mailing list so we can keep you informed of further developments and news of future events. We would like to hear from you and have the opportunity to discuss opportunities for collaboration in future Research Programmes.

Yours sincerely,

Professor Philip. B. Prangnell EPSRC LATEST2 Programme Director

rESEArch conTExT LATEST2 And ThE InduSTrIAL LAndScAPE With a turnover of £100 billion and employing around 600,000 people directly and within the supply chain, it is difficult to overstate the importance of aerospace and automotive manufacturing to the UK economy. Our over-dependence on fossil fuels is clearly unsustainable, both in terms of the demand on supply and the effect of the pollution it creates. The world produced approximately 35 billion tonnes of carbon dioxide in 2011, which is double that seen only twenty five years ago. This upward trend can be attributed to the rapid industrialisation of Brazil, Russia, India and China (the BRIC nations) and continued world population growth (Figure 1).

Transport is currently responsible for 14% of global emissions of which road traffic accounts for by far the greatest share.

Airbus predicts a more than doubling of the world passenger airline fleet by 2030 and, while this presents an unprecedented business opportunity with an estimated value of $5 trillion in aircraft orders, this growth rate is unsustainable without a step change in fuel efficient airfcraft designs.

Fortunately, this impending crisis is now being taken seriously by governments and industry. In the EC the automotive sector is on track to reach the 130 CO2 g/km average fleet limit by 2015. However, the next target of 95 g/km by 2020 is far more demanding and there is already talk of a 65 g/km limit by 2050. Other important aspects of sustainability include the impact

of the entire product life cycle, and thus the avoidance of the use of energy intensive materials and manufacturing processes, as well as issues such as resource scarcity, and the need for closed loop recycling.

Energy use in transport is closely linked to vehicle mass and, due to the low energy storage density of batteries, electric vehicles also need to be as light as possible to extend their range to the level where they become a credible alternative.

Materials and manufacturing technology is now advancing at a frenetic pace to meet this challenge, with demand out-stripping the supply of new scientists and researchers across the sector. LATEST2 is thus proud to be involved in the Sheffield-Manchester EPSRC Centre of Doctoral Training (CDT) in Metallic Systems, which is aimed at training industrially focused, PhD graduates, to become the next generation of metallurgical specialists.

In order to reach these ambitious emission reduction targets, applications for light alloys within the transport sector are projected to more than double in the next decade and the trend is accelerating.

However, in many cases the properties and cost of the materials and manufacturing processes are inhibiting progress in weight reduction. In the automotive industry the material mix depends on the intended market position. The high volume sector is currently still dependent on steel intensive

vehicles. At the top end, carbon fibre reinforced composites are increasingly making their presence felt, but until the cost falls below $10 /kg CFRP will not enter the mass car market. In between these two extremes, in order of volume, companies are introducing hybrid steel-light alloy designs, fully light alloy car bodies and light alloy CFRP composite multi-material products. With reducing costs and increasing pressure it is predicted that the higher cost options will move to higher volume production and fully steel vehicle bodies will soon be replaced with a light alloy intensive multi-material approach.

Indeed, the slogan ‘right material, right place’ has become the mantra of many automotive designs teams. Examples include the ultra-high strength boron steel safety cell with aluminium crash members and closure panels used by Daimler in the 2013 S-class, and the CFRP composite-aluminium BMW3i, which incorporates an aluminium intensive chassis, or ‘drive module’, with a carbon fibre body, ‘life module’.

Fig. 2 Comparison of the energy required to produce 1 kg of aluminium, steel and carbon fibre reinforced plastic.

Fig. 1 Annual global CO2 emissions, by sector (Center for Climate and Energy Solutions)

To be able to introduce lighter materials in vehicle designs, there is an increasing focus on offsetting their higher cost by reducing the part count through the use of larger integral components and near-net-shape technologies. A further issue with the use of carbon fibre composites is that they require 286 MJ/kg to produce compared to 23 MJ/Kg for recycled aluminium, and the energy is not easily recoverable as CFRPs cannot currently be recycled into the same product form (Figure 2).

In the aerospace sector metals use is also rapidly changing. The first generation of composite dominated multi-material aircraft that are now entering service still contain over 40% metallic structure, but have a much higher reliance on titanium alloys owing to incompatibility problems between CFRP and aluminium. The greater use of expensive materials like titanium has increased the focus on near-net-shape manufacturing processes, to improve the high buy-to-fly ratio, and similar issues have been highlighted in automotive manufacturing where reducing costs through greater use of integrated structures and new joining technologies is a high priority. New higher performance titanium and aluminium alloys will also be substituted into existing legacy airframe designs to achieve incremental weight savings for many years to come and essential research is required to industrialise potential solutions for replacements to hexavalent chromate corrosion protection treatments, to comply with REACH legislation. In the UK Airbus are investing ÂŁ1 billion in the ‘wing of the future’ to

develop new ultra-efficient wing concepts, an ambitious project in which LATEST2 in is participating.

In this rapidly changing landscape it is essential to develop the knowledge base that supports advanced metals manufacturing. LATEST2 serves this role by providing a fundamental view on strategically important materials issues.

Examples within the three themed areas of forming, joining and surface engineering include: developing crystal plasticity models of important materials like magnesium and titanium so that we can use sound scientific principles to improve formability of higher specific strength materials than are currently used in industry; developing models of interface reaction between dissimilar metals so that we can design alloy compositions, or coating systems, that prevent intermetallic compound formation during welding dissimilar metals like aluminium to magnesium, or titanium; studying the fundamentals of electrochemical oxide growth on metals so that we can tailor surfaces to have better performance in both corrosive environments and for adhesive bonding and paint finishing, with lower energy input processes.

LATEST2 benefits from a multidisciplinary team, which allows an integrated approach to tackling challenging problems. For example, 7xxx aluminium alloys have the potential to deliver yields stresses in excess of 600 MPa and could be used in automotive applications with a substantial weight saving, if we can better understand how to form them with a cost-effective process. However, at the same time, we also need to tackle their poor stress corrosion behaviour particularly when welded, or around self-piercing rivets or fasteners.

Other examples of important topics that benefit from this multidisciplinary approach include: the effect of surface deformation in situations such as forming or rectification on corrosion; protection of heterogeneous microstructures associated with welded joints; the application of microstructure models developed for welding processes to predict product variability in additive manufacturing; and the prediction of the influence of elements accumulating in closed loop recycling on forming and corrosion behaviour.

ThE rESEArch ProgrAmmE

I enjoyed the creative freedom of undertaking academic research with industrial relevance.

Arnas Fitzner, PhD Student

The EPSRC LATEST2 programme's prime goal was to facilitate a step change in weight reduction in transport, by developing the science base required to overcome critical issues inhibiting progress towards second generation, light alloy, multi-material designs. LATEST2 was designed to accelerate the exploitation of new transformative, low energy, environmentally-compliant manufacturing processes, by providing solutions to the important materials challenges and predictive capabilities required by industry.

This required the development of an enhanced fundamental scientific understanding and modelling capability.

As anticipated by LATEST2, the future direction of the transport industry requires more geometrically complex designs with a lower part count and the efficient utilisation of more expensive, lighter alloys. At the same time, industry has to cope with the difficulties presented by the introduction of less formable, higher performance and more recycled materials. These conflicting requirements require a better understanding of the fundamental issues controlling forming, joining and surface engineering of light alloy products, as well as the development of more reliable predictive models.

LATEST2 research has been supported by the development of new approaches to materials analysis, modelling and simulation to facilitate more rapid industrial optimisation, while maintaining cost competitiveness and recyclability. A focus on the use of low energy manufacturing routes and recycled materials was an important aspect of the research, to ensure a competitive cost base as well as a low environmental footprint.

The LATEST2 programme has involved three interacting themes in formability, joining and surface engineering illustrated opposite, which have expanded over the time frame to include other important topics, such as additive manufacturing, accelerated testing and organic coatings.

THEME 1 CONQUERING LOW FORMABILITy • Forming high performance light alloys • Modelling microstructural evolution • Advanced forming processes and techniques • Modelling micromechanics of deformation • Exploiting recrystallization and texture control

THEME 2 JOINING ADVANCED ALLOyS AND DISSIMILAR MATERIALS • Joining for multi-material high performance light alloy structures • Joining dissimilar material combinations • Modelling interface reactions, weld microstructures and performance

SIMULATION AND MODELLING RECYCLABILITY

THEME 3 SURFACE ENGINEERING FOR LOW ENVIRONMENTAL IMPACT • In service protection and cosmetic control • Surface engineering for adhesion (e.g. composite to metal bonding) • Fundamentals of corrosion at all length scales

OUTPUT AND TECHNOLOGY TRANSFER Enabling knowledge for manufacturing advanced light alloy materials and their interfacing in multi-material systems with more complex, mass efficient, design and architecture

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Being part of the LATEST2 research Team was a great opportunity and a decisive step for my career.

Andronikos Balaskas, PhD Student

ThEmE 1 conquErIng Low FormABILITy For oPTImISEd dESIgn ArchITEcTurES Our aim has been to develop the scientific base required for forming advanced light alloy materials, to achieve the more complex shapes required by industry in these difficult materials in a cost effective manner. A key ambition was to develop microstructure sensitive models and intelligently optimise innovative techniques for extending formability in higher strength, lower ductility, materials and recycled alloys.

Whereas formability has been extensively investigated in steel and some automotive aluminium alloys, a new approach has been required for studying warm deformation in high strength alloys and in hexagonal metals (HCP) e.g. titanium, magnesium. This has involved understanding and modelling the development of precipitate distributions and its simultaneous interaction with deformation during warm forming and then extending modelling to describe advanced warm forming processes. For titanium and magnesium, the aim was to clarify the micromechanics of deformation, including twinning processes, for implementation in crystal plasticity models that could capture the influences of microstructural and texture heterogeneity that lead to strain localisation and limit formability.

Another important component of the work in Theme 1 was the control of microstructure during thermomechanical processing, which is essential for good formability. There has been particular focus on the role of particles in recrystallization of aluminium alloys, which is increasingly important as recycled content increases, and on the texture homogeneity of titanium and the control of texture and grain size in wrought magnesium alloys. There has also been a growing activity on microstructural control of additive manufactured titanium material.

The research has been aimed at developing the fundamental science required to underpin the following application areas: Developing models for microstructural evolution, including texture, during themomechanical processing of light alloys.

Extending shape capabilities in conventional cold forming of medium strength aluminium alloys with increased recycled content.

Selection and optimisation of new warm forming operations for high strength aluminium alloys.

Energy efficient, warm forming of HCP materials (magnesium, titanium).

Exploiting recrystallization and texture control to improve formability of HCP metals.

THEME 1: KEy OUTPUTS WITH POTENTIAL FOR HIGH IMPACT From Theme 1, to date, LATEST2 has generated signiďŹ cant industrial and academic interest in the following areas, which have high potential for longer term impact: Development of a new crystal plasticity model that can account for twinning in hcp metals, enabling better texture predictions during thermomechanical processing and forming.

Using computational modelling to show how the texture of hcp metals, like titanium and magnesium, can affect formability by promoting the formation of twin clusters that lead to strain localization.

Development of a new understanding of how precipitation can be used to strengthen magnesium alloys, leading to new strategies for alloy development.

Obtaining the first direct evidence that grain boundary segregation occurs in rare earth element (RE) containing magnesium alloys and that it is crucial to controlling texture, a mechanism which can be exploited without using costly and scarce RE elements.

Discovering that dynamic precipitation can be used to improve the drawability of high strength aluminium alloys, producing a product with a more homogeneous final microstructure.

Demonstrating that the development of substructure in aluminium alloys is directly linked with the strain heterogeneity during deformation, opening the way for the development of new descriptions of the deformed state and microstructure evolution models.

Explaining the effect of particle size on the development of particle deformation zones.

Explaining the role of aluminium on the twinning behaviour of titanium, demonstrating that it actually acts to enhance twinning at small addition levels, informing alloy development.

Measuring strain localization in Ti6Al-4V with sub-micro resolution for the first time and establishing it as a new, powerful tool for comparing the fatigue behaviour of different microstructures.

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Understanding formability by observing deformation at the microstructural scale J. quinta da Fonseca LATEST2, School of materials The university of manchester

The deformation around particles in aluminium is important for formability in two ways. Particles are fundamental for microstructure control during processing as they act as preferential sites for recrystallization and help randomize the texture, which improves formability. At the same time, particles are also preferential sites for void nucleation during failure.

Lawrence Ko, a PhD student in LATEST2, used high-resolution digital image correlation (HRDIC) to study the deformation around small particles during plain strain compression. The results of these experiments, shown in Figure 1, revealed that deformation is highly discontinuous in nature, making the interaction between deformation and particle sensitive to particle size, shape and orientation, aspects of which cannot be captured using current continuum models.

The unique data we can obtain with this approach will be used to develop new models for deformation around particles in aluminium alloys, which can be used to improve recrystallization predictions in an industrial context.

The formability of hexagonal metals like titanium and magnesium is difficult to understand due to their inherent mechanical anisotropy, which evolves rapidly during deformation because of twinning. Furthermore, twinning and strain localization are important to ductility. For example, it is known that adding aluminium to titanium increases its strength but decreases ductility, probably because it leads to more slip localization and less twinning.

During his final year undergraduate project, Albert Smith used HRDIC to observe twinning in-situ and to unravel the details of this important mechanism. As can be seen in Figure 2, this new approach allows us to measure the strain during twinning inside individual grains and quantify slip localization. This work, part of the PhD project of Arnas Fitzner and sponsored by TIMET, aims to explain the effect that aluminium and other common alloy additions have on these mechanisms and help develop new, stronger alloys, with higher ductility and improved formability.

An important part of understanding formability is studying the mechanisms of deformation at the microstructural scale.

Traditionally this has been carried out by post-mortem analysis of deformed samples using TEM and more recently EBSD. Although this provides useful information, it can only show the remnants of deformation, leaving one to speculate about the actual deformation mechanisms.

At Manchester we have developed a new technique that makes it possible to measure strain with sub-micron resolution [1]. This approach relies on the deposition of a very fine gold pattern, which is then imaged during deformation and analysed using digital image correlation (DIC). In LATEST2, this technique has now been used to study two fundamental issues in the formability of light alloys: deformation around particles in aluminium and strain localisation and twinning in titanium.

[1] Fabio Di Gioacchino and João Quinta da Fonseca. 2013. “Plastic Strain Mapping with Sub-micron Resolution Using Digital Image Correlation.” Experimental Mechanics 53 (5): 743–754

Shear strain

Relative misorientation

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Fig. 1 a) Shear strain around a Si particle in an Al-0.1Si alloy and b) corresponding EBSD map of relative misorientation.

Deformation is clearly heterogeneous at the microstructural scale, and the rotations of the lattice are affected by the intensity, density and curvature of the slip bands.

Publications: 1. "Plastic strain mapping with sub-micron resolution using digital image correlation", F. Di Gioacchino, J. Quinta da Fonseca, Experimental Mechanics, 53, 5, 743-754, DOI: 10.1007/s11340-012-9685-2

Fig. 2 Strain maps obtained during the twinning of a Ti-2Al alloy. In a) a 65° compression twin can be seen surrounded by a matrix of zero strain, indicating a hard oriented grain. The map clearly shows the high levels of strain generated by twinning and the deformation in the grain above where the twin impinges. b) shows the strain map moments after, clearly illustrating how deformation in this grain occurs primarily by twin thickening.

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Developing Titanium Alloys with Higher Strength and Improved Ductility A. Fitzner, J. quinta da Fonseca, m. Preuss LATEST2, School of materials The university of manchester Titanium alloys are high strength, lightweight materials that are becoming increasingly important in the aerospace sector where they are a much better match for the composite fuselage than aluminium alloys. Light weighting can be achieved by increasing the strength of alloys but in titanium, increased strength often comes with decreased ductility. This LATEST2 project, a collaboration with TIMET, aims to understand the fundamental strengthening mechanisms in titanium alloys and to help develop new compositions that have higher strengths without sacrificing ductility.

Conventionally studies of deformation mechanisms have relied on ex-situ observations of the microstructure and texture via optical or electron microscopy and x-ray diffraction. However, these only show the effects of deformation, leaving much of the active mechanisms to be divined. In-situ studies using digital image correlation (DIC) are more appropriate to track slip activity during deformation. To achieve a spatial sub-grain resolution, gold features in the nanometer scale (Figure 1, top left) are applied on the sample surface.

The advantage of having small gold particles on the surface of the material is the fact that they enable, for the first time, strain mapping with sub-micron spatial resolution. The downside of the technique is the tremendous effort to record images using electron microscopes. Patterns

obtained using spray paint or etching marks on grain boundaries can be imaged on optical microscopes and are therefore much easier to use, but do not give sub-grain resolution and many of the questions posed by alloy development require sub-grain resolution answers.

Figure 1 shows schematically how the high resolution strain mapping approach works.

The top left image is an electron backscattered image of gold droplets on a polished titanium specimen. The strain map shows 0% strain for the macroscopically unloaded state. The microstructure map from electron backscattered diffraction measurements (EBSD) of this alpha titanium alloy shows equiaxed grains. The colours correspond to the crystal orientation, with blue and green tones representing crystals with the prismatic planes orientated towards the loading direction. Images of the gold droplets were acquired step-wise during compression. In accordance with the deformation of the underlying metal grain, the droplets will move on the imaged

Fig. 1 Starting with a nanoscaled gold pattern (left), used for digital image correlation to evaluate strain localisation (middle) with increasing compressive deformation, which relates to microstructure (right)) development during uniaxial compression.

Acknowledgements: TIMET (Sponsor) with special thanks to Matthew Thomas.

Publications: 1. “The effect of aluminium on deformation and twinning in alpha titanium: the 45° case”, A. Fitzner, D. G. Prakash, J. Quinta da Fonseca, M. Preuss, M. J. Thomas, S. Y. Zhang, Materials Science Forum, 765, 549-553 (2013).

surface. The DIC software DaVis converts these relative movements into displacement vectors which can be differentiated to give strain. Areas without strain stay dark blue, while areas of high strain appear in bright blue, up to yellow-red for higher strains. As the strain increases slip lines 1-10µm apart become apparent. Finally, at 8.7% strain, a big area of strain localisation is present, which was identified as a deformation twin from the EBSD map after the test. The exsitu EBSD microstructure maps represent the microstructural evolution from a bigger area: they are not appropriate to represent the slip activity but show therefore the deformation induced twin lamellas. The twins appear red as the basal plane points towards the loading.

It is thought that the interaction between slip localization and deformation twinning is key to obtaining strong alloys with good ductility and with high resolution strain mapping we can study the mechanism as it happens and understand how it is affected by alloy compositions.

The Assessment and Quantitative Measurement of Formability in Aluminium Alloys Using Digital Image Correlation (DIC) J. quinta da Fonseca and K. Sotoudeh LATEST2, School of materials The university of manchester The aim of the research on formability in LATEST2 is to understand the interplay between microstructural parameters (grain size and distribution, second phase particle distribution, texture, etc.) and the formability of different light alloys. Key to this work is the ability to assess the degree of anisotropy in the material by measuring r-values and building forming limit diagrams (FLDs). In the past, these have been measured by measuring the deformation on grids etched on the surface. These methods, however, provide limited spatial resolution and cannot be used to measure the evolution of deformation during straining, which often provides valuable clues. To overcome these limitations, the testing in LATEST2 will make use of state-of-the-art digital image correlation (DIC) techniques.

DIC is a non-contact optical method of measuring fullfield surface deformation.

With DIC it is possible to make time resolved, in-situ measurements of the full 2D deformation tensor. Since the technique is essentially magnification independent, it can be used to measure deformation development at different scales, opening up the possibility of observing directly how microstructural features affect local deformation.

The formability tests will make use of a 3D version of the method, developed by LaVision, Gรถttingen. Two sets of images of the surface of the specimen are recorded at pre-determined time intervals during testing, using two digital high-speed cameras. These images are then filtered, calibrated and cross-correlated to give deformation data i.e. strains and their distribution and inhomogeneity. Our setup provides a strain resolution of 0.002 with sub mm spatial resolution. Figure 1 shows the setup in our lab. for a LaVision image correlation system and an Erichsen 145/60 Hydraulic sheet forming press.

DIC will be used to compile forming limit diagrams for different materials. FLDs are usually determined by the Nakazima or the Marciniak tests in accordance with ISO 12004. The principle of the Nakazima test uses a hemispherical punch to deform wasted specimens of different widths until failure. The maximum characteristic deformations achievable (before failure) of the different shapes of specimens are determined and thus define the forming limit curve of a material. Figure 2 shows the camera views of a specimen before and

after deformation as well as the strain distribution over a typical Nakazima test sample.

The data, in here, true strains, obtained and calculated by the DIC method are usually presented in a 2D diagram with perpendicular axes where the vertical and horizontal axes give the major and minor principal strains, respectively. This allows the determination of formability limits in different processes such as stretch forming, deep drawing or the combination of both.

Figure 3 below shows a typical forming limit diagram for aluminium alloys.

Fig. 3 a) non-deformed; b) deformed specimen; and c) strain distribution of the deformed sample.

Fig. 2 Shows typical forming limit diagram for aluminium alloys, the red curve delineates the onset of local necking, above which a successful deformation is attainable. Four strain paths/ straining modes (the dashed lines and the vertical axis) are also shown on the diagrams to guide the user. The non-deformed state of an element of the sheet, dotted circle; and the deformed state, unfilled circle and ellipses elongated along the major axis are observable.

Fig. 1 Materials Science Centre, The University of Manchester. Experimental setup including an acquisition computer system and a hydraulic sheet forming press a) Computer system for data acquisition and analysis. b) Ring LED light source. c) High-speed cameras. d) Specimen clamped over the punch. e) Forming press. f) Acquisition system for mechanical data.

Near-Net-Shape and Property Tailoring in Rolled Aerospace Products Phil Prangnell LATEST2, School of materials, The university of manchester In the aerospace industry, many major components are currently machined from hot rolled aluminium plate with a very low level of material utilisation. LATEST2 is working with Primetals Technologies (formerly Siemens VAI Metals), to investigate the metallurgical issues associated with applying advanced rolling mill control-systems to produce thicknesstailored aluminium plates, for application in the aerospace industry. This new approach to rolling can be employed to manufacture nearer-net-shape variable thickness, or tapered sections, which can potentially reduce machining waste of expensive aerospace alloys and increase the plate dimensions achievable from a single DC ingot. In this feasibility study, the potential for rolling tapered, wing skins from advanced Al-Li alloys has been investigated.

In the production of such plates, the main metallurgical challenges surround the necessity to stretch the plates after solution

treatment, to reduce residual stresses and optimise the microstructure through precipitation of the dislocation nucleated, main strengthening phase, TI. FE modelling and simulation with digital image correlation was performed to show that it has been possible to achieve a greater than 2% stretch in the entire plate with the required skin blank taper (Figure 1) without fracture, but this would lead to a much higher pre-stretch in the range of up to 15% at the thin end of the plate.

Following on from this analysis, a detailed investigation was performed on the effect of excessive stretching on the properties and microstructure evolution in a typical 3rd generation, high strength, aerospace alloy, 2195. This work has come to some exciting and important conclusions. Firstly, it has been found that by increasing the pre-stretch, to far higher levels than are currently used in industry, a large increase in strength could be achieved after artificial

Fig. 1 Simulation of the effect of stretching on the plastic strain distribution in plates with different roll-taper ratios.

ageing, above that expected. For example, the benefits of pre-stretching were previously thought to saturate at relatively low strain levels of < 6%. However, on pre-stretching to 15% the yield strength of the AA2195 alloy investigated was found to continue to increase to 670 MPa, compared to 580 MPa with the standard stretch and T8 temper. Although this resulted in a reduction in ductility (Figure 2), elongation to failure retained was still within the range acceptable for application in a compressiveloaded top wing skin. As well as this study being successful in demonstrating it is possible to produce nearer-net-shape sections by rolling, it has also shown that extending the pre-deformation prior to ageing can be exploited so that the properties can be improved and locally tailored within products: for example, to produce higher strength at a wing tip and greater damage tolerance at the root.

Fig. 2 Effect of excessive stretching on the yield Stress (0.2% proof), tensile strength and ductility (plastic strain to failure) of AA2195 in its final T8 Temper AA2195.

The origin of the strength improvements found has also been studied in this project.

Detailed analysis using XRD line broadening measurements and TEM showed that a continual increase in dislocation density with pre-strain and a very uniform dislocation distribution were seen in the 2195 alloy, even at very high pre-strain levels. The XRD results indicated a surprisingly low reduction in dislocation density after artificial ageing, implying that recovery is greatly inhibited in alloys like 2195. This has been attributed to strong solute interactions between dislocations and the Cu and Mg in solution, as well as the strong segregation of Cu and Mg to, and the nucleation of TI plates on, dislocations during the early stages of artificial ageing.

Measurements from STEM images revealed a continued decrease in the TI plate’s average diameter, as well as a narrowing of their size distribution and an increase in number density, with increasing pre-strain levels up to 15% (Figure 3). The spatial distribution of the TI phase was also found to reflect the uniform dislocation density still seen in the samples subjected to large pre-strains. Good agreement was found between the experimental results and predictions of the effect of pre-stretch on the upper bound strain hardening and precipitation hardening contributions to the alloy’s yield stress (Figure 4). Modelling has shown that the strength contribution from precipitation hardening actually decreases with increasing pre-stretch, owing to the

Fig. 3 Effect of pre-strain on T1 phase refinement; (a) and (b) STEM HAADF images showing in the T8 condition for 3% and 15% pre-strain, respectively, (c) Eevolution of the average plate diameter and number density with increasing pre-strain.

stronger dependence of the obstacle strength on the plate diameter relative to the precipitate density. In contrast, due to the low level of recovery, the contribution from strain hardening increased parabolically with pre-stretch.

Thus, while previous research has attributed the increase in yield strength seen in alloys like AA2195 with increased pre-strain to an increase in the number density of TI precipitates, the results here suggested the opposite. In that, there is a reduction in the TI strengthening contribution with increasing levels of pre-strain and the increase in strength that results from high levels of pre-strain is a consequence of the high level of strain hardening retained in the material following artificial ageing.

Fig. 4 Effect of Pre-Strain on the main components contributing to the yield strength in the T8 temper, as a function of pre-strain.

Partners: Primetals Technologies , Constellium Acknowledgements: Ben Rodgers (PhD Student) Publications: 1. “Quantification of the influence of increased pre-stretching on microstructure-strength relationships in the Al-Cu-Li alloy AA2195”, P. B. Prangnell, B. I. Rogers, Acta Materialia, In press (2016).

Improving the Quality of Magnesium Castings using Modelling and 3-Dimensional Imaging d. mackie1, J. d. robson1, P. J. withers2, m.Turski3 LATEST2, School of materials, The university of manchester 2 henry mosely x-ray Imaging Facility, The university of manchester 3 magnesium Elektron, manchester

1

Magnesium alloys are increasingly being considered for critical structural parts in aerospace and automotive applications due to the weight saving potential associated with their use in place of aluminium or steel. Key to realizing this potential is the development of processing methods that reliably produce components that are free from internal defects that could produce premature failure. The magnesium industry is increasingly making use of nondestructive testing methods such as ultrasonic inspection to ensure that as-cast magnesium billets can meet the stringent requirements demanded by aerospace industry regulation. At present this results in scrapping a large number of defect containing billets, which adds a significant and undesirable penalty to the alloy production cost. A key difficulty is that little is understood about the nature and source of the defects that lead to failure during ultrasonic inspection.

A study of the liquid metal filtering used in the casting process and a simulation of the metal flow (Figure 3) and intermetallic evolution was used to understand the origins of the defects during casting. It was demonstrated that the agglomeration of the oxide and coarse intermetallics, which is particularly undesirable, was produced by a trawling effect as the oxide circulates in the melt pool. The model was used to develop a better casting procedure that provided an improved metal flow path. This was tested and demonstrated to greatly reduce the incidence of oxide becoming trapped, and thus significantly reduce failure rates at ultrasonic inspection.

Fig. 2 Slice from serial sectioning experiment revealing a gas pocket trapped between oxide films in a magnesium casting.

The purpose of this work was to use 3-dimensional imaging methods such as X-ray tomography and serial sectioning to understand in detail the nature of the defects that form in magnesium alloy castings, and then use modelling and targetted experiments to improve the processing to reduce the incidence of such defects.

Material containing defects, as identified by ultrasonic inspection, was isolated and examined using 3-dimensional X-ray tomography across a range of length scales.

A tomography image of one of the larger defects inspected is shown in Figure 1. It was found that these defects consisted of two main features; an entrained oxide film surrounded by an agglomeration of large intermetallic particles which were identified

by EDX analysis as insoluble Al-Mn phase (Al8Mn5). Serial sectioning using focussed ion beam milling (FIB) revealed further details, showing that the oxide films contained trapped pockets of gas (Figure 2); it is these trapped pockets that lead to a strong signal response in ultrasonic inspection.

Fig. 1 X-ray tomography image showing a large defect in a magnesium alloy casting. Green regions indicate entrained oxide film, blue indicates large Al8Mn5 intermetallic particles.

Fig. 3 Simulation of liquid metal circulation in the sump during casting showing velocity vectors.

Acknowledgements: This LATEST2 associated project was performed through the EngD centre for advanced manufacturing and processing with support from Magnesium Elektron.

Publications: 1. "Analysis of Casting Defects in Magnesium-Aluminium-Zinc Direct Chill Castings by X-Ray Tomography", D. Mackie, J. D. Robson, P. J. Withers, and M. Turski, TMS (2012) 2."Study of Defects in Direct Chill Magnesium Castings Using X-Ray Tomography", D. Mackie, J. D. Robson, P. J. Withers, M. Turski, T. Wilks, EuroMat 2011, France (2011) 3. â&#x20AC;&#x153;Characterisation and modelling of defect formation in direct-chill cast AZ80 alloyâ&#x20AC;?

D. Mackie, J. D. Robson, P. J. Withers and M. Turski, Materials Characterization, 104, 116-123, DOI: 10.1016/j.matchar.2015.03.033 (2015).

Control of Twinning in Magnesium Alloys Using Precipitates J. d. robson1, n. Stanford2, m. r. Barnett2 LATEST2, School of materials, The university of manchester, uK 2 centre of Excellence in Light metals, deakin university, Australia

1

Poor low temperature formability and tension/compression asymmetry are often observed in wrought magnesium products and are detrimental to performance. The origin of these effects is now well understood, and is due to the large differences in critical resolved shear stress (CRSS) for the deformation systems operating in the hexagonal crystal. As a result the strength in directions in which easy deformation modes (basal slip and {10-12} c-axis tension twinning) can be activated is low compared to strength in directions where the resolved shear stress for these systems is low.

One potential method to reduce asymmetry and increase formability is to directly suppress twinning by strengthening this

deformation mode, whilst promoting alternative slip deformation modes. The current work explores the potential to use precipitates to achieve this objective. On a fundamental level it also aims to better understand the interactions between precipitation and twinning in hexagonal (hcp) metals, a subject that has to date received little attention in the literature but is critical to the performance of most commercial hcp alloys.

In this work, magnesium alloys known to form precipitates of different shape and habit were tested before and after precipitation treatment to study the effect of precipitation on asymmetry and explore in detail how precipitates and twins interact. It was shown (Figure 1) that

precipitation in some alloys (e.g. AZ91) leads to a reduction in asymmetry, whereas in other alloys (e.g. Z5) precipitation increases asymmetry. Detailed microscopy was used to explore how precipitates inhibit twin growth. Figure 2 shows an example of a basal plate precipitate in AZ91 entering a twin and becoming elastically bent, which introduces an additional back stress inhibiting propagation of the twin.

Based on this understanding a model was developed to predict which precipitates are most effective at reducing asymmetry whilst also increasing alloy strength. The model can be used to produce strengthening maps (e.g. Figure 3) that can be used to predict the precipitate balance needed to meet given property goals.

Fig. 2 Stress-strain curves of AZ91 extrusion tested in compression and tension. In the precipitate free case, the compressive strength is low due to twinning leading to a high level of mechanical asymmetry.

After precipitation, twinning is suppressed and asymmetry reduced.

Fig. 1 TEM micrograph showing a plate shaped precipitate in the matrix (M) entering a twin (T) and becoming deflected due to the imposed shear.

Acknowledgements: This work was carried out with the support of a Global Research Fellowship from the Royal Academy of Engineering (JDR).

Publications: 1. "Reducing Mechanical Asymmetry in Wrought Magnesium Alloys", J. D. Robson, Materials Science Forum, 765, 580-584, DOI: 10.4028/www.scientific.net/MSF.765.580 (2013).

2. "On the impact of second phase particles on twinning in magnesium alloys”, M. R. Barnett, N. Stanford, J. Geng, and J. D. Robson, 2011, in TMS 2011, 289-293 (2011).

3. “Effect of precipitate shape on slip and twinning in magnesium alloys” J. D. Robson, N. Stanford, M. R. Barnett, Acta Materialia, 56 (5), 11, DOI: 10.1016/j.actamat.2010.11.060 (2011).

4."Effect of particles in promoting twin nucleation in a Mg–5 wt.% Zn alloy", D. Robson, N. Stanford, M. R. Barnett, Scripta Materialia, 63 (8), 823-826, DOI: 10.1016/j.scriptamat.2010.06.026 (2010).

Fig. 3 Model predicted strengthening map showing the effect of different mixtures of the three main precipitate types observed in magnesium.

Warm Forming of High Strength Aluminium Alloys for Automotive Applications r. nolan, P. B. Prangnell and J. quinta da Fonseca LATEST2, School of materials, The university of manchester Weight saving is a powerful strategy for improving energy efficiency in transport applications. In the automotive industry, this can be achieved by replacing steel with composite materials and light alloys like aluminium and magnesium. At the moment, light alloys have cost advantages and are much easier to reuse and recycle than composites materials. Current automotive aluminium alloys are based on 6xxx precipitation hardened alloys. There is an interest in replacing these with higher strength 7xxx aerospace alloys. However, their applicability to the automotive sector is currently limited by their lower ductility, which hampers formability, and stress corrosion cracking (SCC) susceptibility in their peak-hardened condition.

A Fig. 1 Tensile test results for Al 7021 tested at different temperatures in the (a) T4 condition and (b) T6 condition.

The low formability of 7xxx alloys is a direct consequence of their unstable microstructure. In these alloys, precipitation happens at room temperature, strengthening the material, but also reducing its ductility. One way to avoid the difficulties generated by precipitation is to form the material hot, right after solution heat treatment. This is not only difficult to control, it also produces an undesired microstructure that needs further heat treatment and which is susceptible to SCC. In this project, a collaboration with Constellium, we explored the possibility of warm forming between 150 and 250째C, well below the recrystallization temperature but at the temperatures at which precipitation occurs. The aim was to understand the impact of dynamic precipitation on formability and on the final microstructure and associated hardness. The material was tested in the T4 (naturally aged) and T6 (peak aged conditions) in uniaxial and biaxial tension at different temperatures. Cup drawing was used to determine drawability.

B

Tensile testing showed that peak ageing increases the room temperature (RT) strength, but reduces the work hardening ability, resulting in a lower elongation to failure, as can be seen in Figure 1.

Increasing the testing temperature has a drastic effect on the strength of the T6 condition and reduces the work hardening ability further but the ductility increases due to an increase in the extent of stable necking. In the T4 condition, the effect of temperature on both strength and ductility is much more unpredictable. Increasing the temperature to 150째C reduces the strength considerably, however, further increasing the temperature leads to an increase in the flow stress, peaking at 220째C, although the work hardening ability is significantly decreased. Despite this, the ductility is highest at this temperature, which, as in the T6 condition, is a consequence of an extended period of stable necking. Biaxial tensile testing showed that ductility in the biaxial condition varied in a similar way.

Warm cup drawing tests with a cold punch revealed that the T4 material shows superior drawability at all temperatures, except at 250°C, at which both materials show similar behaviour, as can be seen in Figure 2. In the T4 condition, drawability at 190 °C was significantly better than at 170°C and 220°C. This increase in drawability was accompanied by a noticeable increase in the hardness after drawing, shown in Figure 3, with the T4 material showing hardness comparable to that of the T6 tested at the same temperature.

Fig. 2 Maximum draw depths for a 110mm disk.

30 mm corresponds to a fully drawn cup.

Microstructural studies revealed that this was a result of the strong interaction between precipitation and deformation, which peaks at 190-200°C. The typical deformed microstructure in this material is shown in Figure 4. This not only enhances drawability and produces a strong final product, but also leads to a very homogeneous precipitate distribution (Figure 5), which will be beneficial for SCC performance.

Fig. 3 Comparison of the hardness of the drawn material at the top of the cup and the wall. Note that after drawing at 190 °C the hardness is higher than after drawing at RT and comparable to the material deformed at 220 °C.

Fig. 4 Dark field TEM image of the material drawn at 190 °C showing the different precipitates and their interaction with a dislocation.

Fig. 5 High resolution SEM images of the T4 and T6 microstructure. The T6 material shows obvious grain boundary precipitation and denuded grain boundaries.

Acknowledgements: David Strong, Research Technician, School of Materials, The University of Manchester.

Understanding and Improving Formability in Magnesium Alloys Joseph robson, Sarah haigh, david griďŹ&#x192;ths LATEST2, School of materials, The university of manchester The increased use of magnesium for weight reduction in wrought products such as automotive body sheet is hampered by its poor room temperature formability. It is now well established that this formability can be improved by modifying the texture.

This texture modification can be achieved by adding a small (often <0.1wt%) addition of rare-earth (RE) elements [1]. However, REs are expensive with concerns about security of supply. Therefore it is desirable to find alternative, lower cost methods to achieve the same effect. This first requires the RE texture effect to be understood so that it can be replicated.

Fig. 1 Rare earth (RE) elements used to produce Mg-RE alloys in this work.

Binary Mg-RE alloys were produced with a range of different RE elements. These alloys were chosen to cover a range of solubilities and size misfit since these are both believed to be important factors in the RE texture effect. Figure 1 plots these parameters for all REs and shows the binary systems that were selected. These alloys were rolled and annealed to study recrystallization and texture evolution.

Studies using the unique TITAN G2 80-200 ChemiSTEM in the School of Materials have proved that segregation of RE elements to grain boundaries is critical to produce the suppression of DRX and the texture change effect. Figure 2 shows an example of Y segregation on a grain boundary in Mg-0.15 at% Y alloy. High-resolution images (Figure 2c) demonstrate that the RE forms very small clusters at the boundary.

It has been demonstrated that an essential function of the RE additions is to suppress dynamic recrystallization (DRX) during hot deformation. This enables static recrystallization from deformed material with a greater spread of orientations.

When this segregation does not occur, even in RE containing alloy, the RE texture is not produced. Using the high resolution EDX system on the TITAN ChemiSTEM, a semi quantitative estimate of the RE concentration on the boundary has been possible for the first time; it has been shown for Y that the boundary concentration is approximately 20 times that in bulk.

Fig. 2 Y distribution on a grain boundary in Mg-0.15at%Y alloy HAADF STEM images and EDX composition map (a-c) increasing magnification showing clustering of Y on the boundary.

The effect of RE segregation on grain boundary drag has been explored using the classical Cahn-Lücke-Stüwe (CLS) model [2].

From this, processing maps can be predicted showing regions of temperature and boundary velocity where SRX and grain growth will be suppressed by RE addition (Figure 3). The model predictions support the hypothesis that for typical processing conditions RE segregation does not provide enough boundary drag to prevent SRX but will suppress grain growth, enabling a desirable fine grained structure with a weak texture to be obtained after processing.

Summary It has been proven that strong segregation of RE elements to grain boundaries is an essential requirement to produce the weaker characteristic RE texture in magnesium alloys that leads to improved formability. This segregation also explains why RE can be effective even when added in low concentrations. The work suggests that other elements with a strong tendency to segregate could produce a similar texture effect without the need for expensive RE additions. Recent work on Mg-Ca alloys suggests this is indeed the case.

Fig. 3 Predicted boundary drag map showing regions where addition of Y will lead to a drag pressure that suppresses static recrystallization (Pd>Prex) or grain growth Pd>Pgg.

Acknowledgements: This LATEST-2 associated project was performed through the EPSRC Centre for Doctoral Training in Advanced Metallic Systems with support from Magnesium Elektron.

Publications: 1. "Explaining texture weakening and improved formability in magnesium rare-earth alloys", D. Griffiths, Materials Science and Technology, Volume 31, 1, 10-24, DOI: 10.1179/1743284714Y.0000000632 (2015).

2. “Effect of rare-earth additions on the texture of wrought magnesium alloys: the role of grain boundary segregation”, J. D. Robson, Metallurgical and Materials Transactions A 45 (8), 3205-3212, DOI: 10.1007/s11661-013-1950-1 (2014).

3. “Grain boundary segregation of rare-earth elements in magnesium alloys”, J. D. Robson, S. J. Haigh, B. Davis, D. Griffiths, Metallurgical and Materials Transactions A, 47 (1), 522-530, DOI: 10.1007/s11661-015-3199-3 (2016).

Thermomechanical Processing of α+β Titanium Alloy – TIMETAL407 gaurav Singh1, J. quinta da Fonseca1, m. Thomas2, m. Preuss1 The university of manchester, School of materials, manchester, uK 2 TImET uK, Po Box 704, witton, Birmingham, uK

1

Thermomechanical processing of titanium alloys is essential to generate products with tailored microstructures and a balance of strength, improved damage tolerance, and fatigue resistance. For example, fine equiaxed or bi-modal microstructures are obtained by deformation and annealing in the α+β phase field. The crystallographic texture depends greatly on the temperatures used and on the relative phase fraction during deformation.

Recently, TIMET’s Henderson Technical laboratory in the US, in collaboration with TIMET UK, developed a new α+β titanium alloy, TIMET407 (or Ti407) for applications requiring a high degree of energy absorption and manufacturability. TIMET are now collaborating with LATEST2 to study the microstructure evolution during thermomechanical processing of this new alloy. The aim of this project is twofold: to quantify the evolution of microstructure and deformation texture during thermomechanical processing and to determine an effective process window for this new alloy.

Ti407 blocks in the β-annealed condition were uni-directionally rolled at two temperatures, 820 and 650 °C, to 50 and 75% reductions in thickness in multiple passes with intermediate reheating between each pass. Subsequently, after rolling at the two temperatures, blanks were recrystallized annealed at 820 °C for 8 h. The microstructures obtained after rolling and annealing are shown in (Figure 1) demonstrating that spherodisation was only achieved when the material was rolled at 650 °C to 75% reduction.

The driving force for static spherodisation depends upon the stored energy during deformation which, in turn, depends on the extent of deformation and the deformation temperature. From these results, it appears that only the material rolled to 75% at 650 °C had the required stored energy for complete spherodisation.

The texture of the rolled materials is shown in (Figure 2). Two major texture components were identified – one is the transverse texture and the other is a texture in which <c> axis is tilted ~30 ° from the normal direction towards RD. Rolling and annealing Ti407 to 50 and 75% at 820 °C, gave dominance to a transverse texture with 4-6 X random pole intensity (Figure 2a and 2b).

On the other hand, rolling Ti407 to 50% at 650 °C and annealing at 820 °C led to a weak transverse texture component while the tilted basal-normal texture component strengthened to 5-7 X intensity. The transverse texture component completely vanished when Ti407 was rolled to 75% at 650 °C and annealed at 820 °C.

.

Fig. 1 Optical micrographs of Ti407. Rolled at 820 °C to (a) 50 and (b) 75% reduction and annealed at 820 °C. Rolled at 650 °C to (c) 50 and (d) 75% reduction and annealed at 820 °C.

Fig. 2 (0002) and (101 ¯0) α-phase pole figures of Ti407.

Rolled at 820 °C to (a) 50 and (b) 75% reduction and annealed at 820 °C. Rolled at 650 °C to (c) 50 and (d) 75% reduction and annealed at 820 °C.

It is well known that hot workability of titanium alloys decreases rapidly with falling temperature. Thus, the processing window for titanium alloys is usually narrower in than in conventional steel and Al alloys. A processing map of Ti407 was constructed for the determination of optimum hot working conditions. Maps of power dissipation and deformation instability for Ti407 were generated at a strain of ε = 0.5 and are shown in (Figures 3a and 3b), respectively.

These maps show different peaks and valleys of η and ξ (where η is the deformation efficiency and ξ is the instability parameter), which signify different deformation mechanisms operating at different combinations of T and ε .̇ A domain in these maps is defined as the window over the values of η and ξ are high and constant. From the processing map, four domains could be identified: I-A- T= 825-875 °C, ε ̇= 10-1 s-1, η = 45-65, ξ= positive; II-A- T= 725-775 °C, ε ̇= 10-2.3-10-0.8 s-1, η = 30-35, ξ= positive; III-A- T= 680-720 °C, ε ̇= 10-3-10-2.6 s-1, η = 35-40, ξ = negative; and I-B- T= 900-950 °C, ε ̇= 10-3 s-1, η = 40-65, ξ= positive.

Microstructural analysis of the deformed samples in these domains was then carried out to determine the key microstructural features. Domain I-A is characterized by peak efficiency of 65% and a positive ξ value. Microstructural analysis in domain I-A indicates dynamic spherodisation (Figure 4c), where the α lamellae are sheared during deformation and subsequently spherodise during annealing by diffusion controlled process to minimize the surface energy.

Fig. 3 (a) Power dissipation and (b) instability maps of Ti407.

Microstructures of Ti407

Domain II-A is associated with low values of η varying between 30-35%. In this domain partial spherodisation of the α lamellae occurred with no formation of flow instabilities. Ti407 exhibited flow instability only in domain III-A, which was manifested in flow localization bands, kinking and bending of α laths (Figure 4d). Processing of the alloy above the β-transus regime, i.e., in domain I-B, showed a peak efficiency of 65% with dynamic recovery as the rate controlling mechanism.

Acknowledgements: David Strong, Research Technician, School of Materials, The University of Manchester.

Fig. 4 (c) domain I-A and (D) III-A, flow localization and kinking of α laths are highlighted with broken rectangles.

I joined LATEST2 because I wanted to work with leading academics.

Liam Dwyer, PhD Student

ThEmE 2 JoInIng AdVAncEd ALLoyS And dISSImILAr mATErIALS The main aim of Theme 2 was to develop the underpinning metallurgical science required to support cost effective, routes for joining advanced high strength light alloys and multi-material structures. Key areas requiring solutions included; the poor weldability of high strength alloys, interfacial reaction between dissimilar metals, thermal damage, distortion and residual stress, as well as the issues associated with manufacturing metalcomposite hyper joints. Theme 3 also contributed to the Joining topic, through improving current knowledge of tailoring oxide films on metal surfaces for improved adhesion and investigating the protection of dissimilar material joints, where galvanic coupling is a major issue.

The dissimilar metal combinations required by industry, e.g. Al-steel, Mg-Al, Al-Ti, are very difficult to join by traditional fusion welding methods. We have thus focused on low energy friction joining processes, for dissimilar metal combinations, and advanced surface engineering to facilitate adhesive bonding and composite to metal joining (Theme 3). Solid state friction welding techniques are highly efficient and have the advantage of far greater weldability and reduce the risk of interfacial reaction when welding dissimilar materials.

New advances in welding technology that were targeted included, friction stir spot welding (FSSW) stationary shoulder friction stir welding (SSFSW), and high power ultrasonic spot welding (USW), in conjunction with selected fusion welding techniques, such as laser conduction spot and conventional laser seam welding.

A key aspect of the theme was to develop models to predict the microstructure and mechanical behaviour of welds in highperformance multicomponent alloys. We have also developed a better understanding of the thermodynamic and kinetic factors that affect the metallurgical reactions between dissimilar metals in welding, which has enabled us to develop strategies for inhibiting detrimental interactions, such as the formation of brittle intermetallic layers at the weld interface.

The research has been targeted at under pinning the following application areas: Energy efficient joining of Mg and Al in automotive bodies.

Friction welding advanced alloys for aerospace structures with new welding techniques.

Friction welding dissimilar metal combinations requiring control of interfacial reaction (e.g. Al to galvanised steel, Ti to Al).

Low heat input laser welding light alloys and dissimilar metals.

High performance metal-composite joints; facilitated by manufacturing mechanical locking features on the metal surface to increase shear transfer (so called hyper-joints).

Surface engineering to facilitate adhesive bonding (Theme 3) Modelling joint performance through linking process models to microstructure and weld zone property predictions.

Microstructure optimisation of additive layer manufacturing higher performance aerospace components.

THEME 2: KEy OUTPUTS WITH POTENTIAL FOR HIGH IMPACT From Theme 2, to date, LATEST2 has generated signiďŹ cant industrial and academic interest in the following areas, which have high potential for longer term impact: Delivery of a full description of the performance of titanium hyper-pins for metal-composite joining and the development of a new, cheaper, more effective method of manufacturing hyper-pin arrays.

Systematic assessment of new friction stir spot welding technologies for joining aluminium automotive alloys and using fundamental process understanding to develop new techniques for high speed welding (<1 second).

Development of friction spot welding technologies capable of producing high integrity joints between dissimilar metals (aluminium to steel).

The development of integrated process and microstructure models, in collaboration with industry, that predict joint performance in light alloy welds, including in laser and friction welding.

The development of integrated process and microstructure models that predict intermetallic reaction rates in dissimilar metal joints.

The development of new coating systems for controlling intermetallic reaction in dissimilar joints in highly reactive systems (e.g. Al-Mg) and for the first time demonstrating a viable welding technology for Al to Mg spot welds.

The development of models capable of predicting joint performance in high strain rate conditions and the application of these models to predicting blast performance of aluminium armoured vehicles, in collaboration with DSTL. Development of 3D defect quantification and automated microstructure heterogeneity measurement tools, to provide funadamental processunderstanding and aid industrial partners (Airbus, GKN, Rolls-Royce) in qualifying additive manufacturing processes for aerospace components.

Optimisation of Ultra-Short Cycle Friction Stir Spot Welding for Thin Automotive Sheet Phil Prangnell LATEST2, School of materials, The university of manchester Friction stir spot welding (FSSW) (Figure 1a) is a low heat input solid-state process highly suitable for joining difficult-to-weld high strength aluminium alloys and for forming joints between dissimilar materials.

However, the standard process has not been widely adopted in the automotive industry due to a number of problems, which include too long a weld cycle time and the formation of a â&#x20AC;&#x2DC;key holeâ&#x20AC;&#x2122; from the plunge of the tool probe that causes cosmetic issues and weakens the joints. Research in LATEST2 has used a range of techniques,

including 3D tomography, to gain a better understanding of the material flow in FSSW (Figure 2), as well as thermal and microstructure modelling, to try to optimise friction spot welding processes for forming more rapid and higher quality welds in thin aluminium sheet.

This work has shown that the probe on the tool used in conventional FSSW is not necessary in thin sheet welding. By removing the probe from the tool (Figure1b), we have demonstrated that it is possible to weld faster, simplify the process,

and solve the keyhole issue. We have shown that high quality welds can be produced within 1 second using a pinless tool that has been redesigned to reduce slip with the sheet top surface (Figure 2). As an added advantage, the more rapid welding cycle leads to little heat affected zone damage and after a paint bake cycle the welds become stronger than the parent material, due to the positive effect of the shorter natural ageing time of the weld zone on the artificial ageing kinetics (Figure 3).

Fig. 1 Schematic diagrams of (a) conventional friction stir spot welding (FSSW), (b) Pinless FSSW and (c) the Refill FSSW processes.

Fig. 3 Hardness distributions across FSSW produced in 0.5 seconds, immediately after welding and following natural ageing and the paint bake cycle.

Fig. 2 Examples of flow studies of FSSW with a pinless tool, using marker materials with welds produced in 0.5 and 1 second.

We have also applied a similar systematic approach to evaluate and optimise the RefillTM variant of FSSW, developed by HZG Germany, which employs a two part tool that refills the probe hole as part of the weld cycle (Figure 1c). Following on from a full analysis of the material flow behaviour, we have modified the process by adding an extra stage that better consolidates the material after the ‘refill’ step. With this

modification, we have shown it is possible to produce welds in under 0.5 seconds with the Refill method (Figure 4). The failure behaviour of the spot welds has also been modelled with good agreement shown between predictions and real shear tests (Figure 5). The welds are defect free and have excellent properties, although there is an ongoing concern surrounding tool wear with this technology.

Overall, comparison of the lap shear test failure loads recorded, for the optimised short-cycle time FSSW processes, showed superior joint properties to competing processes (Figure 6).

Fig. 4 Failure behaviour of a FSSW-Refill weld produced in 0.55 seconds, from 6111 1 mm thick sheet, during lap shear testing.

Fig. 5 Example of FE modelling of the failure process of a Refill FSSW, showing the principal tensile stress distribution in a Refill weld during lap-shear testing.

Fig. 6 Comparison of the lap shear test failure loads recorded, for conventional FSW, FSW with a pinless tool (developed in LATEST) and the FSSW-Refil method, to benchmark data for USW and SPR* and RSW*. *Data taken from * L. Han et al. Materials and Design 31 (2010).

Acknowledgements: Dr Ying-Chun Chen, Basem Al-Zubaidy (PhD Student) Collaborators: JLR, Novelis Publications: 1. “Assessment of rapid refill FSSW for 6111-T4 aluminium automotive alloys”, B. Mohysen Al-Zubaidy, Y. C. Chen and P. B. Prangnell, 14th International Friction Stir Welding Symposium, Beijing, China, Publ. TWI, On CD (2014).

2. “Dissimilar friction spot welding of aluminium and magnesium for automotive applications using novel approaches - abrasion circle FSSW and refill FSSW”, Y. C. Chen, B. Mohysen Al-Zubaidy and P. B. Prangnell in 14th International Friction Stir Welding Symposium, Beijing, China, Publ. TWI On CD (2014).

3. “The effect of a paint bake treatment on joint performance in friction stir spot welding AA6111-T4 sheet using a pinless tool”, Y. C. Chen, S.F. Liu, D. Bakavos, and P. B. Prangnell, Materials Chemistry and Physics, 141 (2-3), 768-775, DOI: 10.1016/j.matchemphys.2013.05.073 (2013).

4. “Material interactions in a novel pinless tool approach to friction stir spot welding thin aluminium sheet”, D. Bakavos, Y. C. Chen, L. Babout and P. B. Prangnell, Metallurgical and Materials Transactions A, 42A (5), 1266-1282, DOI: 10.1007/s11661-010-0514-x (2011).

Critical Assessment of Welding Techniques for Dissimilar Joining of Aluminium to Steel Phil Prangnell LATEST2, School of materials, The university of manchester New design concepts for light weight vehicles will increasingly involve multimaterial structures, as they provide the best compromise solution between mass reduction, performance, and cost. Such designs allow materials to be used more efficiently and will involve combining light alloys with high strength steels and composites. Dissimilar joining is thus a key technology area for enabling increased fuel efficiency in transport.

Within LATEST2 we have taken an objective fundamental look at a range of welding technologies that could potentially be used for joining steel to aluminium. This work has focused on solid state processes, or processes with rapid thermal cycles, to try to reduce the tendency for intermetallic (IMC) reaction at the joint interface, which is the main limiting factor in producing joints with acceptable failure energies.

Examples of the processes studied, include; ultrasonic spot welding (USW), the main

variants of friction stir spot welding (FSSW), and laser conduction spot welding. Effort has also been directed at developing a better understanding of the IMC reactions seen in dissimilar metal welding and modelling so that solutions can be evaluated for reducing the IMC, in parallel with process developments.

A full range of techniques has been used to study the reaction behaviour, defects formed and, in the case of solid state welding, the material flow and bonding process; including 3D tomography, modelling and high resolution microscopy of the weld interfaces. With laser spot welding it has been shown that it is very difficult to control the IMC layer to a thin enough level. There are also distinct problems when welding coated steels due to evaporation of the zinc. Friction based solid state processes appear more promising, but forming a reliable bond between a hard steel surface and a soft

Fig. 1 Examples of typical thin IMC reaction layers seen in dissimilar welds between DC04 steel and 6111 Al; (a) a TEM image from a 2 sec. conventional pinless tool FSSW, (b) SEM phase identification performed on a 1.5 second USW.

Fig. 2 (a) IMC reaction layer thicknesses measured across weld interfaces in Al (6111)-steel (DC04) ultrasonic and FSSWs (produced with a pinless tool), compared to the predicted temperature profile modelled in a LATEST2 collaboration with Shercliff, Cambridge Engineering. (Note the average IMC thickness data was measured from the weld centre to the edge and has been reflected to aid comparison with the model).

aluminium alloy has been found to greatly increase the weld cycle time, which still allows significant IMC reaction to take place (Figure 1-2). In FSSW this occurs because flow studies have shown that the aluminium sheet develops a sticking condition with the steel surface at an early stage in welding and, as a result, there is little relative motion of the two materials across the interface. There is thus little benefit, in terms of cleaning oxide off the steel surface, and the joining mechanism is principally one of diffusion bonding, facilitated by frictional heating. There is also an issue with galvanised steels due to the low melting point eutectic reaction between aluminium and zinc, which creates a liquid film at the join line, leading to a slip condition which causes weld defects.

As a result of the fundamental studies performed within LATEST2, the most promising solution that has immerged has been termed ‘abrasive circle welding’ (ABC-FSSW). This technique (Figure 3a) involves adapting the friction stir spot welding technique to use a slight orbital path, so that the tool probe lightly abrades the steel surface over a circular area to produce a full clean oxide-free surface during the welding cycle. This technique has allowed successful welds to be produced between steel and aluminium, with a very rapid weld cycle of less than one second.

The abrasion of the tool and short weld time substantially reduces the thickness of the IMC layer and under low heat input conditions can lead to a completely clean interface (Figure 4). As a result, weld failure energies equivalent to that of aluminiumaluminium joints have been achieved (Figure 3c). With the same approach, successful dissimilar welds have also been demonstrated between aluminium and galvannealed zinc coated steel sheets.

Fig. 3 (a) Schematic diagram and (b) surface appearance of an abrasive circle friction spot weld (ABC-FSSW) between Al and steel; (c) comparison of the lap shear test load displacement curves with that found from a conventional FSSW.

Fig. 4 (a) Pull-out failure mode and (b) and (c) SEM and TEM images of the ‘clean’ interface produced by the ABC-FSW process.

Acknowledgements: Dr. Hugh Shercliff, P. Jedrasiak (Uni. Cambridge Engineering) Dr. S. Ganguly (Uni. Cranfield) Dr Farid Haddadi (PhD Student), Dr Yingchun Chen (Latest RA), Lei Xu (PhD student).

Collaborators: JLR, Tata Steel.

Publications: 1. “Effect of interfacial reaction on the mechanical performance of steel to aluminium dissimilar ultrasonic spot welds”, P. B. Prangnell, L. Xu, L. Wang, Y. C. Chen, J. D. Robson, Metallurgical and Materials Transactions A, 334-346, DOI: 10.1007/s11661-015-3179-7 (2016).

2. “Modelling of the thermal field in dissimilar alloy ultrasonic welding”, P. Jedrasiak, H. R. Shercliff, Y. C. Chen, L. Wang, P. B. Prangnell and J. D. Robson, Journal of Materials Engineering and Performance, 24, 799-807, DOI: 10.1007/s11665-014-1342-8 (2015).

3. “Modelling and visualisation of material flow in friction stir spot welding”, P. B. Prangnell, A. Reilly, H. R. Shercliffe, Y. C. Chen, Journal of Materials Processing Technology, 473-474, DOI: 10.1016/j.jmatprotec.2015.06.021 (2015).

4. "Interface structure and bonding in abrasion circle friction stir spot welding: A novel approach for rapid welding aluminium alloy to steel automotive sheet", Y.C. Chen, A. Gholinia, P.B. Prangnell, Materials Chemistry and Physics, 134, 459-463 (2012).

5. “Effect of zinc coatings on joint properties and interface reaction in aluminium to steel ultrasonic spot welding”, F. Haddadi, D. Strong and P. B. Prangnell, TMS, San Diego, Sup. Proc. Vol. 1, Materials Processing and Energy Materials, 735-742 (2011).

6. “Interface structure and bonding in rapid dissimilar FSSW of al to steel automotive sheet”, Y. C. Chen and P. B. Prangnell, In Symposium 13th International Conference on Aluminum Alloys (ICAA13) Edited by: H. Weiland, A. D. Rollett, W. A. Cassada, TMS, Pittsburgh, PA (2012).

Coating Design for Controlling IMC Formation in Dissimilar Al-Mg Metal Welding P. B. Prangnell LATEST2, School of materials The university of manchester The automobile industry is facing ever more demanding emissions targets, which has aroused wide interest in replacing traditional materials with lighter metals, such as Al and Mg. In the future more efficient new vehicle designs will also be increasingly based on multi-material structures, where the best attributes of different materials can be exploited. This new direction of the automotive industry thus presents major challenges in joining dissimilar metals. Direct joining of aluminium to magnesium alloys is very challenging, with virtually all welding methods producing poor weld properties that suffer from low toughness. This is even true for lower temperature solid state joining techniques, like friction stir welding [1,2]. The problem mainly lies in the rapid formation of Al - Mg intermetallic compounds (IMCs) which can severely embrittle the joint interface.

In particular, the Al3Mg2 phase is reported to have the highest growth rate among the common Al - Mg compounds [1-3] and is the phase in which cracks are most prone to initiate, owing to its low strength and highly brittle nature.

In LATEST2 this reactive system has now been fully characterised, including the identification of the previously controversial Al30Mg23 phase and a full description has been made of the reaction kinetics, grain structure and texture of the reactions layer (Figure 1). We have also now shown, using a FIB ring-core milling procedure, that the IMC layer contains large residual stresses that develop as it grows. Previous work in LATEST2 has both modelled the IMC reaction in this system [2,3] and shown that barrier inter-layers, such as PVD Mn, can be effective in controlling the Al-Mg interfacial reaction rate [4]. Unfortunately, such thin barrier coatings were found to become readily damaged by friction welding processes, reducing their effectiveness [4].

To address the intermetallic reaction problem, now thermodynamic calculations have been used to predict more ductile Alalloy compositions that could be applied as thicker coatings by cheap established technologies, like the Novelis FusionTM process, and change the reaction path to avoid the formation of the problematic β phase [5]. Two candidate alloys were predicted to have potential: i) a Si-rich coating; and ii) an Al-Zn-rich solid solution coating. In the former case, calculations showed the addition of Si favours the more stable Mg2Si phase over β and, in the second, with a high enough Zn content, the ternary phase τ-(Al,Zn)49Mg32 was predicted to replace the β phase. Long-term annealing and refill friction stir spot welding (Refill-SSW) experiments were carried out to study the effect of these new coating systems on the intermetallic growth behaviour, under static and welding conditions. For the Al-Si alloy coating, Novelis provided a 6xxx alloy coated by their

Fig. 1 Examples of the IMC reaction layer kinetic (a) and microstructural data (b) obtained from Al-Mg diffusion couple experiments).

Fig. 2 Interface characterisation of Al-Mg diffusion couples after annealing at 400°C for 3 hrs; (a) unclad Al (6111) and (b) the Al(Si) clad material, both joined to Mg AZ31; (c) identification of the Mg2Si phase in the Al(Si)-Mg IMC layer, and (d) EDX line profile along the red line shown in (b).

proprietary FusionTM process, while the Al-Zn coating material was made in house.

The results of static heat treatments are shown in Figs. 2 and 3, where it can be observed that in both cases the β-Al3Mg2 phase did not develop when the coating alloys were used. With the Al-Si coating (Figure 2) the IMC layer was much thinner and only the γ-Al12Mg17 and Mg2Si phases were identified. In the second case, as predicted, the β-Al3Mg2 phase was found to be replaced by the τ-(Al,Zn)49Mg32 (Figure 3) but unfortunately the new IMC layer still grew at the same rate.

(a)

Results for the Al-Si coating from Refill friction stir spot welding showed that the Si rich coating was less effective than hoped in reducing the IMC layer reaction rate, because it was discreetly distributed within second phase particles and with the very rapid heating cycle seen in welding there was insufficient time for diffusion of Si. However, the Al-Si coating was still effective in increasing the strength of the Al-Mg dissimilar welded joints. In lap shear tests failure loads of within 97% of that of similar welds in the weakest weld member (i.e. Mg-Mg) were achieved, which is the

best performance ever reported for Al to Mg spot welds (Figure 4a). Analysis of partially failed welds showed that this could be related to a reduced IMC reaction layer thickness, but also the residual Si particles within the IMC layer deflected the crack path along the weld interface into the aluminium substrate (Figure 4b). This work has thus demonstrated there is potential to ‘engineer’ the IMC reaction layer in dissimilar welding to mitigate its negative impact on joint properties.

(b)

Fig. 2 Comparison of interface microstructures after annealing Al - Mg couples at 360°C for 24 hrs in (a) unclad Al (6111) and in (b) when welded to an Al(52%Zn) alloy. The inserts are from EBSD phase ID maps.

Fig. 3 (a) Results from lap shear tests conducted on Refill-FSSWs comparing the failure load for welds produced with the new Al-Si coated Al sheet to that for optimised standard uncoated Al-Mg welds and the target properties of Mg-Mg similar welds. In (b) with the Al-Si coating, more limited IMC reaction and crack deflection by the Si particles embedded in the IMC layer can be seen at the joint interface. It can be noted that with the coated sheet the failure load of the dissimilar weld has reached 97% of that for the Mg-Mg benchmark.

Acknowledgements: Yin Wang, Basem Mohysen Al-Zubaidy, Lexi Panteli - project PhD StudentsDr Ying Chun Chen – Theme 2 PDRA. Collaborators: Novelis and Magnesium Electron.

Publications: 1. “Optimisation of aluminium to magnesium ultrasonic spot welding”, A. Panteli, Y. C. Chen, D. Strong, X. Zhang and P. B. Prangnell, Journal of Materials, 64 (3), 414-420, DOI:10.1007/s11837-012-0268-6 (2012).

2. “The effect of high strain rate deformation on intermetallic reaction during ultrasonic welding a luminium to magnesium”, A. Panteli, J. D. Robson, I Brough and P. B. Prangnell, Materials Science and Engineering A, 556, 31-42; DOI:10.1016/j.msea.2012.06.055 (2012).

3. “Interfacial reaction during dissimilar joining of aluminum alloy to magnesium and titanium alloys”, J. D. Robson, A. Panteli, C. Q. Zhang, D. Baptiste, E. Cai, P. B. Prangnell, In Symposium 13th International Conference on Aluminum Alloys (ICAA13) Edited by: H. Weiland, A.D. Rollett, W.A. Cassada, TMS, Pittsburgh, PA (2012).

4. “The effectiveness of surface coatings on preventing interfacial reaction during ultrasonic welding of aluminum to magnesium”, A. Panteli, J. D. Robson, Y. C. Chen and P. B. Prangnell, Metallurgical and Materials Transactions A, DOI: 10.1007/s11661-013-1928-z (2013).

5. “Coating design for controlling b phase imc formation in dissimilar Al-Mg-metal welding”, Y. Wang, L. Wang, J. D. Robson, B. M. Al-Zubaidy and P. B. Prangnell, Friction Stir Welding and Processing VIII, 171, DOI: 10.1002/9781119093343.ch19 (2015).

Assessment of the Advantages of Static Shoulder FSW for Joining Aluminium Aerospace Alloys Philip Prangnell, matt roy LATEST2, School of materials, The university of manchester Friction Stir Welding (FSW) is now a wellestablished process that is widely used to join aluminium alloys, owing to the excellent weld properties that can be obtained. The technology was originally developed in the UK by the TWI and involves translating a rotating tool along the join line between two butted plates, which forges the two weld members together without melting. Stationary (Static) Shoulder Friction Stir Welding (SSFSW) is a new variant of FSW that was first developed to improve the weldability of titanium alloys, because their low thermal conductivity results in a severe temperature gradient through the plate thickness. This is because in conventional FSW heat is generated predominately by the tool shoulder and with thicker material it is not normally possible to maintain a high enough temperature at the base of the weld to

avoid pin failures, unless a low travel speed is used. SSFSW can also provide several additional advantages over the conventional method, including: i) a non-rotating shoulder irons the surface and leads to an improvement in surface quality and ii) the shoulder acts as a heat sink rather than a source so that the heat distribution should become narrower at the top surface and more uniform through the plate.

Surprisingly, despite these clear advantages static shoulder FSW has largely been ignored by the aluminium welding community. In LATEST2 we have developed a systematic approach for comparing the two processes, when applied to joining high strength Al-aerospace alloys. The approach we adopted was to use an identical shoulder and pin geometry for each method (Figure 1) and to first understand and model the relationship between the heat input and

the welding parameters, using torque/ power curves, so that both processes can be compared using a rational selection of the optimum welding conditions. Modelling has also been used to fit the thermal field for each process and predict the systematic effect of varying the contribution of the shoulder heat generation on the HAZ shape (Figure 2b). We have also studied the surface finish that can be achieved (Figure 3) and the formation of weld defects that can be specific to the SS-FSW process and the residual stress distribution in each process (Figure 4).

It has been shown that stationary shoulder welding requires an approximately 30% lower heat input than conventional FSW. Welding with a stationary shoulder also produces welds with a narrower, more parallel, heat affected zone and lower through-thickness microstructure and

Fig. 1 Tool designs and HAZ profiles for the two process variants; (a) FSW, (b) SS-FSW) under optimised conditions, note the narrower and more parallel HAZ with static shoulder FSW.

Fig. 2 (a) comparison of the relationship to rotation rate to the power curves for conventional FSW and SSFSW, with optimum process windows marked by the vertical dashed lines; (b) thermal model showing the effect on the temperature field profile of reducing the shoulder power input, while increasing the probe power to maintain the same weld temperature near the weld root.

property gradients (Figure 1). The welds performed better than conventional FSWs in cross-weld tensile tests. DIC analysis of the strain distribution in the test pieces revealed that this resulted from their narrower HAZ helping to prevent premature failure, by imposing greater constraint on the localisation of plastic strain during deformation.

Thermal simulation, combined with hardness modelling, confirmed that the above benefits arose from changing the

FSW process from one, where the majority of heat is introduced by conduction into the workpiece from the energy dissipated by a rotating shoulder, to one where heat is generated more uniformly through the plate thickness by only the probe (Figure 2). In addition, it was shown that the ironing effect of the stationary shoulder could be used to greatly reduce the weld’s surface roughness (Figure 3). Furthermore, the colder surface temperature dramatically decreased the reduction in workpiece

thickness normally seen along the weld line in the standard FSW process, caused by the shoulder plunge. The distribution of residual stresses was also found to change, with a reduction in the peak tensile stresses seen in certain welding conditions and a narrower residual stress profile (Figure 4). A negative effect of welding with a stationary shoulder was noted in this work under hotter welding condition, in that it can lead to surface ‘speed cracking’ similar to that seen in extrusion.

Fig. 3 Comparison of the difference in surface roughness found between (a) conventional FSW and (b) static shoulder SSFSW.

Fig. 4 Comparison of the longitudinal residual stress distributions seen in (a) FSW and (b) SSFSW, determined by the contour method.

Acknowledgements: Hao Wu (PhD Student), Tianzhu Sun, (PhD Student), Dr. Yingchun Chen.

Publications: 1. “Stationary shoulder FSW for joining high strength aluminium alloys”, H. Wu, Y-C, Chen, D. Strong and P. B. Prangnell, Journal of Materials Processing Technology, 221, 187-196, DOI: 10.1016/j.jmatprotec.2015.02.015 (2015).

2. “Assessment of the advantages of static shoulder FSW for joining aluminium aerospace alloys”, H. Wu, Y. C. Chen, D. Strong, and P. B. Prangnell, Thermec, Las Vegas, USA (2013).

3. “Systematic evaluation of the advantages of static shoulder fsw for joining aluminium”, H. Wu, Y. C. Chen, D. Strong and P. B. Prangnell, Materials Science Forum, 794-796, 407-412 (2014).

Laser Welding of Advanced Aerospace Aluminium Alloys yingtao Tian1, Joseph robson1, Stefan riekehr2, nikolai Kashaev2 LATEST2, School of materials, The university of manchester 2 helmholtz-Zentrum geesthacht, Zentrum f端r material und K端stenforschung gmbh

1

Advanced high strength aluminium-lithium alloys, such as AA2198 and AA2196, have a combination of excellent strength and low density that means they are now the material of choice for future single aisle airframes. To maximize the cost and weight saving benefits of these alloys, there is a strong motivation to replace current mechanical fastening technologies (e.g. riveting) with a welding process. Laser welding is one of the most promising of such processes, allowing fully automated welding at high speed with minimal microstructural damage. However, it is highly challenging to weld Al-Li alloys using any fusion welding process due to the high alloy content and the sensitivity of the strength of the base materials to thermal damage. The high alloy content of the base metals can make the alloys susceptible to hot cracking. Understanding the complex interactions during welding is key to successful laser welding of Al-Li components.

Fig. 1 Flow chart showing the components in the integrated model for laser welding of aerospace aluminium alloys.

The work described here aims to develop simulation tools to develop laser welding for joining of Al-Li alloys. In parallel, advanced characterization techniques have been used to obtain a better understanding of the effect of process parameters on the weld integrity.

The integrated model that has been developed consists of two main components, as shown in Figure 1. The first is a process model that takes the weld process parameters, geometry etc. and calculates the thermal profile at any position. This output is used as an input to the microstructure and hot crack susceptibility (HCS) models. The process model is implemented in the ABAQUS finite element framework.

Once the thermal history of the weld is known, this can be combined with the calculated melt pool chemistry to estimate the HCS. Both the freezing behaviour and

thermal history are considered. Hot cracks form under conditions where thermal contraction leads to cracks that cannot be healed by inward liquid flow. The HCS can be expressed in terms of a critical strain rate (due to thermal contraction) that can be tolerated before cracking. A high value of the inverse of this critical rate indicates a condition with a high susceptibility to HCS. By considering the local thermal conditions and composition in the weld pool, HCS maps can be produced for different conditions and used to identify positions and weld parameters that lead to a high risk of HCS (Figure 2).

In addition to HCS, weld integrity can also be limited by porosity that arises from entrained gas. It is not yet possible to predict such porosity, so this has been characterized experimentally using 3-dimensional X-ray tomography (XCT).

Using the unique capabilities of the Henry Moseley X-ray Imaging Facility (HMXIF) at Manchester, it has been possible for the first time to determine the size and distribution of such pores for a range of weld powers.

An example image for a low weld power is shown in Figure 3. It was found that there was an optimum weld power giving the best compromise between HCS and gas porosity. This is being used to produce a full-scale skin-stringer demonstrator panel.

Ongoing work using the HCS model is underway to further improve the weld performance by identifying promising filler wire chemistries that could replace the standard Al-Si filler typically used in laser welding of Al-Li.

Fig. 2 Fusion zone macrographs and predictions of the hot crack susceptibility (HCS) model for three welds produced at different powers (a) 1400W, (b) 1720W, (c) 2000W. Bright colours indicate higher HCS.

Fig. 3 Porosity (red) identified in a weld produced with low power (1400W) by X-ray tomography.

Acknowledgements: This project was co-funded by LATEST2 and the EU-FP7 CleanSkys programme LAWENDEL. Thanks to Constellium for the provision of materials used in this work.

Surface Engineering Metal Composite Hyperjoints P. B. Prangnell, J. d. robson LATEST2, School of materials The university of manchester The use of composites is increasing in advanced civil airframe designs, to improve fuel efficiency. However, metallic materials, and in particular titanium alloys, still feature strongly where a higher temperature capability, or multi-axis loading is required.

For example, the new A350XWB ‘composite’ aircraft is actually a multimaterial design and contains over 40% metallic structure. Producing reliable joints between high performance titanium alloys and composite components is challenging because of their very different chemical and physical properties. There is a need to improve load transfer efficiency and move away from the reliance on fasteners, which create bearing issues in composite laminates. At the same time, adhesive only metal-composite joints currently do not have a long enough safe design life, or load transfer capability without a large lap area, which increases weight.

A typical aerospace hyperjoint design requires the ability to reliably manufacture arrays of small pins (typically ~ 1 mm diameter) with an accurate geometry on a titanium substrate (Figure 1). In partnership with EADS, within LATEST2 we have explored methods of assessing the quality and predictability of the failure load of hyperpins manufactured by different techniques, so that an industrially viable process can be identified for their full-scale manufacture. Approaches that have been explored, include electron beam surface sculpting (Surfi-Sculpt®) laser additive manufacture (AM), and micro-welding technologies that can attach pre-forged pins sufficiently rapidly for industrialisation.

Such methods can have drawbacks including, restrictions in the pin shape (Surfi-sculpt) and slow production rates (AM). In LATEST2 we have studied the metallurgical issues associated with each approach, including the critical area between the base of the pins and component substrate (Figure 2), where there is usually a sharp microstructural gradient. Methods have also been developed to test and model the performance of individual pins (Figure 3), as well as to study the damage that develops

in a laminate joint assembly under load using the 3-D imaging X-ray Computed Tomography (XCT) facilities in the Manchester X-Ray Imaging Facility (MXIF) (Figure 1). Within Theme 3 on surface engineering, work is also on-going to understand how to use electro-chemical treatments more effectively to tailor titanium surface oxide films pore structures to improve adhesion on metal surfaces.

A potentially viable manufacturing route has now been identified and plans are afoot to expand this activity to investigate the issues associated with scaling up the technology for industrial application.

Fig 3. (b)

2µm

‘Hyperjoints’ are a new class of joint that aim to address some of these problems by incorporating both mechanical and adhesive bonding into one joint design. In Hyperjoints’, arrays of locking features are engineered on to the metal part that are then imbedded into the composite laminate to increase the shear transfer, via both better adhesion and mechanical ‘fit’, through the thickness of the laminate.

This approach can greatly improve the joint strength and failure energy.

Fig 3. (a) Fig. 3 (a) FE model and (b) failure of an additive manufactured hyperpin, during shear testing, (c) an alpha phase EBSD map of the Ti64 AM pin near its base, with prior β grains outlined.

Specimen 11205

Fig 3. (c)

50µm

Collaborators: EADS Innovation works, TWI. Acknowledgements: Rotimi Oluleke (EADS- PhD Student) Dr. Fabien Leonard (MXIF)).

Fig 1.

2mm

Fig. 1 X-ray micro tomography image showing the hyper pin array in a loaded lap joint with the development of damage in the composite indicated in red.

Fig 2.

Fig. 2 High resolution SEM image showing the microstructure variation across the melt pool fusion boundary of a ‘welded on’ hyper-pin with a Ti64 rolled plate substrate.

Publications: 1. "Mechanical and microstructural characterization of percussive arc welded hyper-pins for titanium to composite metal joining", R. J. Oluleke, D. Strong, O. Ciuca, J Meyer, A. De Oliveira and P. B. Prangnell, in LMT2013, 6th International Symposium on Light Metals Technology, Materials Science Forum, 765 , 771-775., DOI: 10.4028/www.scientific.net/MSF.765.771 (2013).

Understanding Defects in Additive Manufacturing Phil Prangnell LATEST2, School of materials, The university of manchester.

Additive manufacturing (AM) is an exciting up-and-coming near-net-shape technology that is in the process of being rapidly industrialised for aerospace manufacturing.

AM is extremely attractive to the aerospace industry as it allows great design flexibility, reduces lead times, and most importantly greatly reduces the amount of machining required to produce components made out of expensive and difficult materials like titanium alloys. For example, the buy-to-fly ratio for a typical titanium component machined from forged billet is 10 – 20:1 compared to 2 – 5:1 when manufactured by AM. A particular issue in the qualification of AM for aerospace applications is the control of defects that can arise and their effect on fatigue life. In titanium AM the defects that are generated arise primarily from gas

porosity and a lack of fusion of the powder particles, caused by process instability.

Within LATEST2 we have been actively engaged in using advanced characterisation tools, such as 3D X-ray computed tomography (XCT) to characterise the defects formed in different AM processes with statistically reliable data and correlate their size and positon to the process parameters (e.g. Figure 1).

This work has shown that in some commercial powder bed AM processes the control software does not always perform as expected and can over-correct for factors such as overhang regions, or on beam path reversal in rastering, which results in too low a local heat input and a high defect density (Figure 2). We have also investigated the effectiveness of HIPing operations to close pores in AM components (Figure 2 d,e). In addition, work has been performed to understand the effect of pores on high cycle fatigue life. This has included developing procedures for reducing the scatter in fatigue data and predicting worst case defects in components, by ranking the

local stress concentration factor calculated from pore data-sets obtained from full XCT scans of test samples. In this procedure, the proximity of pores to a surface, or to other pores, and the effect of sample geometry were estimated using simplified linear mechanics. By using this method to plot the number of cycles to failure against the stress intensity factor at the crack initiation location, rather than the global stress, the scatter in fatigue data was greatly reduced (Figure 3).

The role of porosity in AM parts in fatigue crack growth has also been studied by repeatedly re-scanning fatigue samples as cracks initiate and grow, which has revealed that pores within most powder bed parts are generally to widely spaced to have a significant effect on fatigue crack growth.

This observation has been confirmed by meshing of the XCT data within FE models, which has shown that pores don’t greatly influence the stress field at a crack tip unless it is approached to within one pore diameter of the crack front (Figure 4).

Fig. 3 High cycle fatigue life data: (a) plotted as a standard S-N plot of stress range against cycles to failure; and (b) re-plotted in terms of the stress intensity factor range generated by the specific pore found at the crack initiation site, against cycles to failure.

Fig. 1 Examples of pore types (a) and (b) density near the edge and centre of selective electron beam melted (SEBM) Ti64 samples, measured by XCT.

Fig. 2 Example of the effect of process themes on the distribution of porosity in cubic SEBM test samples; (a) and (b) projections of all the defects in the x-y pane for (a) separate standard contouring and hatching routines and (b) when just using the contour setting; (c) corresponding plot of the pore volume fraction with distance from the sample surface. (d) and (e) show the high effectiveness of HIPing in closing extreme defects in samples built with poor process control.

Fig. 2 (a) Growth of a fatigue cracks past a poor in an AM sample, tracked by XCT and (b) the influence of pores on the stress field at a crack tip (von Mises) modelled using automated messhing of XCT data.

Acknowledgements: Airbus, UK, EADS, Innovation Works, Filton, UK, GKN Aeropsace, UK. Collaborators: Prof Iain Todd Sheffield (Collaborator) Sam Tammas-Williams (RRs- PhD student).

Publications: 1. “XCT analysis of the influence of process parameters on defect population in Ti-6Al-4V components manufactured by selective electron beam melting”, S. Tammas-Williams, H. Zhao, F. Leonard, F. Derguti, I. Todd and P. B. Prangnell, Journal of Material Characterisation, 102, 47 - 61, DOI: 10.1007/s10008-015-2864-1 (2015).

2. “The effectiveness of hot isostatic pressing for closing porosity in titanium parts manufactured by selective electron beam melting”, P. B. Prangnell, S. Tammas-Williams, I. Todd, P. J. Withers, Metallurgical and Material Transactions. A, In press (2016).

3. “Predicting the influence of porosity on the fatigue performance of titanium components manufactured by selective electron beam melting”, S. Tammas-Williams, J. Donoghue and P. B. Prangnell, Ti-2015: The 13th World Conference on Titanium, On CD (2015).

Understanding Heterogeneity in Additive Manufacturing with Titanium Phil Prangnell LATEST2, School of materials, The university of manchester AM is attractive to the aerospace industry as it allows great design flexibility, and nearnet-shape manufacture of components made from expensive and difficult to machine materials like titanium alloys. For example, the buy-to-fly ratio for a typical titanium component machined from forged billet is 10 - 20:1, compared to 2 - 5:1 when manufactured by AM. A range of AM platforms are available from laser and electron beam powder bed, to blown powder and wire based systems, such as plasma or laser wire deposition. These systems vary in resolution (layer height) and the deposition rate and size of components that can be built. There is thus a trade-off between precision and component scale; i.e. SLM laser powder bed is most suitable for complex high precision, but small (typically less than 0.5 m), components, whereas plasma-arc wire deposition can be used to produce large less complex parts

(over 10 m in length). Although a lot of work has been done to develop these technologies, to date surprisingly little effort has been devoted to understanding the materials issues they present, particularly in terms of the uniformity and isotropy of the microstructure and texture developed in AM components, which is of concern to the aerospace industry.

In AM the material solidifies in a small moving melt pool, and material is built up with many overlapping raster tracks, leading to very high solidification and cooling rates and a complex cyclic thermal history. The moving melt pool solidification conditions in AM tend to promote very coarse directional primary grain structures, particularly in titanium alloys which exhibit little solute partitioning on solidification. Within LATEST2 this phenomenon has been investigated across a full range of AM

platforms. This work has conclusively shown that the coarse β grain structure primarily develops by epitaxial re-growth of β grains at the fusion boundary, which re-form and coarsen every time the material is re-heated above the β transus temperature as the heat source approaches (Figure 1).

Columnar growth follows the solidification front at the rear of the melt pool and can occur up through many added layers allowing, selection of preferentially orientated grains and leading to a strong β texture. Work has shown that the grain structure and texture seen in AM components is thus very dependent on the melt-pool shape, size, and travel speed. The grain structure is also affected by the beam path and in powder bed AM systems proximity to the part surface, where the powder can provide opportunities for heterogeneous nucleation (Figure 2).

Fig. 2 Examples of variability in primary β- grain structures with Ti64 in (a) a thin section wall produced in an SEBM powder bed system and (b) evidence of nucleation from the surrounding powder at the wall surface, (c) effect of a change in section thickness, and (d) effect of alternating the raster path with layer height in a large scale arc based AM process (WAAM).

Fig. 1 The development of a coarse-columnar primary β- grain and strong texture intensity seen with Ti64 in thick sections for in the SEBM AM Processes.

A parallel investigation has been performed on the homogeneity of the transformation structure seen in different AM processes with the alloy Ti-6Al-4-V. To obtain statistically reliable results, this has involved developing an automated tool for mapping the main microstructure indicators, namely the α lath width and the retained β spheroidicity, across different length scales.

The tool involves automatically batch processing large arrays of high resolution SEM images, either as stitched maps to study local heterogeneity, or regularly

spaced in grids to capture long range heterogeneity. This work has revealed that the transformation microstructure can vary significantly, both across individual layers, and over long distances across whole sections (Figure 3a) in the build plane and vertically, well as in response to geometry changes (Figure 3b). For example, in SEBM powder bed systems the microstructure is coarser and more spherdoidised near the base of a build, because the material consolidated first spends a longer time at a high temperature. For components with

non-uniform sections, changes in section and build orientation can also affect the transformation structure because this influences the local heat flow (e.g. through the solid metal towards the base plate, relative to that into the lower conductivity surrounding powder). In certain machines the control system also dynamically manages the heat input to each layer, depending on the local geometry, which can also affect the transformation microstructure.

Fig. 3 Statistical data obtained from automated batch processing of arrays of high resolution SEM images showing, (a) a progressive decrease in α lath width and reduction in circularity of the retained β with build height, for a 30 cm tall part, and (b) variation in α lath width with build height and sample orientation in a triangular cross section (Ti64 SEBM powder bed process).

Acknowledgements: Dr Alphons Antonysamy (ex EADS-PhD Student now at GKN), Hao Zhao (PhD student) Sam Tamas-Williams (RRs- PhD student).

Collaborators: Airbus, UK, EADS, Innovation Works, Filton, UK, GKN Aeropsace, UK. Publications: 1. “Automated multi-scale microstructure heterogeneity analysis of selective electron beam melted TiAl6V4 components”, H. Zhao, A. A. Antonysamy, J. Meyer, O. Ciuca, S. W. Williams and P. B. Prangnell, TMS 2015, Additive Manufacturing Symposium, Supplementary Proceedings, 429-435, DOI: 10.1002/9781119093466.ch54 (2015).

2. “Effect of build geometry on texture and grain structure development in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A. Antonysamy, P. B. Prangnell and J. Meyer, Thermec, Quebec (2011).

3. “Influence of build geometry on beta grain structure and texture during additive layer manufacture (ALM) of Ti-6Al-4V by electron beam selective melting”, A. A. Antonysamy, P. B. Prangnell and J. Meyer, Titanium Conference (2011).

4. “Effect of wall thickness transitions on texture and grain structure in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A Antonysamy, P. B. Prangnell and J. Meyer, Materials Science Forum, 706 - 709, 205-2010, DOI: 10.4028/www.scientific.net/MSF.706-709.205 (2012).

Integration of In-Process Deformation with Additive Manufacture of Ti-6Al-4V Components - for improved β Grain Structure Refinement and Texture Control P. B. Prangnell LATEST2, School of materials The university of manchester

Additive Manufacturing (AM) is a rapidly growing technology that is attracting great interest and large investments in the aerospace sector, because it allows nearnet-shape manufacture of complex parts with a low buy-to-fly ratio. AM can also facilitate shorter product lead times and more design freedom than traditional manufacturing processes, which can provide substantial weight savings by allowing the manufacture of topographically optimised components. However, AM is based on the layer-wise deposition of material through melting with a moving heat source and this can lead to quite different microstructures and textures than are produced in more conventional processes, as has been previously demonstrated in a prior LATEST2 project [1].

Of particular concern when manufacturing large scale AM components with titanium alloys, like Ti-6Al-4V, is that the solidification conditions promote homo-epitaxial re-growth within each melted layer, causing very coarse directional grain structures to develop (Figure 1a).

Because of the preferred <001> growth direction in cubic metals, these large columnar grains tend to have a strong β <001> fibre texture parallel to the average solidification direction within a particular AM process. On cooling, the final transformation texture is weakened by the 12 possible variants of the α phase formed within each β grain (Figure 2a), as described by the Burgers orientation relationship, but this can still lead to anisotropy in the properties of titanium AM

components. Disrupting this undesirable primary columnar β structure by metallurgical means is challenging as there are few options for grain refining additions in titanium.

Fig. 1 Examples of reconstructed IPF coloured EBSD maps comparing the coarse columnar, strongly <001> textured, primary β grain structure, that is normally seen in AM parts, with the refinement that can be obtained by an in-process deformation step: (a) wire arc AM without and with the application of a roller to each deposited layer, (b) laser blown powder AM without and with the application of peening by UIT. Note; the red colour denotes a strong <001> orientation aligned ~ with the build direction (samples courtesy of Cranfield University and BAE Systems).

In partnership with Airbus, BAE SYSTEMS, and Cranfield University, LATEST2 has been investigating the potential for introducing a deformation step within AM, to reduce residual stresses and improve the grain structure and texture. Two methods have been studied, mechanical peening (ultrasonic impact treatment; UIT) and constrained rolling of each layer after it is deposited. The results have been excellent (Figs 1 & 2). For example, despite the small strains introduced into the layers in rolling (10 - 20%) the β grain size in wire arc additive manufacturing (WAAM) was reduced from several millimetres to less than 100 μm, which has led to a more fundamental study on why adding an ‘in-process’ deformation step in AM is so

effective at refining the β grain structure.

This has involved simulating the deformation step and rapid heating cycles seen in AM, as well as observing, for the first time, the α -> β transition in a lightly deformed AM material in-situ in an SEM by EBSD (Figure 3).

The results of this work have revealed that the β grain refinement mechanism involves the formation of new orientations within the thin retained β layers between the fine α lamellar by twinning, when the AM transformation structure is deformed. These new orientations then grow when reheating above the β transus, on depositing the next layer, which refines the grain structure and randomises the texture in the substrate material on which each new melt

track solidifies. This prevents columnar growth developing epitaxially over many layers and thus disrupts the establishment of the strong texture and coarse grain structure normally found in AM parts. The mechanism for re-orientating the retained β discovered in this work has not been observed before and it is thought that it occurs specifically in AM materials because of the fine nature of the transformation structure, which promotes twinning during cold deformation.

Fig. 3 Examples from in-situ EBSD heating studies showing the reconstructed prior β phase at room temperature and direct indexing of the re-growth of β at close to the transus temperature; (a) for a lightly deformed material (~2% strain) and (b) a higher pre-strain (~15%). Unreconstructed regions in the room temperature maps correspond to α phase twinning. In (a) new β orientations can be seen within the α twins, whereas many more new β orientations are found in (b).

Fig. 2 The prior beta and final alpha textures seen in AM samples produced by the blown powder method (a) a standard part and (b) with the application of UIT (peening) to each layer.

Acknowledgements: Jack Donoghue - project PhD Student; Dr Ali Gholinia – Experimental Officer Collaborators: Gatan, developmental high temperature heating stage; Airbus, student support; BAE Systems, blown powder direct metal deposition and ultrasonic impact treatment; Cranfield University, wire arc AM; WAAM-rolling.

Publications: 1. "The effectiveness of combining rolling deformation with wire-arc additive manufacture on ß grain refinement and texture modification in Ti-6Al-4V materials characterization", J. Donoghue, A. A. Antonysamy, F. Martina, P. A. Colegrove, S.W. Williams and P.B. Prangnell, Materials Characterization, DOI: 10.1016/j.matchar.2016.02.001 (2016).

2. “In-situ high temperature EBSD analysis of the effect of a deformation step on the alpha to beta transition in additive manufactured Ti6Al4V”, J. M. Donoghue, J. Quinta Da Fonseca and P. B. Prangnell, Ti-2015: The 13th World Conference on Titanium, On CD (2015).

3. “Integration of deformation processing with additive manufacture of Ti-6Al-4V components for improved ß grain structure and texture, additive manufacturing”, J. Donoghue, J. Sidhu, A. Wescott and P. B. Prangnell, TMS 2015, Additive Manufacturing Symposium Supplementary Proceedings, 437-444, DOI: 10.1002/9781119093466.ch55 (2015).

4. "EBSD analysis to understand Additive Manufacturing (3D Printing) in titanium", P. B. Prangnell, J. Donoghue, A. Gholinia, O. Ciuca, A. A. Antonysamy, Opening address at RMS-EBSD Meeting, London (2014).

I really enjoyed being part of and contributing to the LATEST2 research Team.

Teruo Hashimoto, LATEST2 Technical Support StaďŹ&#x20AC;

ThEmE 3 SurFAcE EngInEErIng For Low EnVIronmEnTAL ImPAcT And InTErFAcE dESIgn The aim of Theme 3 was to develop the scientific understanding required to underpin and explore creative, new, environmentallycompliant and economically viable solutions to i) enhance surface properties and performance, including reduced corrosion susceptibility, ii) facilitate joining of dissimilar materials (e.g. metals to composites) and the manufacture of hybrid materials and iii) protect multi-material structures, thus facilitating the introduction of more efficient designs.

For light alloys, corrosion control is a vital aspect of many surface treatments where, for example, local variations in microstructure impact significantly on both the corrosion susceptibility and the uniformity of protective coating development. Importantly, microgalvanic effects are also decisive in determining the performance in service.

Consequently, major topics in this theme include understanding of the roles of microstructure at all length scales on surface engineering, including advancement of 3D electron imaging of corrosion and protection systems, and local subsurface microstructures, textures and surface roughening, developed through forming and joining.

Such understanding has provided improved surface appearance and performance of formed materials from knowledge of the impact of near-surface deformed layers on optical appearance and surface integrity. For surface treatments, a more detailed knowledge of conventional anodizing and plasma electrolytic oxidation of light alloys has enhanced practical applications. In addition, other treatments, including sol gel processes and conversion coating are also of importance for effective use of light alloys.

The research has been aimed at supporting the following application areas: Development of environmentally-friendly, economic coating routes for advanced light alloys across the transport sector.

Prevention of cosmetic corrosion in automotive closure panels by control of process-surface activated corrosion.

Prevention of stress corrosion cracking of light alloys for applications in the transport sector.

Development of self-healing and â&#x20AC;&#x2DC;smartâ&#x20AC;&#x2122; coating technologies and new system assessment procedures, for example, image assisted electrochemical noise analysis to replace accelerated corrosion testing.

Designing versatile surface treatment and finishing procedures to support the use of advanced forming and joining approaches for advanced light alloys.

Development of targeted surface treatments for protecting welded joints between dissimilar materials.

Surface engineering for enhanced bonding of metals in hybrid materials/ laminates and to polymer matrix composites.

THEME 3: KEy OUTPUTS WITH POTENTIAL FOR HIGH IMPACT From Theme 3, to date, LATEST2 has generated signiďŹ cant industrial and academic interest in the following areas, which have high potential for longer term impact: Nanoscale 3D characterization has provided new insights into alloy degradation mechanisms through precise determination of corrosion propagation paths and locations of local anodes and cathodes. For the first time, intergranular corrosion has been correlated with the quantitatively determined distribution of defects within grains.

Knowledge created will be exploited by industry for alloy development.

The development of a fast screening technique, based on the quantification of the influence of near-surface deformed layers on the optical appearance of aluminium alloys, for production line quality control of rolled products.

Tailored REACH compliant anodizing and surface pretreatments for aluminium and magnesium alloys in aerospace and automotive industries.

Development of surface treatments for protecting welded joints between dissimilar light metals.

3D characterization of the degradation process of corrosion protection coatings. Knowledge created has been exploited by AkzoNobel for developing new coating formulations.

Environmentally Friendly Surface Treatment for New Generation Aluminium-Lithium Aerospace Alloys x. Zhou, g. E. Thompson, y. ma LATEST2, School of materials The university of manchester Increasing payload and fuel efficiency are drivers for the aerospace industry to strive to improve lightweight materials for application in aircraft structures. Lithiumcontaining aluminum alloys are attractive due to their low density and high stiffness compared with conventional aluminum alloys. For service performance, an adequate, economic, and environmentallyfriendly corrosion protection scheme is necessary. Traditionally, the anticorrosion performance of aerospace aluminum alloys has been achieved through chromic acid anodizing (CAA), followed by painting.

However, the increasing environmental concerns and strict legislation on the use of chromic acid require the development of low-cost and environmentally-friendly anodizing electrolytes.

(a)

In this work, the anodizing behavior of a commercial Al-Li-Cu alloy in an environmentally-friendly electrolyte, namely tartaric-sulfuric acid (TSA), has been investigated. Attention is focused on optimizing the process parameters to tailor the morphology, composition and structure of the resultant porous anodic films to achieve desirable performance.

A relatively fine porous anodic film, with well-defined cells, was observed at relatively low voltages, with copper-rich nanoparticles occluded in the film material (Figure 1).

Pores of increased dimensions, with lateral porosity, were observed at increased voltages (Figure 2). The oxidation of copper is responsible for the additional lateral porosity in the anodic film. It is also revealed that copper in the alloy matrix can be occluded in the anodic film material as copper-rich nanoparticles (Figure 3) or it can be oxidized and incorporated into the film material as copper ions, depending on the anodizing voltage. Further, lattice images of copper-rich nanoparticles indicate that they have structures consistent with either the Ө, Ө' or Ө"phases, regardless of their locations in the anodic films. (a)

(b)

(c)

(d)

(a)

(b) Fig. 2 Transmission electron micrographs of an ultramicrotomed section of AA 2099-T8 aluminum alloy after anodizing at a constant voltage of 14 V: (a) bright field image; (b) HAADF image.

100nm

Fig.3 Lattice images of copper-rich nanoparticles: (a-d) in different regions of the anodic film.

Acknowledgements: This LATEST2 project was performed with support from Airbus Publication

(b)

200nm

Fig. 1 Transmission electron micrographs of an ultramicrotomed cross section of AA 2099-T8 aluminum alloy after anodizing from the OCP to 3 V (SCE) at a sweep rate of 0.03 V/min: (a) bright field image; (b) HAADF image.

Publications: 1. Y. Ma, X. Zhou, G. E. Thompson, M. Curioni, P. Skeldon P. Thomson and E. Koroleva. Single-step Fabrication of Metal Nanoparticle Loaded Mesoporous Alumina Through Anodizing of a Commercial Aluminum Alloy, Electrochemical and Solid-State Letters, 15, E4-E6, 2012.

2. Y. Ma, X. Zhou, G. E. Thompson, M. Curioni, X. Zhong, E. Koroleva, P. Skeldon P. Thomson and M. Fowles. Discontinuities in the Porous Anodic Film Formed on AA 2099-T8 Aluminium Alloy, Corrosion Science, 53, 4141-4151, 2011.

3. “Microstructural modification arising from alkaline etching and their effect on anodizing behaviour of Al-Li-Cu alloy”, J. Electrochemical Society, 160, C111-118, 2013 (Y. Ma, X. Zhou, G.E. Thompson, X Zhang, C Luo, M. Curioni and H. Liu).

1. “Anodic Film Growth on Al-Li-Cu Alloy AA2099-T8”, Electrochimica Acta, 80,148-159, 2012, (Y. Ma, X. Zhou, G.E. Thompson, M. Curioni, P. Skeldon, X. Zhang, Z. Sun, C. Luo, Z. Tang and F. Lu).

Nanotomography Coupled with RF-GDOES for Evaluation of the Corrosion Performance of Processed Aluminium Alloys A. cassell, g. E. Thompson, x. Zhou LATEST2, School of materials, The university of manchester It is known that the thermomechanical processing of aluminium alloys by rolling and extrusion significantly alters their microstructures. These microstructures can be beneficial to the mechanical behaviour of the material, but they can also be detrimental to the corrosion properties in real-life situations. In particular, an altered microstructure is developed in the near-surface regions during thermomechanical processing.

The understanding of the corrosion behaviour of a commercially produced aluminium alloy is important for material durability. Employing a technique recently developed at The University of Manchester, nanoscale in-SEM tomography allows the observation of the nanoscale structures developed within the near-surface region of commercially produced alloys. Examples of results are presented in Figures 1 and 2 The information that can be acquired from this technique can quantify changes in the size, shape and distribution of the relevant microstructural features.

During rolling, the altered near-surface microstructure is distributed across the surface by the rolls in a manner that can result in inconsistent distributions of such microstructures. The varying microstructure across the surface can have significantly different corrosion behaviour when compared to the bulk alloy.

Further, it is often difficult to assess the corrosion properties of the commercially produced alloys due to the complex nature of altered near-surface microstructures, which also have altered phase distributions.

In particular, contact with the rolls can lead to the incorporation of various hot-formed oxides into the near-surface region.

Microalloying of various types of oxides, including those of magnesium, zinc and aluminium, have been witnessed beneath the surface.

Elemental depth profiles of the same commercially produced alloy are provided by radio frequency glow discharge optical emission spectroscopy. Analysis of the first few microns of the rolled surface can provide accurate readings relating to elemental concentrations present within the near-surface region, as shown in Figure 3. Such analysis helps to correlate the corrosion behaviour of the alloy to the distribution of the chemical species in the near-surface region of the alloy.

GDOES Element-time Profile of 7021 T4 As-rolled and As-polished (dash-dotted line) surfaces

8

Element Count

6

4

2

0 0

5

10

15

20

25

Times (s)

Fig. 1 3D rendering of the volume of the microstructure associated with the near-surface region of a commercially produced AA7xxx alloy, revealing three zones: namely a, b and c, with significantly different microstructures compared with the bulk.

Fig. 2 HAADF micrograph of the cross section of the same near-surface region rendered in 3D in Fig. 1. Features within the zones are readily compared.

Fig. 3 The elemental depth profiles for magnesium and zinc which contribute significantly to the corrosion behaviour of the alloy. A sputtering rate of 66 nm/s was achieved. Magnesium oxides are present at the surface after rolling.

Acknowledgements: This LATEST2 project was performed with support from Constellium.

Publications: 1. A. Cassell, G. E. Thompson, X. Zhou, T. Hashimoto and G. Scamans. Relating Grain Misorientation to the Corrosion Behaviour of Low Copper 7xxx Aluminium Alloys, Mater. Sci. Forum, 765, 623-628, 2013.

30

EďŹ&#x20AC;ects of Sulphur Impurity in Chromic Acid Anodizing of Aluminium P. Skeldon LATEST2, School of materials The university of manchester Anodizing processes are widely used for protecting aluminium alloys against corrosion. The resultant films are composed of amorphous alumina and consist of a porous, outer region and a thinner, nonporous, inner region. The films are most commonly formed in chromic, oxalic, phosphoric and sulphuric acids. The films formed in the last three acids contain electrolyte anions. In contrast, those formed in chromic acid contain comparatively few chromate ions and the pore walls are feathered. The latter films are industrially important, especially for protection of aerospace alloys. However, the use of chromates will be restricted by impending REACH (Registration, Evaluation, Authorisation and Restriction of Chemicals) legislation. Alternative anodizing processes have been developed but not yet widely adopted. Hence, interest remains in the chromic acid process.

In the present work, the effects of chromic oxide purity on the anodizing of aluminium and AA2024-T3 aluminium alloy have been examined. Anodizing was carried out at 100 V in 0.4 mol dm-3 chromic acid at 313 K, using reagent grade chemicals supplied by Fisher Chemical and Acros Organics.

The respective electrolytes, designated HSCA and LSCA, contained 12.6 and â&#x2030;¤0.5 ppm sulphur.

Figure 1 shows that the steady current density was reduced by a factor of ~1.8 during anodizing in HSCA. Cross-sections of films formed in HSCA from 15 to 360 s reveal the film development (Figure 2).

Elemental maps reveal sulphur distributed part way through the pore walls and to a depth of ~70% of the barrier layer thickness (Figure 3), where the atomic ratio of S:Al was ~0.02. Similar film morphologies and elemental maps were obtained for LSCA films, but no sulphur was detected. Figure 4 compares cross-sections

of specimens that were anodized in LSCA and HSCA. The respective film thicknesses and the charges passed during anodizing indicated that the volume expansions on converting the aluminium to oxide are ~0.99 and 1.23 respectively. Figure 5 shows scanning electron micrographs of specimens after chemical stripping of the films formed for 360 s in LSCA and HSCA. Both surfaces reveal irregularly ordered cells of various sizes and shapes. The average cell diameters are 137 and 214 nm respectively, corresponding to ratios of ~1.4 and 2.1 nm V-1. The ratio for the HSCA specimen is significantly lower than the usual value for porous anodic alumina, namely ~2.5 nm V-1. Further, the efficiencies of growth film, calculated from the oxygen contents of the films, determined by nuclear reaction analysis, and the charge passed through the cell, were ~0.6 and 0.5 in HSCA and LSCA respectively.

Fig. 2 Bright field transmission electron micrographs of cross-sections of aluminium anodized for (a) 15 s, (b) 30 s, (c) 90 s, (d) 180 s and (e) 360 s at 100 V in 0.4 mol dm-3 high sulphur chromic acid electrolyte (HSCA) at 313 K. Fig. 1 The dependence of the current density on time during anodizing of aluminium at 100 V in 0.4 mol dm-3 chromic acid electrolyte at 313 K. Curve (1) low sulphur electrolyte (LSCA). Curve (2) high sulphur electrolyte (HSCA).

The principal findings of the study are that the incorporation of sulphur species into the films decreases the current density during film growth and reduces the pore size.

Further, the volume expansion factor and the efficiency of film growth are increased.

The contrasts between the film growth in LSCA and HSCA indicate an altered growth mechanism, possibly involving influences of the sulphur on the transport numbers of

Al3+ and O2-, the magnitude and distribution of stress, the density of the film material and the sites of new oxide growth. In previous work, the displacement of an arsenic tracer suggested that major pores may develop by inward transport of film material, which fills the volume created by the oxidation of the aluminium. Further, stress measurements on films have revealed a high compressive stress at the

film/electrolyte interface, which has been attributed to incorporated electrolyte anions. The stress has been proposed to cause oxide flow in the film. Sulphate ions may possibly generate increased compressive stress and promote oxide flow in the present films. From a practical point of view, the sulphur impurity clearly has a significant on the film morphology, which is an important factor in adhesion of paint.

Fig. 4 Scanning electron micrographs (backscattered electrons) of aluminium anodized for 900 s at 100 V in 0.4 mol dm-3 chromic acid at 313 K. (a) Low sulphur electrolyte (LSCA). (b) High sulphur electrolyte (HSCA). The inset shows the films at increased magnification.

Fig. 3 (a) High angle annular dark field transmission electron micrograph and EDX elemental maps of (b) aluminium, (c) oxygen and (d) sulphur for a cross-section of aluminium anodized for 180 s at 100 V in 0.4 mol dm-3 high sulphur chromic acid electrolyte (HSCA) at 313 K.

Acknowledgements: D. Elabar - project PhD student Dr A. Baron-Wiecheć, Dr A. Němcová – PDRAs Publications: 1. “18O tracer study of porous film growth on aluminium in phosphoric acid”, A. Baron-Wiechec, J. J. Ganem, S. J. Garcia-Vergara, P. Skeldon, G. E. Thompson and I. C. Vickridge, Journal of the Electrochemical Society, 157, 399-407, DOI: 10.1179/136217109X12590746472616 (2010).

2. “Role of oxide stress in the initial growth of self-organized porous aluminum oxide”, Ö. Çapraz, P. Shrotriya, P. Skeldon, G. E. Thompson and K. R. Hebert, Electrochimica Acta, 167, 404-411, DOI: 10.1016/j.electacta.2015.03.017 (2015).

3. “Factors controlling stress generation during the initial growth of porous anodic aluminium oxide”, O. Capraz, P. Shrotriya, P. Skeldon, G. E. Thompson and K. R. Hebert, Electrochimica Acta,159, 16-22, DOI: 10.1016/j.electacta.2015.01.183 (2015).

Fig. 5 Scanning electron micrographs (secondary electrons) of the surfaces of aluminium anodized for 360 s at 100 V in (a) 0.4 mol dm-3 low sulphur chromic acid electrolyte (LSCA) and (b) 0.4 mol dm-3 high sulphur chromic acid electrolyte (HSCA) at 313 K and finally immersed in chromic/phosphoric acid to remove the anodic film.

Impact of Shot Peening Forming on Surface Integrity of Aluminum Alloys x. Zhou, g. E. Thompson, P. gai LATEST2, School of materials The university of manchester Shot peen forming is a dieless process performed at room temperature which has been widely used to form various aircraft components. Shot peening usually produces spherically-shaped dents (Figure 1) on the peened component after small, round steel shots impact the surface of the work piece, resulting in stretching of the material in the near-surface region and local plastic deformation that result in residual compressive stress. The compressive stress induces a convex curvature on the peened side. In order to achieve weight reduction and improved service life, integrated construction panels are employed as mainly load-bearing components in wings or the fuselage of large aircraft. Due to the overall size and the complex curves of the large panels, large size shots are used to improve the efficiency of shot peen forming.

In the present study, the microstructure evolution in the near-surface layer induced by a shot peen forming process is investigated. Due to the use of large shots, deep dents are generated on the surface of the alloy and defects, such as microcracks, may develop around the dents. The fatigue life of the formed panels may be influenced by such defects. Thus, it is essential to determine the defect distribution around the dents. The objective of the investigation is to understand the effect of processing parameters on the microstructure in the near-surface layer and, therefore, to optimize shot peen forming for improvement of the mechanical properties of the components.

It was revealed that severe plastic deformation and, consequently, a modified microstructure, including ultrafine grains, microcracks and redistribution of intermetallic particles, were introduced to the near-surface layer (Figure 2). The coarse intermetallic particles in the near-surface layer beneath the dents were broken up into finer ones and redistributed during shot peen forming, which retards the propagation of cracks and, hence, improves the fatigue properties of the alloy. Further, an ultrafine grained structure was produced in the near-surface layer of the dent region on the aluminium alloy subjected to shot peen forming (Figure 3). The co-action of dislocation activities and dynamic recrystallization was considered to be the main mechanism responsible for grain refinement. The thicknesses of the refined grain layers increased with the increasing air pressure.

A

Fig. 1 Optical image of the alloy surface after shot peen forming.

B Fig. 2 3D X-ray volume reconstruction of a dent on the surface of the alloy peened at 0.5 MPa.

Fig. 3 Transmission electron micrograph of a cross section of the near-surface region at the centre of a dent, revealing an altered microstructure characterized by ultrafine grains.

Acknowledgements: This LATEST2 project was performed with support from BAMTRI Publications: P. Gai, Y. Zeng, X. Zhou, G. E. Thompson. Microstructure Evolution in the Near-Surface Layer of AA2024 Aluminum Alloy during Shot Peen Forming, submitted to Acta Materialia.

New Insights into Pore Initiation in Anodic Alumina A. Baron-wiecheć, m.g. Burke, T. hashimoto, h. Liu, P. Skeldon, g. E. Thompson LATEST2, School of materials, The university of manchester Porous anodic films are of great importance to the protection of aluminium alloys against corrosion and wear. The films are composed of amorphous alumina permeated by fine, cylindrical pores that extend from the film surface almost to the metal substrate. A much thinner, nonporous barrier layer separates the pores from the metal, as shown in the example of a transmission electron micrograph of a porous film that was formed in a phosphoric acid electrolyte, presented in Figure 1. Over the last fifty years, the growth of the films and the formation of the pores have usually been explained by a field-assisted dissolution model. In this model, the anodic alumina is formed at the metal/film interface due to migration of O2ions across the barrier layer. The migration takes place under a high electric field at the barrier layer, which is established by the external power supply in the electrolytic cell.

At the same time that the oxide is formed, dissolution occurs at the pore base, such that the barrier layer remains of constant thickness. The dissolution is vastly

accelerated in comparison with the usual chemical dissolution of the film in the electrolyte, which is attributed to the effect of the electric field at the pore base.

There has been a resurgence of interest in porous anodic films, partly due to the interest in potential applications in nanotechnology, but also for the development of new processes that can eliminate the need for anodizing in chromic acid, which is an often favoured process for aerospace applications, but which is now under legislative pressure due to environmental and health reasons. Within the LATEST Portfolio Partnership and LATEST2 programmes, alternative anodizing processes have been investigated in detail, coupled with fundamental research into the growth mechanism of the films. The latter has led to a re-evaluation of the mechanism of pore formation. Firstly, using tungsten tracers, it was shown that the pore growth involves flow of oxide within the barrier layer, with field-assisted dissolution having a minor or negligible role under many conditions of film growth. Thus, as new oxide is added at the base of the barrier layer, oxide within the barrier layer is pushed toward the pore walls due to the stresses associated with the film growth.

The oxide is made plastic due to the ionic transport processes within the barrier layer that involve migration of both Al3+ and O2- ions.

Fig. 2 High angle annular dark field scanning transmission electron micrographs and energy-dispersive X-ray SDD spectrum images of arsenic and phosphorus obtained from a crosssectioned specimen of aluminium following anodizing to 60 V at 5 mA cm-2 in 0.1 mol. dm-3 sodium arsenate electrolyte at 296 K and re-anodizing at 110 V in 0.4 mol dm-3 phosphoric acid electrolyte at 296 K for (a) 15 s and (b) 180 s.

Fig. 1 Transmission electron micrographs of a porous film formed in phosphoric acid on a thin layer of sputtering-deposited aluminium. (a) The original aluminium layer on top of an amorphous layer of anodic alumina. (b) The porous film.

In more recent work, attention has been directed toward the initiation of pores and for this purpose a new tracer approach was developed using arsenic species, which do not migrate during the film growth. The arsenic is introduced into the film by a first stage of anodizing in sodium arsenate electrolyte. The aluminium is then further anodized in a phosphoric acid electrolyte.

Figure 2(a) shows transmission electron micrographs and elemental maps of the film at an early stage of re-anodizing, before the pores have initiated. The arsenic is revealed to be buried slightly below the film surface, and phosphorus species are also present in the outer region of the film. Figure 2(b) shows the film at later stage, when the main pores of the film have begun to form.

The arsenic map discloses a thin band of arsenic within the barrier layer at the base of the pore. The distribution of the arsenic can be explained by the flow of oxide inward from the original surface of the film.

Figure 3 shows schematically the progress of pore development in the anodic alumina film, and the displacement of the arsenic by the flow of oxide. This is the first time that such a process has been demonstrated experimentally. The new tracer approach is currently being further applied to examine pore formation under a range of conditions of film growth, including anodizing in chromic acid which results in a different pore morphology. It also has a potential for application to studies of pore formation in oxides other than porous alumina.

Fig. 3 Schematic diagrams of the formation of anodic films on aluminium. (a) Barrier film formed to 60 V at 5 mA cm-2 in 0.1 mol dm-3 sodium arsenate at 296 K, showing incorporation of arsenic species. (b) Barrier film formed after re-anodizing the specimen depicted in (a) for ~15 s at 110 V in 0.4 mol dm-3 phosphoric acid at 296 K, showing the burial of the arsenic. (c) Nucleation and growth of incipient pores and nucleation of a major pore in the film of (b) following further anodizing in the phosphoric acid. (d) Growth of the major pore. Arsenic species are retained in the film and transported inward by plasticized film.

Publications: 1. “Volume expansion factor and growth efficiency of anodic alumina formed in sulphuric acid”, F. Zhou, A. K. M. Al-Zenati, A. Baron-Wiechec, M. Curioni, S. Garcia-Vergara, H. Habazaki, P. Skeldon, G. E. Thompson, Journal of the Electrochemical Society, 158 (6), C202-C214, DOI: 10.1149/1.3578028 (2011).

2. “Effect of current density and behaviour of second phases in anodizing of a Mg-Zn-RE alloy in a fluoride/glycerol/water electrolyte”, A. Nemcová, I. Kubena, M. Šmíd, H. Habazaki, P. Skeldon and G. E. Thompson, Journal of Solid State Electrochemistry, 179, 394-401, DOI: 10.1007/s10008-015-2864-1 (2015).

3. “Tracer study of pore initiation in anodic alumina formed in phosphoric acid”, A. Baron-Wiechec, M. G. Burke, T. Hashimoto, H. Liu, P. Skeldon, G. E. Thompson, H. Habazaki, J. Ganem, and I. C. Vickridge, Electrochimica Acta, 113, 302-312, DOI: 10.1016/j.electacta.2013.09.060 (2013).

Plasma Electrolytic Oxidation of Coupled Light Metals A. Baron-wiecheć, P. Skeldon, m. curioni, g. E. Thompson LATEST2, School of materials, The university of manchester The use of multi-material components is rapidly increasing in modern designs in order to optimize performance and reduce weight. If these are subject to corrosive environments, protection schemes may be required to ensure durability of the product.

In the case of light metals, protection usually requires application of conversion coatings, anodic coatings and paints as part of a coating system. However, conversion and anodic treatments are usually metalspecific, i.e. designed for application to aluminium, magnesium or titanium parts, and hence are not suited individually to treatment of a mixed-metal component in a single treatment process. However, plasma electrolytic oxidation offers a potential to overcome this difficulty. Plasma electrolytic oxidation involves polarization of a metal at a high potential in an aqueous electrolyte, usually under AC or pulsed DC conditions.

The high potential results in numerous, short-lived discharges on the treated surface, where coating material is formed through a combination of anodic oxidation, thermal oxidation, thermolysis and plasmachemical processes. The mechanism of

Fig. 1 Current density responses of AA7075 alloy/ZE41 alloy couples oxidized in sodium phosphate/sodium silicate electrolyte at 150, 525 and 780 mA cm-2.

coating growth is not well-understood, since the discharges are small and have lifetimes often of the order of microseconds, making it difficult to probe the formation mechanism by conventional approaches. Nevertheless, coatings of up to several hundred microns thickness are readily formed in suitable electrolytes that are regarded as environmentally-friendly and safe to handle. Further, the coatings can provide excellent wear resistance due to the formation of high-temperature, crystalline oxide phases, and can also provide corrosion protection; for the last case, this may require a sealing treatment or paint top-coat since the coatings contain porosity. Many studies are available in the literature on the formation of coatings on aluminium, magnesium and titanium and their respective alloys, usually using different compositions of the electrolyte and different electrical regimes. However, only one study has addressed the applicability of the process to treatment of mixed-metal systems. Thus, within the LATEST2 programme, investigations have been carried out on the treatment of mixed-metal systems consisting of a combination of either aluminium and AA 7075-T6 aluminium alloy or of ZE41 magnesium alloy and AA 7075-T6 aluminium. These have shown the possibility of successfully forming thick coating on both combinations of metals. The work utilized an alkaline

electrolyte and an AC electrical regime, with various RMS current densities applied. A key observation was the requirement to select an appropriate current density to achieve similar thicknesses of coating on the metal combination. Clearly, due to the dissimilar compositions of the metals, the details of the discharge conditions and the coating compositions differ between the two metals. Consequently, the current flow to the two parts is not stable during the coating formation as each of the coupled metals presents a different and varying resistance as the coating builds in thickness, as shown in Figure 1. If an inappropriate current density is employed the currents may diverge, such that large differences in the coating thickness result on the treated metals. However, with proper selection of the current, the current flow to each metal can be maintained at a similar level, such that coatings can be formed of similar morphology and thickness to those on the individually treated metals, as shown in Figure 2. Thus, the work has demonstrated the potential suitability of plasma electrolytic oxidation for the treatment of mixed light alloys. However, further investigation is required to ascertain the general applicability of the approach, for instance to combinations with titanium, to treatments under voltage rather than current control and to combined metals with different area ratios.

Fig. 2 Cross-sections of coatings formed on the coupled AA7075/ZE41 substrates at (a,b) 150 mA cm-2 and (c,d) 525 mA cm-2. (e,f) Coatings formed on the respective individually-oxidized alloys.

Acknowledgements: The authors are grateful to the European Community for financial assistance within the Integrating Activity “Support of Public and Industrial Research Using Ion Beam Technology (SPIRIT)”, under EC contract no.

227012. In addition, they wish to acknowledge the support of the European Community's Seventh Framework Programme FP7/2007-2013 through the award of a Marie Curie Fellowship to ABW under grant agreement No PIEF-GA-2008-219913.

Publications: 1. “Plasma electrolytic oxidation of coupled light metals”, A. Baron-Wiechec, M. Curioni, R. Arrabal, E. Matykina, P. Skeldon and G. E. Thompson, Transactions of the Institute of Metal Finishing, 91 (2), 107-112, DOI: 10.1179/0020296712Z.00000000083 (2013).

Electrochemical Testing Coupled with Real Time Imaging Provides a New Tool for Practical Assessment of Anticorrosion Performance m. curioni and g. E. Thompson LATEST2, School of materials The university of manchester There is general agreement that industrial accelerated corrosion tests such as Salt Spray Test (SST) and others are not always adequate to evaluate real-life performance.

Electrochemical tests, more common in Academia, rely on measuring the response due to an externally applied voltage or current of an immersed corroding surface.

They are fast and provide fundamental information on the corrosion processes but it is debated if they are representative of the real-life behaviour due to the electrical perturbation of the corroding surface.

Further, they are generally not standardized and difficult to standardize, since the optimum test parameters depend on the material-environment combination; optimization and interpretation requires a well-trained operator.

Publications: 1. “Interpretation of electrochemical noise generated by multiple electrodes”, M. Curioni, R.A. Cottis and G. E. Thompson, Corrosion, 69, 158, DOI: 10.5006/0701 (2013).

Electrochemical Noise Analysis is unique among the electrochemical techniques because it does not require the application of probing signal to the corroding surfaces.

In practice, two nominally identical specimens are immersed in a test solution and electrically connected through an external circuit. As a result of corrosion on the surfaces, current and potential fluctuations are detected and recorded.

The theory behind the interpretation of the electrochemical noise signal is well established, but relatively complex. For this reason, a specific software package has been recently developed and distributed online (Figure 1). The package requires minimal user knowledge and estimates electrode impedance (inversely proportional to corrosion rate), average charge (proportional to volume of material corroded) and frequency of corrosion events, as a function of exposure time.

Data obtained from electrochemical noise measurements are intrinsically representative of a freely corroding system because no probing signal is applied.

Further, the use of ready-made software to extract relevant, time-dependent, corrosionrelated quantities, does not require detailed understanding of the underlying theory (Figure 2). For these reasons, the method is an ideal candidate to be standardized (by standardizing the test environment) and to provide simultaneously quantitative fundamental and practical performance data.

2. “An alternative to the use of a zero resistance ammeter for electrochemical noise measurement: Theoretical analysis, experimental validation and evaluation of electrodes asymmetry”, M. Curioni, A. C. Balaskas and G. E. Thompson, Corrosion Science, 77, 281-291, DOI:10.1016/j.corsci.2013.08.014 (2013).

3. "Application of electrochemical noise analysis to corroding aluminium alloys”, M. Curioni, R. A. Cottis and G. E. Thompson, In press, Surface and Interface Analysis, 45 (10), 1564-1569, DOI: 10.1002/sia.5173 (2013).

4. “Reliability of the estimation of polarization resistance of corroding electrodes by electrochemical noise analysis: Effects of electrode asymmetry”, M. Curioni, P. Skeldon and G. E. Thompson, Electrochimica Acta, 105, 642-653, DOI: 10.1016/j.electacta.2013.04.119 (2013).

Being an immersion test, as an added benefit, the surface of the specimens can be imaged in real time and imageanalysis techniques and accelerated footages can be used to highlight the details of corrosion initiation and propagation (Figure 3). The two combined approaches, automated electrochemical noise analysis and associated surface imaging provide a new intuitive, low cost and robust tool for the comparative evaluation of the corrosion performance of protective treatments, inhibitors and paints.

A stand alone cabinet, capable of simultaneously recording and analysing the electrochemical noise signal and the surface appearance of the corroding specimens has been recently developed. Direct comparison of images and time-lapse video allows a rapid identification of the best candidate treatment between competing solutions.

Consideration of the values of lowfrequency noise impedance provides quantitative estimation of the anticorrosion performance. Once finalized and commercially available, it will be a powerful tool for both fundamental and applied corrosion studies, enabling reliable information to be obtained without requiring a highly trained operator.

Fig. 2 Time evolution of the low-frequency noise impedance for two ZE41 magnesium alloy specimens supporting oxide coatings obtained by plasma electrolytic oxidation; a) 10 mA and b) 20 mA for 10 min, corrosive electrolyte: 3.5% NaCl. High values of impedance indicate low corrosion rates, low values of impedance indicate that corrosion is propagating, rapid decrease indicates corrosion initiation. Lines are intended as a guide to the eye.

Fig. 1 Homepage of the website where the electrochemical noise analysis software can be downloaded (www.electrochemicalnoise.com)

Fig. 3 Images acquired during corrosion of ZE41 magnesium alloy supporting oxide coatings obtained by plasma electrolytic oxidation; a) 10 mA and b) 20 mA for 10 min. Red arrows indicate the first sign of coating failure (4h and 12h respectively), corrosive electrolyte: 3.5% NaCl.

Understanding the InďŹ&#x201A;uence of Alloying Elements/Impurity on Corrosion Property of Magnesium Alloys x. Zhou LATEST2, School of materials The university of manchester Magnesium alloys are of great value for engineering applications due to their low density and high strength-to-weight ratio.

A major deficiency is their low corrosion resistance when exposed to aqueous and humid environments. A thorough understanding of the influence of alloying elements/impurity on the corrosion behaviour of magnesium alloys would allow tailoring the microstructure to achieve better corrosion resistance and, would also help in the development of recyclable magnesium alloys, to cut the high cost for the primary magnesium production.

The distribution of iron impurities, has been successfully detected in corrosion products surrounding Fe-rich particles during short immersion in distilled water (Figure 1). It is found that before the initiation of localized corrosion, the Fe-rich particles are the main sites for the cathodic reaction; during the corrosion propagation, the Fe-rich particles can act as cathodes only when they are still attached to the Mg matrix. However, they are oxidized once they are detached from Mg matrix and, consequently, lose their cathodic activity.

The in situ monitoring of corrosion propagation has been successfully achieved using SVET to determine the current distribution on Mg surfaces following immersion in 3.5wt.% NaCl solution.

Generally, the local breakdown of the surface film occurred after 5-10 min immersion. When the anodic activity swept across almost the entire surface, strong localized corrosion occurred at some sites where a strong anodic current was detected.

Fig. 1 Scanning electron micrographs of Mg after immersion in distilled water, showing the distribution of Fe-rich particles in Mg.

Fig. 2 Distribution of current density on Mg surface during immersion in 3.5wt.% NaCl solution. The blue and red colours represent the anodic and cathodic currents respectively.

From the local initiation sites, the corrosion propagated radially and laterally over the surface, leaving a grey network of filaments behind (propagation stage I). Once the surface has been consumed in this first stage, the corrosion propagation changed to a more localised attack (propagation stage II).

Microscopic examination of the two corrosion propagation stages is presented in Figure 3. The filaments developed during stage I are several microns in width and are confined within the near-surface region, with a maximum depth of less than 10 µm.

During stage II, however, severe localised corrosion developed into the bulk material up to hundreds of micrometres.

TEM was employed to investigate cathodic surface activation phenomenon during corrosion propagation. The transmission electron micrograph in Figure 4 clearly shows the presence of an enriched layer which is located between the corrosion product and the intact alloy. Corresponding EDX maps reveal that this layer is enriched in zinc. As zinc is cathodic, with respect to the matrix, the zinc-enriched layer can enhance cathodic activity when in contact with the electrolyte. The findings explain specific corrosion phenomena of magnesium, such as the so called negative difference effect and the cathodic surface activation.

Fig. 3 Secondary electron micrographs of AZ31 alloy after corrosion: (a) the alloy surface after removal of corrosion product, the regions of the two different corrosion propagation stages are separated by the white, dashed line; (b) cross section showing grain boundary attack and preferred crystallographic pitting, taking place simultaneously; (c) a cross section revealing the corrosion propagation under the Mg(OH)2 outer layer.

Fig. 4 Transmission electron micrographs of AZ31 alloy after corrosion: (a) BF image showing the presence of a layer at the corrosion product/alloy interface; (b) HAADF image of a representative region; (c) corresponding EDX maps showing a interfacial layer enriched with zinc.

Acknowledgements: Heike M. Krebs, Juliawati Alias – project PhD Students; Teruo Hashimoto – Experimental Officer Dr Sergiu P. Albu, Dr L Yang, Dr S Pawar – PDRA. Collaborators: Magnesium Elektron, Brunel University Publications: 1. “Corrosion behaviour of pure magnesium with low impurity content but high corrosion rate in 3.5 wt% NaCl solution”, L. Yang, X. Zhou, M. Curioni, S. Pawar, H. Liu, Z. Fan and G. E. Thompson, Journal of Electrochemical Society, 162, C362-368, DOI: 10.1149/2.1041507jes (2015).

2. “Investigation of the microstructure and the influence of iron on the formation of Al8Mn5 particles in twin roll cast AZ31 magnesium alloy”, S. Pawar, X. Zhou, G. E. Thompson and T. Hashimoto, Journal of Alloys and Compounds, 628, 195-198, DOI: 10.1016/j.jallcom.2014.12.028 (2015).

3. “Effect of traces of silicon on the formation of Fe-rich particles in pure magnesium and the corrosion susceptibility of magnesium”, L. Yang, X. Zhou, S. M Liang, R. Schmid-Fetzer, Z. Fan and G. Scamans, Journal of Alloys and Compounds, 619, 396-400, DOI: 10.1016/j.jallcom.2014.09.040 (2015).

4. “Corrosion behaviour of pure magnesium with low impurity content but high corrosion rate in 3.5 wt% NaCl solution”, L. Yang, X. Zhou, M. Curioni, S. Pawar, H. Liu, Z. Fan and G. E. Thompson, Journal of Electrochemical Society, 162, C362-368, DOI: 10.1149/2.1041507jes (2015).

Anodic Film Formation on a Magnesium Alloy Using a Glycerol-based Electrolyte P. Skeldon LATEST2, School of materials The university of manchester The use of magnesium alloys is potentially attractive for many applications owing to their light weight. However, surface treatment is often required in order to provide the requisite corrosion protection.

Electrolytic processes, such as anodizing and plasma electrolytic oxidation, are commonly employed, and a variety of processes is available that produce relatively thick, porous coatings under dielectric breakdown, which are generally used as part of a coating system. Films formed in the absence of dielectric breakdown are also being investigated. However, despite the significant research into the anodizing of magnesium, the understanding of the film growth mechanisms is much less developed in comparison with other light metals. Mechanistic investigations of film growth are made easier when the films are of uniform thickness and relatively unreactive in the electrolyte. Such films have recently been formed using a fluoride/glycol/water electrolyte.

In the present study, the formation of the films on a cast Mg-Zn-RE alloy, supplied by Magnesium Elektron Ltd, with composition 3.2 % Nd, 0.8 % Zr, 0.7 % Zn, 0.2 % Gd, bal. Mg was investigated. The alloy was anodized using a glycerol-based electrolyte containing 0.35 M ammonium fluoride and 5 vol.% of water at 293 K. The microstructure of the alloy, shown in Figure 1, reveals a discontinuous Mg-Zn-RE phase at grain boundaries and clusters of zirconium-rich particles.

Fig. 1 Scanning electron micrograph (backscattered electrons) of the microstructure of the Mg-Zn-RE alloy.

Figure 2 shows a bright field transmission electron micrograph of an anodic film formed above the alloy matrix and the Mg-Zn-RE phase. The light band arrowed is due to the incorporation of the oxide/hydroxide film formed on the alloy before the start of anodizing that acts as an immobile marker. The film is thicker above the Mg-Zn-RE phase than above the matrix, with respective formation ratios of ~2.0 nm V-1 and ~1.2 nm V-1. Further, the light band is located at a depth of ~0.1 of the film thickness, compared with ~0.5 in the film above the matrix, indicating a greater contribution of cation transport to film growth above the matrix. A thinner light band is also present near the centre of the film formed above the second phase.

Ion beam analysis revealed that the band

separates an outer region, where both fluorine and oxygen are present, and an inner region, where oxygen is depleted, indicating that oxygen migrates inward more slowly than fluorine. Neodymium and zinc are distributed throughout the thickness of the film, and zinc is enriched in the alloy at the alloy/film interface.

Electron diffraction showed that the films are nanocrystalline and contain MgO and MgF2.

Fig. 2 Transmission electron micrograph (bright field) and EDX elemental maps for the Mg-Zn-RE alloy following anodizing in a glycerol-fluoride electrolyte.

The anodizing process oxidizes second phase particles, locally modifying the film composition. Figure 3 shows a bright field image of the matrix, where two needle-like particles, which possibly consist of the Zr2Zn3 phase, have been partly oxidized.

Figure 4 shows oxidation of plate-like zinc- and zirconium-rich particles, resulting in zinc- and zirconium-rich material in the inner and outer regions of the film.

The efficiency of anodizing is close to 100 %, as calculated from the ratio of the charges due to the cations in the films and the charges passed though the anodizing

cell, which indicates negligible loss of species to the electrolyte. Studies of crystalline anodic oxide films have generally indicated that ionic transport occurs mostly by migration of oxygen species along short-circuit paths. The present films are strikingly different, since cations and anions have significant mobility in the films. The enrichment of zinc in a thin alloy layer immediately beneath the anodic film is also found in Al-Zn alloys and has been related to the less negative Gibbs free energy per equivalent for formation of zinc oxide in comparison with that for formation of

aluminium oxide. Future work will investigate further the present type of films in order to develop a deeper understanding of the enrichment of alloying elements in the alloy and the ionic transport processes in the film, as well as their corrosion protection properties.

Fig. 3 Transmission electron micrograph (bright field) and EDX elemental maps for the Mg-Zn-RE alloy following anodizing in a glycerol-fluoride electrolyte.

Fig. 4 Transmission electron micrograph (bright field) of the Mg-Zn-RE alloy following anodizing in a glycerol-fluoride electrolyte.

Acknowledgements: Dr A. Němcová – PDRA Dr I. Kuběna – CEITEC IPM, Czech Republic Dr M. Šmíd – Institute of Physics of Materials, AS CR, Czech Republic Publications: 1. “Formation of barrier-type anodic films on sputteringdeposited Al-Ti alloys”, V.C. Nettikaden, A. Baron-Wiechec, P. Bailey, T. C. Q. Noakes, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 3717-3721, DOI: 10.1016/j.corsci.2010.07.022 (2010).

2.“Effect of current density and behaviour of second phases in anodizing of a Mg-Zn-RE alloy in a fluoride/glycerol/water electrolyte”, A. Nemcová, I. Kubena, M. Šmíd, H. Habazaki, P. Skeldon and G. E. Thompson, Journal of Solid State Electrochemistry, 179, 394-401, DOI: 10.1007/s10008-015-2864-1 (2015).

3. “Growth of barrier-type anodic films on magnesium in ethylene glycol electrolytes containing fluoride and water”, H. Habazaki, F. Kataoka, K. Shazad, E. Tsuji, Y. Aoki, S. Nagata, P. Skeldon and G. E. Thompson, Electrochimica Acta, 179, 402 - 410, DOI: 10.1016/j.electacta.2015.02.168 (2015).

Formation of Electroless Nickel-Boron on Magnesium and AZ91D Alloy E. correa1, A. A. Zuleta1, L. guerra1, J. g. castaño1, F. Echeverría1, A. Baron-wiecheć2, P. Skeldon2 and g. E. Thompson2 2 LATEST2, School of materials, The university of manchester Due to a low density and high strength-toweight ratio, magnesium alloys have become a commonly preferred choice for weight reduction in applications such as automobile and computer parts, aerospace components, mobile phones, sporting goods, handheld tools and household equipment. However, poor corrosion and wear resistance are challenges to the successful use of magnesium alloys. Various coatings, which provide a means to avoid direct contact of the alloy with the environment, are being investigated to provide corrosion protection. Recently, electroless nickel–boron has attracted research interest due to its ability to provide a hard, wear and corrosion resistant surface.

The most difficult aspect of the electroless process is often the selection of an appropriate pre-treatment, which should promote a rapid initiation of the electroless coating and minimize corrosion of the substrate. Some plating technologies use hydrofluoric acid (HF) or chromic compounds in order to protect the magnesium surface or to generate a suitably rough surface to enhance coating adhesion. However, such chemicals are hazardous to health. Notably, little work has been reported on the formation of electroless Ni–B on magnesium alloys without the use of these compounds.

Within the LATEST2 programme, in collaboration with the University of Antioquia, procedures have been developed to coat commercial purity magnesium and the general purpose casting alloy AZ91 by means of an electroless Ni–B process that provides a uniform, adherent and continuous layer without employing HF or chromic compounds. The substrates were mechanically polished with wet 100 grit SiC paper, then grit-blasted with alumina (150 μm). A final cleaning was carried out in 37 g/l NaOH and 10 g/l Na3PO4 for 10 min at 65 °C, followed by activation in 200 g/l NH4HF2 at room temperature for 10 min, and finally immersion in an electroless bath containing various additives, listed in Table 1, including NH4HF2, which is easier to handle, less volatile and cheaper than HF.

Table 1. Chemical composition of the electroless nickel plating bath and coating conditions.

Chemical composition NiCl2·6H2O

20 g/l

NaBH4

8 g/l

CH4N2S

1 mg/l

C2H8N2

35 ml/l

NaOH

110 g/l

NH4HF2

Variable

Operating conditions pH

> 12

Temperature

80 °C

Plating time

120 min

Figure 1 shows the typical nodular morphology of the coatings, which can be grown to various thicknesses by selection of the time of immersion in the electroless bath. Control of the fluoride concentration in the electroless bath is important to minimize the corrosion rate of the coated alloy, as demonstrated in Figure 2, which displays the amount of hydrogen gas generated due to corrosion of the coated magnesium in sodium chloride solution. The coatings were formed in baths with a range of fluoride contents, with the results showing that corrosion is accelerated by an excess of fluoride, which is related to generation of porosity in the coating. With an optimized bath composition, corrosion of coated coupons following immersion in sodium chloride solution is limited to the edges and corners, as shown in figure 3.

Further testing has revealed an excellent wear resistance of the coatings, with a greatly reduced wear rate compared with that of the uncoated alloy.

Acknowledgements: 1 Centro de Investigación, Innovación y Desarrollo de Materiales—CIDEMAT, Universidad de Antioquia UdeA, Calle 70 No. 52-21, Medellín, Colombia The authors are grateful to “Departamento Administrativo de Ciencia, Tecnología e Innovación, COLCIENCIAS”, Universidad de Antioquia for financial assistance (project 111545221131 and Estrategia de Sostenibilidad 2013–2014 de la Universidad de Antioquia).

Publications: 1.“Effect of NH4HF2on deposition of alkaline electroless Ni-P coatings as chromium-free pretreatments for magnesium”, A. A. Zuleta, E. Correa, G. E. Thompson, M. Curioni, T. Hashimoto, P. Skeldon and E. Koroleva, Corrosion Science, (55), 194-200, DOI:10.1016/j.corsci.2011.10.028 (2012).

2."Nickel–boron plating on magnesium and AZ91D alloy by a chromium-free electroless process", E. Correa, A.A. Zuleta, M. Sepúlveda, L. Guerra, J.G. Castañoa, F. Echeverría, H. Liub, P. Skeldon, G.E. Thompson, Surface and Coatings Technology, 206, 13, 3088 - 3093, DOI: 10.1016/j.surfcoat.2011.12.023 (2012).

Fig. 2 Dependence of the amount of hydrogen evolved and average weight loss rate on time of immersion in 3.5 wt.% sodium chloride solution for magnesium with electroless Ni–B coatings formed in baths containing different concentrations of NH4HF2.

3.“Tribological behaviour of electroless Ni-B coatings on magnesium and AZ91D alloy”, E. Correa, A. A. Zuleta, L.Guerra, M. Goméz Botero, J. G. Castaño, F. Echeverría, H. Liu, P. Skeldon and G. E. Thompson, Wear 305, 115-123, DOI: 10.1016/j.wear.2013.06.004 (2013).

4.“Formation of electroless Ni-B on bifluoride-activated magnesium and AZ91D alloy”, E. Correa, A. A. Zuleta, L. Guerra, J. G. Castaño, F. Echeverría, A. Baron-Wiechec, P. Skeldon and G. E. Thompson, Journal of the Electrochemical Society, 232, 784-794, DOI: 10.1149/2.012309jes (2013).

Fig. 1 Scanning electron micrographs (backscattered electrons) of magnesium in (a) plan and (b) cross-section after 120 min immersion in an alkaline Ni–B electroless bath containing 5 g/l NH4HF2.

Fig. 3 The appearances of specimens treated in an electroless bath containing 5 g/l before (a, b) and after (c, d) immersion in 3.5 wt.% sodium chloride solution for 60 minutes. Arrows point to locations of corrosion.

5. “Coating development during electroless Ni-B plating on magnesium and AZ91D alloy”, E. Correa, A. A. Zuleta, L. Guerra, M. A. Gómez, J. G. Castaño, F. Echeverría, H. Lui, A. BaronWiechec, T. Hashimoto, P. Skeldon and G. E. Thompson, Surface and Coatings Technology, 232, 784-794, DOI: 10.1016/j.surfcoat.2013.06.100 (2013).

I enjoyed the creative aspects of undertaking academic research.

Heike Krebs, PhD Student

X-ray Computed Tomographic Investigation of the Porosity of Plasma Electrolytic Oxidation Coatings x. Zhang, S. Aliasghari, A. nÄ&#x203A;mcovĂĄ, T. L. Burnett, g. E. Thompson, P. Skeldon and P. J. withers LATEST2, School of materials The university of manchester Plasma electrolytic oxidation (PEO) processes are considered to be amongst the most environmental-friendly surface treatments of aluminium, magnesium and titanium alloys, providing good wear, thermal and corrosion resistance. The coatings have potential for applications in a range of industry sectors, including aerospace, automotive, textile processing, electronic components, energy, oil and gas, leisure and sports products. Porous ceramic coatings are formed during PEO under dielectric breakdown at the sites of micro-discharges. However, porosity in the coatings affects the coating hardness, wear resistance, corrosion resistance and the thermal conductivity. Few studies are available that provide detailed, quantitative

information on the porosity. The present study examines the potential of X-ray CT for characterizing a coating formed on titanium. A Zeiss Xradia Versa 520 lab-based X-ray CT scanner, operated at an accelerating energy of 120 kV, was used to collect the results.

A rough surface, with nodular features and pores, can be seen in the X-ray CT image of the coating (Figure 1). Three regions in a sub-volume (see red box) were selected for detailed investigations: labelled 1, 2 and 3 in Figure 2: (i) a nodule that contains an approximately central pore (1), a nodulefree region (2), and a nodule that appears pore free (3) The physical cross-sections of the regions created in the FIB-SEM were

Fig. 1 X-ray CT data of the PEO coating rendered in 3D giving an overview of the total sample imaged.

(a1)

(a2)

compared to the virtual cross-sections observed by X-ray CT as shown in Figure 3.

The locations of large pores at the coating surface, associated with the nodules, are visualized in Figure 4 (a). The porosity within the coating is also shown in Figure 4 (b).

The pores are mapped onto a map of the roughness of the titanium/coating interface.

The images show a correlation between the locations of the nodules, large pores and depressions in the substrate. Figure 5 reveals the shape of a pore in 3D; the pore within the coating connects to the coating surface, but also exhibits a number of branches.

Fig. 2 (a) X-ray CT data rendering of the chosen 3D sub-volume with distinctive regions highlighted: 1) nodule with central pore; 2) finely porous region; 3) nodule without central pore. (b) Secondary electron SEM image showing the same region with the same features highlighted.

(b1)

(b2)

Fig. 3 Comparison of X-ray CT virtual slices and FIB/SEM cross-sections of (a) the nodule with a central pore, (b) the finely-porous region and (c) the nodule without a central pore.

(c1)

(c2)

The study showed that X-ray CT is capable of resolving and quantifying of volumes of at least 6 µm3. For larger pores, a good correlation is obtained with the size and shape of pores observed by scanning electron microscopy. The larger pores constituted ~5.7% of the coating volume.

The numerous cross-sections available from virtual slicing of the coating enable a more accurate assessment of the variations in coating thickness to be obtained in comparison with conventional crosssectioning. Furthermore, the connectivity of pores beneath nodules is revealed enabling identification of pores that open directly to the coating surface and ones that terminate

in the coating. A model was proposed to explain the development of the pores by flow of molten coating due to the pressure of generated oxygen gas. The ability of X-ray CT to examine and quantify the porosity non-destructively, including its volume, location and interconnected nature, complements conventional electron microscopy of investigation. The technique is unique among those currently available in its ability to quantify the distribution of porosity and its relation to the local coating morphology.

Acknowledgements: The authors thank the Engineering and Physical Sciences Research Council for support of this work through the LATEST 2 Programme Grant (EP/H020047/1) and for funding of the Henry Moseley X-ray Imaging Facility (EP/F007906/1 and EP/F028431/1). This work was partly realized in CEITEC – Central European Institute of Technology – with research infrastructure supported by the project CZ.1.05/1.1.00/02.0068 financed from the European Regional Development Fund.

Fig. 4 X-ray CT images of (a) the coating surface with pores highlighted and (b) additionally showing pores within the coating.

Collaborators: I. Kuběna, Institute of Physics of Materials, AS CR, Žižkova 22, Brno, 616 62, Czech Republic M. Šmíd, CEITEC IPM, Žižkova 22, Brno, 616 62, Czech Republic Publications: 1."X-ray computed tomographic investigation of the porosity and morphology of plasma electrolytic oxidation coatings", X. Zhang, S. Aliasghari, A. Nemcová, T. L. Burnett, I. Kubena, M. Šmíd, G. E. Thompson, P. Skeldon and P. J. Withers, ACS Applied Materials and Interfaces, in press.

Fig. 5 (a) Contour plot showing the titanium/coating interface. The colour scale shows the height of the substrate/coating interface, measured with respect to the lowest point of the interface. Pores have been rendered (in blue). (b) A zoom-inside shows the volcano-like pore in the black circle.

2."Effects of reagent purity on plasma electrolytic oxidation of titanium in an aluminate–phosphate electrolyte", S. Aliasghari, A. Němcová, J. Čížek, A. Gholinia, P. Skeldon, G. E. Thompson, Transactions of the IMF: The International Journal of Surface Engineering and Coatings, 94, 1, 32-42, DOI: 10.1080/00202967.2015.1121692 (2016).

3. "Influence of coating morphology on adhesive bonding of titanium pre-treated by plasma electrolytic oxidation", S. Aliasghari, A. Němcová, P. Skeldon, G. E. Thompson, Surface and Coatings Technology, 289, 101-109, DOI: 10.1016/j.surfcoat.2016.01.042 (2016).

rESEArch ProJEcT LIST Postdoctoral Research Projects Advanced Electrochemical Methods for Evaluation of Corrosion Performance of Light Alloys Alloy Composition/Forming and Performance Anodic Treatments of Light Alloys (Plasma Electrolytic Oxidation/Anodizing) Chromate Replacement in Surface Treatment of Aerospace Alloys (REACH) Development of a Distributable Software Package for Electrochemical Noise Analysis Development of DIC Formability Assessment Methodology and Formability of Mg Alloy Sheets Environmentally-Friendly Anodizing/Corrosion Testing Feasibility Study on Applicability of Advanced Electrochemical Methods for Fast Corrosion Testing of Aerosol Cans Grain Boundary Structure of New Generation Aerospace Alloys Improving the Performance of Extruded Aluminium Interfacial Reaction â&#x20AC;&#x201C; Modelling and Control In Friction Joining and Fusion Welds Modelling Twin Clustering and Its Effect on Formability Nanotomography for Understanding Sensitisation of AA5xxx Aluminium Alloys New chrome-free coatings and inhibitors for protection of aluminium alloys Novel Friction Joining Processes for Dissimilar Metals Novel Friction Joining Processes for Light Alloys Particle/Twin Interactions in Magnesium Alloys Post Anodizing Surface Treatment for Aerospace Applications Process Modelling of Laser Welding and Additive Manufacture Replacement of Copper Conductors with Aluminium Texture and Microstructure Evolution in New Generation Two-Phase Ti Alloys Understanding the Performance of 7xxx Aluminium Alloy Forgings Use of Selected Ionic Fluids for Finishing of Light Alloys

Electron Optics Specialist Projects Use of Advanced Electron optical approaches for understanding the performance of light alloys

Research Assistant Projects Laser welding of aluminium-lithium alloys and performing validation of such models Repair of Armoured Vehicles - Weld Re-Processing

PhD Research Projects Alkali Resistant Anodic Films for Automotive Applications Alloy Design for Large-Scale Additive Manufacturing of Aluminium Aerospace Components A Novel Refill Friction Stir Spot Welding Approach to Joining Automotive Sheets Anodic Films on Titanium Anodizing of Aluminium Alloys with Rare Earth Additions Characterisation and Simulation on Interface in Metallic Matrix Composites Control of Cosmetic Corrosion in Aluminium Automotive Alloys Controlling Interfacial Reaction in Aluminium to Steel Dissimilar Metal Welding Controlling Interfacial Reaction in Titanium to Aluminium for Aerospace Applications Conversion Coatings of Aluminium Corrosion Control of Dissimilar Metals Corrosion Control of Heat Exchange Alloys Corrosion Protection by Encapsulated Inhibitors Deformation Mechanisms in Polycrystalline Materials Studied By Diffraction Contrast Tomography Development of Near-Surface Microstructure and Its Influence on Performance of AA3104 Aluminium Alloy Dynamic Deformation of Magnesium Alloys Effect of Microstructure on Corrosion Resistance and Anodizing Behaviour of AA2099T8 Alloys Environmentally-Friendly Novel Coatings for Aerospace Alloys Excessive Grain Coarsening In IN718 Engine Disc Forgings Friction Joining of Aluminium to Magnesium for Light Weight Automotive Applications Friction Stir Welding of Aluminium AA5xxx Alloys Galvanic Corrosion of Magnesium Alloys Hard Anodising of Aluminium Alloys High Performance Magnesium Alloys for Aerospace Applications High Resolution, Low Voltage Electron Imaging Hybrid Additive Manufacture with Deformation for Large Scale Near Net Shape Manufacture of Titanium Aerospace Components Impact of Fabrication Process on the Performance of Aerospace Aluminium Alloys

PhD Research Projects (continued) Impact of Near Surface Microstructure on the Performance of Metallic Materials Improving Aluminium-To-Magnesium Dissimilar Welding For Lightweight Automobile Applications Influence of Forming On Corrosion of Lean 7000 Alloys Influences of New Electrolyte Formulations on the Anodizing Behaviour and Corrosion Protection of Aerospace and Automotive Aluminium Alloys Interaction of Solute and Second Phase Particle Evolution with Deformation Mechanisms in Commercial Aluminium Alloys Joint Performance and Interface Reactions in Dissimilar Aluminium to Steel Ultrasonic Spot Welding Laser Spot Welding Dissimilar Materials Laser Surface Processing Laser Surface Treatment of Magnesium Alloys Local Electrochemistry/Microstructural Revelation Localised Corrosion of High Strength Aluminium Alloys Mechanism of Pore Formation in Anodic Alumina Metallurgical Performance of Hyper-Joint Pins in Composite to Metal Joining Micro-Galvanic Control of Early Stage Etching of Flat-Rolled Aluminium Products Microstructural Descriptors and Deformation Heterogeneity in Titanium Alloys Microstructure Characterisation and Corrosion Properties of the Heat Affected Zones of the Automotive AA6111 Alloy Microstructure Formability Relationships in New Generation High Strength Aluminium Automotive Alloys Microstructure Modelling For FSW Microstructure, Texture and Mechanical Property Evolution during Additive Manufacturing of Ti6Al4V Alloy for Aerospace Applications Modelling of Friction Welding Processes Modelling of the Friction Spot Welding Process Nanotube Formation on Zirconium Near-Surface Microstructures and their Influence on Performances of 8xxx and AA5182 Aluminium Alloys Novel Environmental Friendly Surface Treatment for Al-Cu-Li Alloys Optimisation of Stationary Shoulder FSW Optimising Precipitate Shape and Habit for Strengthening in Magnesium Alloys Particle Effects on Local Deformation, Recovery and Stored Energy in Aluminium Alloys By Measurement and Simulation Particle Stimulated Nucleation: Deformation around Particles Performance of Recycled Aluminium Alloys Performance of Recycled Magnesium Alloys Plasma Electrolytic Oxidation of Titanium Predicting Performance of Al Armour Alloy Welds under Blast Conditions Prediction of the Role of Defects in Fatigue Failure in Additive Manufactured SEBM Titanium Components Process Quality Relationships in Material Addition Repair of High Value Aerospace Components Qualification of the EBM Wire Fed Process for Manufacture with Ti6Al4V Quantifying Microstructure Heterogeneity and its Effect on Additive Manufactured Ti6Al4V Parts REACH Compliant Strategies for Aerospace Corrosion Prevention Steel to Aluminium Laser Seam Welding Stress Corrosion Cracking of Marine Alloys Surface Integrity of Aerospace Aluminium Alloys Surface Integrity through Tomographic Reconstruction Surface Treatment of Titanium and its Alloys for Adhesion Promotion Synthesis, Characterization and Corrosion Protection Performance of Hybrid Nanocomposite Coatings The Application of Taper Rolling to the Near-Net Shape Manufacture of Aluminium The Effect of Alloying Elements on Deformation by Twinning in Alpha Titanium The Effect of Chromium Content on the Microstructure and Recrystallisation Behaviour of Al-Mg-Si Aluminium Alloys The Effect of Intermetallic Precipitation on the Corrosion Resistance of Ultra High Strength Stainless Aerospace Steels The Effect of Macrozones in Crack Initiation and Propagation in Titanium Alloys The Impact of Warm Forming on the Microstructure and Corrosion Behaviour of Recycled Aluminium Alloys The Origins of Reverse Loading Effects in Aero Engine Alloys Thermo-Mechanical Processing of Advanced RE-Magnesium Alloys Thermo-Mechanical Processing of Magnesium Alloy Elektron 43 Understanding Improved Formability in Mg Alloys Caused by Rare Earth Alloying Additions Understanding the Effect of Microstructure on Strain Localization and Failure in 7xxx Aluminium Alloys Understanding the Formability of Titanium

EngD Research Projects Characterisation of Magnesium Castings Using X-Ray Tomography and Ultrasonic Inspection Industrial Application of USW Aluminium Car Body Panels Interrogation of the Manufacturing Route of Aluminium AA 1050 Alloy Used for Lithographic Application Sol-Gel Coatings for Aerospace Alloys

MPhil Research Projects PEO of Magnesium

MEng Research Projects Dissimilar Refill Spot Welding of Al to Mg Effect of Aluminium on Quasi Static Compression Behaviour of Cross-Rolled Alpha Titanium Effect of Paint Bake Cycle on Friction Stir Spot Welding Of Aluminium Automotive Sheet Effect of Tin and Zirconium on Twinning in Alpha Titanium Fatigue in the Microstructure of Titanium Interpretation of the Effect and Thermodynamics of Copper Interfacial Enrichments on A6111 Alloys Strain Homogeneity of Titanium Alloy With and Without Macrozones The Effect of Zirconium on Twinning in Alpha Titanium

Visitor Research Projects 3-D Imaging of Rheocast Aluminium Alloy Anodic Oxidation of Titanium for Energy Application Anodizing of Titanium and Titanium Alloys Antibacterial Properties of Coatings of Silanols Characterisation of porous anodic films formed on aluminium Coatings on Aerospace Alloys Collaboration of Friction Stir Welding Comparison of Ultrasonic Welding Variants for Al/Ti-Joints by Mechanical and Microstructural Analysis Corrosion and Protection of Mg-RE Alloy Corrosion Performance of Dissimilar Material Joints Development, Optimization and Characterization of Environmentally Friendly Anodic Oxides and Sealing Processes for Corrosion Protection of Aerospace Alloys Electroless Ni-P Coatings on Magnesium Electroless Ni-B Coatings on Magnesium Fatigue of PEO Coated Magnesium Alloy Formation of Porous Films on Iron Laser Shock Peening of Titanium Alloys Low-Density Smart Polymers for Packaging Food Nanoparticle Characterisation for Inhibition/Biocide Activity Nanotube Film Formation on Titanium Alloy Plasma Electrolytic Oxidation of Titanium for Photocatalysis and Energy Conversion Applications Preparation of Electroless Nickel, Electroless Boron Nitride Particle-Reinforced Composite Coating for Improvement of the Wear and Corrosion Resistance of Aluminium Alloys Shock Peening of Aluminium Alloys Sol-Gel Films Suppression of the Formation of Fayalite (Fe2SiO4) By Antioxidant Composed of Refractory Powders for High Si Steel TEM Observation of TiO2 Films Texture evaluation of Mg-based alloys during thermomechanical processing The Effects of Impurities on Chromic Acid Anodizing The Effect of Aluminium on Stress Corrosion Cracking of Mg Alloys Training on Electrochemical Techniques for Corrosion Studies on Light Understanding the Strength of Sharply Textured Magnesium Extrusions

PuBLIcATIonS

12.

“Mechanisms of joint and microstructure formation in high power ultrasonic spot welding 6111 aluminium automotive sheet”, D. Bakavos and P. B. Prangnell, Materials Science and Engineering, 527A, 15, DOI: 10.1002/9781118062111.ch85 (2010).

13.

“Degradation of the corrosion resistance of anodic oxide films through immersion in the anodizing electrolyte”, M. Garca-Rubio, P. Ocon, M. Curioni, G. E. Thompson, P. Skeldon, A. Lavia and I. Garca, Corrosion Science, 52, 7, 2219-2227, DOI: 10.1016/j.corsci.2010.03.004 (2010).

“Control of weld composition when arc welding high strength aluminium alloys using multiple filler wires”, C. G. Pickin, S. W. Williams, P. B. Prangnell, C. Derry and M. Lunt, Science and Technology of Welding and Joining, 15, 6, 491-496, DOI: 10.1179/136217110X12785889549660 (2010).

14.

“Preferential anodic oxidation of second-phase constituents during anodizing of AA2024-T3 and AA7075-T6 alloys”, M. Saenz De Miera, M. Curioni, P. Skeldon and G. E. Thompson, Surface and Interface Analysis, 42, 4, 241 - 246, DOI: 10.1002/sia.3191 (2010).

“Efficacy of active cooling for controlling residual stresses in friction stir welds”, D. G. Richards, P. B. Prangnell, P. J. Withers, S. W. Williams, T. Nagy and S. Morgan, Science and Technology of Welding and Joining, 15, 2, 156-165, DOI: 10.1179/136217109X12590746472490 (2010).

15.

“Deformation twinning in Ti-6Al-4 V during low strain rate deformation to moderate strains at room temperature”, D. G. Leo Prakash, R. Ding, R. J. Moat, I. Jones, P. J. Withers, J. Quinta da Fonseca, M. Preuss, Materials Science and Engineering: A, 527, 21-22, 5734-5744, DOI: 10.1016/j.msea.2010.05.039 (2010).

16.

“Twinning in structural material with a hexagonal close-packed crystal structure”, M. Preuss, J. da Fonseca, V. Allen, D. Prakash and M. Daymond, Journal of Strain Analysis for Engineering Design, 45, 5, 377-389, DOI: 10.1243/03093247JSA624 (2010).

17.

“A model relating tool torque and its associated power and specific energy to rotation and forward speeds during friction stir welding/processing”, S. Cui, Z. W. Chen, J. D. Robson, International Journal of Machine Tools and Manufacture, 50, 7, DOI: 10.1016/j.ijmachtools.2010.09.005 (2010).

18.

“Incipient melting during friction stir processing of AZ91 magnesium castings”, J. D. Robson, S. Cui, Z. W. Chen, Materials Science and Engineering: A, 527, 7299-7304, DOI: 10.1016/j.msea.2010.07.093 (2010).

19.

“Modelling microstructural evolution during multiple pass friction stir welding”, J. D. Robson, P. Upadhyay and A. P. Reynolds, Science and Technology of Welding and Joining, 15, 7, 6, DOI: 10.1179/136217110X12813393169651 (2010).

20.

“Model for grain evolution during friction stir welding of aluminium alloys”, J. D. Robson and L. Campbell, Science and Technology of Welding and Joining, 15, 2, 6, DOI: 10.1179/136217109X12590746472616 (2010).

21.

“18O tracer study of porous film growth on aluminium in phosphoric acid”, A. Baron-Wiecheć, J. J. Ganem, S. J. Garcia-Vergara, P. Skeldon, G. E. Thompson and I. C. Vickridge, Journal of the Electrochemical Society, 157, 399-407, DOI: 10.1179/136217109X12590746472616 (2010).

1.

“Flow modulated ionic migration during porous oxide growth on aluminium”, M. Curioni, E. Koroleva, P. Skeldon and G. E. Thompson, Electrochemica Acta, 55, 23, 7044-7049, DOI: 10.1016/j.electacta.2010.06.088 (2010).

2.

“Enrichment, incorporation and oxidation of copper during anodizing of aluminium - copper alloys”, Surface and Interface Analysis, M. Curioni, F. Roeth, S. Garcia-Vergara, T. Hashimoto, P. Skeldon, G. E. Thompson and J. Ferguson.

42, 4, 234-240, DOI: 10.1002/sia.3139 (2010).

3.

4.

5.

“The behaviour of second phase particles during anodizing of aluminium alloys”, M. Saenz de Miera, M. Curioni, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 7, 2489-2497, 10.1016/j.corsci.2010.03.029 (2010).

6.

“Influence of applied potential on titanium oxide nanotube growth”, A. Valota, M. Curioni, D. Leclere, P. Skeldon, P. Falaras and G. E. Thompson, Journal of the Electrochemical Society, 157, 12, 243-247, DOI: 10.1149/1.3494155 (2010).

7.

“The formation of nano grain structures and accelerated room temperature theta precipitation in a severely deformed Al-4wt%Cu alloy”, Y. Huang and P. B. Prangnell, Acta Materialia, 58, 14, DOI: 10.1016/j.actamat.2009.11.008 (2010).

8.

“Analysis of the homogeneity of particle refinement in friction stir processing Al-Si alloys”, C. Y. Chan, P. B. Prangnell, and S. J. Barnes, Advanced Materials Research, 6, 85-90, DOI: 10.4028/www.scientific.net/AMR.89-91.85 (2010).

9.

“Effects of combined Zr and Mn additions on dispersoid formation and recrystallization behaviour of AA2198 alloy sheet”, D. Tsivoulas, P. B. Prangnell, C. Sigli, B. Bès, Advanced Materials Research, 89-91, 569-273, DOI: 10.4028/www.scientific.net/AMR.89-91.568 (2010).

10.

“Room temperature instability of an Al-4%Cu super saturated solid solution in a nano-crystalline alloy produced by SPD”, Y. Huang and P. B. Prangnell, Journal of Materials Science, 45, 17, 4851, DOI: 10.1007/s10853-010-4318-6 (2010).

11.

“Novel approaches to friction spot welding thin aluminium automotive sheet”, P. B. Prangnell, and D. Bakavos, Materials Science Forum, 638-642, 1237-1242, DOI: 10.4028/www.scientific.net/MSF.638-642.1237 (2010).

22.

“Anodic oxides on InAlP formed in sodium tungstate electrolyte”, A. Suleiman, P. Skeldon, G. E. Thompson, F. Echeverria, M. J. Graham, G. I. Sproule, S. Moisa, T. Quance and H. Habazaki, Corrosion Science, 52, 595-601, DOI: 10.1016/j.corsci.2009.10.019 (2010).

32.

“Influence of current density on the distribution of tungsten tracers in porous anodic films”, F. Zhou, D. J. LeClere, S. J. Garcia-Vergara, P. Skeldon, G. E. Thompson and H. Habazaki, Surface and Interface Analysis, 42, 247-251, DOI: 10.1002/sia.3179 (2010).

23.

“Effect of excimer laser surface melting on the microstructure and corrosion performance of the die cast AZ91D magnesium alloy”, A. E. Coy, F. Viejo, F. J. Garcia-Garcia, Z. Liu, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 387-397, DOI: 10.1016/j.corsci.2009.09.025 (2010).

33.

“Incorporation and migration of phosphorus in anodic alumina films containing tungsten tracer layers”, F. Zhou, D. J. LeClere, S. J. Garcia-Vergara, T. Hashimoto, I. S. Molchan, H. Habazaki, P. Skeldon, and G. E. Thompson, Journal of the Electrochemical Society, 157, 437-443, DOI: 10.1149/1.3499218 (2010).

24.

“Susceptibility of rare-earth magnesium alloys to microgalvanic corrosion”, A. E. Coy, F. Viejo, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 3896-3906, DOI: 10.1016/j.corsci.2010.08.006 (2010).

34.

“Formation of porous anodic titanium oxide films in hot phosphate/glycerol electrolyte”, H. Habazaki, M. Teraoka, Y. Aoki, P. Skeldon and G. E. Thompson, Electrochimica Acta, 55, 3939-3943, DOI: 10.1007/s11665-014-1262-7 (2010).

25.

“Investigation of the mechanism of plasma electrolytic oxidation of aluminium using 18O tracer”, E. Matykina, A. Baron-Wiecheć., R. Arrabal, D. J. Scurr, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 1070-1076, DOI: 10.1016/j.corsci.2009.11.038 (2010).

35.

“Differentiation of 180- and 160-rich layers in anodic alumina films by glow discharge time-of-flight mass spectroscopy“, I. S. Molchan, G. E. Thompson, P. Skeldon, N. Trigoulet, A. Tempez, P. Chapon, N. Tuccitto and A. Licciardello, Surface and Interface Alaysis, 211-214, DOI: 10.1002/sia.3227 (2010).

26.

“Optimization of the plasma electrolytic oxidation process efficency on aluminium”, E. Matykina, R. Arrabal, P. Skeldon, G. E. Thompson, Surface and Interface Analysis, 42, 221-226, DOI: 10.1002/sia.3140 (2010).

36.

“Impurity-driven defect generation in porous anodic alumina”, I. S. Molchan, T. V. Molchan, N. V. Gaponeneko.

P. Skeldon and G. E. Thompson, Electrochemistry Communications, 12, 693-696, DOI: 10.1016/j.elecom.2010.03.008 (2010).

27.

“AC PEO of aluminium with porous alumina precursor films”, E. Matykina, R. Arrabal, P. Skeldon, G. E. Thompson and P. Belenguer, Surface and Coatings Technology, 205, 1668-1678, DOI: 10.1016/j.surfcoat.2010.05.014 (2010).

37.

28.

“Plasma electrolytic oxidation of a zirconium alloy under AC conditions”, E. Matykina, R. Arrabal, P. Skeldon, G. E. Thompson, P. Wang and P. Wood, Surface and Coatings Technology, 204, 2142-2151, DOI: 10.1016/j.surfcoat.2009.11.042 (2010).

“Influence of pre-treatment on the surface composition of Al-Zn alloys.” M. Gentile, E. V. Koroleva, P. Skeldon, G. E. Thompson, P. Bailey and T. C. Q. Noakes, Corrosion Science, 52, 688-694, DOI: 10.1016/j.corsci.2009.10.023 (2010).

38.

“Influence of grain orientation on zinc enrichment and surface morphology of an Al-Zn alloy”, M. Gentile, E. V. Koroleva, P. Skeldon, G. E. Thompson, P. Bailey and T. C. Q. Noakes, Surface and Interface Analysis, 42, 287-292, DOI: 10.1002/sia.3147 (2010).

39.

“Surface topography effects on glow discharge depth profiling analysis.” N. Trigoulet, T. Hashimoto, I. S. Molchan, P. Skeldon, G. E. Thompson, A. Tempez and P. Chapon, Surface and Interface Analysis, 42, 328-333, DOI: 10.1002/sia.3165 (2010).

40.

“Influence of water content on the growth of anodic TiO2 nanotubes in fluoride containing ethylene glycol electrolytes.”

P. Schmuki, S. Berger, J. Kunze, A. Valota, D. LeClere, P. Skeldon and G. E. Thompson, Journal of the Electrochemical Society, 157, C18-C23, DOI: 10.1149/1.3251338 (2010).

41.

“In-vitro evaluation of cell proliferation and collagen synthesis on titanium following plasma electrolytic oxidation”, P. Whiteside, E. Matykina, J. E. Gough, P. Skeldon and G. E. Thompson, Journal of Biomedical Materials Research, 94A, 38-46, DOI: 10.1002/jbm.a.32664 (2010).

29.

“Anodic zirconia nanotubes: composition and growth mechanism”, F. Muratore, A. Baron-Wiecheć, T. Hashimoto, P. Skeldon and G. E. Thompson, Electrochemistry Communications, 12, 1727-1730, DOI: 10.1016/j.elecom.2010.10.007 (2010).

30.

“Relationship between microstructure and corrosion performance of the AA2050-T8 aluminium alloy after excimer laser surface melting”, F. Viejo, A. E. Coy, Z. Liu, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 2179-2187, DOI: 10.1016/j.corsci.2010.03.003 (2010).

31.

“Performance of Al alloys following excimer LSM-anodizing approaches”, F. Viejo, Z. Aburas, A. E. Coy, F. J. Garcia-Garcia, T. Hashimoto, Z. Liu, P. Skeldon and G. E. Thompson, Surface and Interface Analysis, 42, 252-257, DOI: 10.1002/sia.3144 (2010).

42.

“Corrosion behaviour of a magnesium matrix composite with silicate plasma electrolytic oxidation coating”, R. Arrabal, A. Pardo, M. C. Merino, M. Mohedano, P. Casajús, E. Matykina, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 3738-3749, DOI: 10.1016/j.corsci.2010.07.024 (2010).

43.

“Tracer studies relating to alloying element behaviour in porous anodic alumina formed in phosphoric acid”, S. J. Garcia-Vergara, H. Habazaki, P. Skeldon and G. E. Thompson, Electrochimica Acta, 55, 3175-3184, DOI: 10.1016/j.electacta.2010.01.038 (2010).

44.

45.

“Formation of barrier-type anodic films on sputteringdeposited Al-Ti alloys”, V.C. Nettikaden, A. Baron-Wiecheć, P. Bailey, T. C. Q. Noakes, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 3717-3721, DOI: 10.1016/j.corsci.2010.07.022 (2010).

“Calcium and titanium release in simulated body fluid from plasma electrolytically oxidized titanium”, Y. Zhang, E. Matykina, P. Skeldon and G. E. Thompson, Journal of Materials Science: Materials for Medicine, 21, 81-88, DOI: 10.1007/s10856-009-3850-x (2010).

52.

“Electrochemical techniques for practical evaluation of corrosion inhibitor effectiveness Performance of cerium nitrate as corrosion inhibitor for AA2024T3 alloy”, N. Rosero-Navarro, M. Curioni, R. Bingham, A. Duran, M. Aparicio, R. Cottis and G. E. Thompson, Corrosion Science, 52 (10), 3356-3366, DOI: 10.1016/j.corsci.2010.06.012 (2010).

53.

“Performance of Al alloys following excimer LSM - anodizing approaches”, F. Viejo, Z. Aburas, A. Coy, F. Garcia-Garcia, Z. Liu, P. Skeldon and G. E. Thompson, Surface and Interface Analysis, 42 (4), 252-257, DOI: 10.1002/sia.3144 (2010).

54.

“Enhanced performance of the AA2050-T8 aluminium alloy following excimer laser surface melting and anodizing processes.” F. Viejo, A. Coy, F. Garcia-Garcia, M. Merino, Z. Liu, P. Skeldon and G. E. Thompson, Thin Solid Films, 518 (10), 2722-2731, DOI: 10.1016/j.corsci.2009.09.025 (2010).

55.

“Stress-enhanced growth rate of alumina scale formed on FeCrAlY alloy”, X. Zhao, F. Yang, A. Shinmi, P. Xiao, I. Molchan and G. E. Thompson, Scripta Materialia, 63 (1), 117-120, DOI: 10.1016/j.scriptamat.2010.03.031 (2010).

46.

“Crack-free sol-gel coatings for protection of AA1050 aluminium alloy. Surface and Interface Analysis”, Z. Feng, Y. Liu, G. E. Thompson and P. Skeldon, Electrochemica Acta 42, 306-310, DOI: 10.1002/sia.3162 (2010).

56.

“Co-operative corrosion phenomena”, A. Hughes, T.H. Muster, A. Boag, A. M. Glenn, C. Luo, X. Zhou, G. E. Thompson and D. McCulloch, Corrosion Science, 52, 665-668, DOI: 10.1016/j.corsci.2009.10.021 (2010).

47.

“Detection of negative ions in glow discharge mass spectrometry for analysis of solid specimens.” S. Canulescu, I. Molchan, C. Tauziede, A. Tempez, J. Whitby, G. E. Thompson, P. Skeldon, P. Chapon and J. Michler, Analytical and Bioanalytical Chemistry, 396 (8) 2871-2879, DOI: 10.1007/s00216-009-3366-8 (2010).

57.

“The ubiquitous beilby layer on aluminium surfaces”, G. M. Scamans, M. F. Frolish, W. M. Rainforth, Z. Zhou, Y. Liu, X. Zhou and G. E. Thompson, Surface and Interface Analysis, 42, 175-179, DOI: 10.1002/sia.3204 (2010).

58.

“Surface structure”, G. E. Thompson, X. Zhou, Materials World, 18, 26-27, DOI: 10.1016/j.matlet.2011.06.088 (2010).

59.

“Nanotomography for understanding materials degradation”, T. Hashimoto, X Zhou, C. Luo, K. Kawano, G. E. Thompson, A. E. Hughes, P. Skeldon, P. J. Withers, T. J. Marrow and A. H. Sherry, Scripta Materialia, 63, 835-838, 10.1016/j.scriptamat.2010.06.031(2010).

60.

“Corrosion behaviour of mechanically polished AA7075-T6 aluminium alloy”,Y. Liu, A. Laurino, T. Hashimoto, X. Zhou, P. Skeldon, G. E. Thompson, G. M. Scamans, C. Blanc, W. M. Rainforth and M. F. Frolish, Surface and Interface Analysis, 42, 185-188, DOI: 10.1002/sia.3136 (2010).

61.

“Evolution of near-surface deformed layers during hot rolling of AA3104 aluminium alloy”, Y. Liu, M. F. Frolish, W. M. Rainforth, X. Zhou, G. E. Thompson, G. M. Scamans and J. A. Hunter, Surface and Interface Analysis, 42, 180-184, DOI: 10.4028/www.scientific.net/MSF.765.358 (2010).

62.

“Effect of Al8Mn5 intermetallic particles on grain size of as-cast Mg-Al-Zn AZ91D alloy”, Y. Wang, M. Xia, Z. Fang, X Zhou and G. E. Thompson, Intermetallics,18, 1683-1689, DOI: 10.1016/j.intermet.2010.05.004 (2010).

48.

“Anodic film formation on binary al-mg and Al-Ti alloys in nitric acid", F. Garcia-Garcia, E. Koroleva, G. E. Thompson and G. Smith, Surface and Interface Alaysis, 258-263, DOI: 10.1016/j.corsci.2011.12.035 (2010).

49.

“Galvanostatic growth of nanoporous anodic films on iron in ammonium fluoride-ethylene glycol electrolytes with different water contents”, H. Habazaki, Y. Konno, Y. Aoki, P. Skeldon, and G. E. Thompson, Journal of Physical Chemistry C, 114 (44), 18853-18859, DOI: 10.1021/jp1078136 (2010).

50.

51.

“Investigation of the mechanism of plasma electrolytic oxidation of aluminium using O-18 tracer”, E. Matykina, R. Arrabal, D. Scurr, A. Baron, P. Skeldon, and G. E. Thompson, Corrosion Science, 52 (3), 1070-1076, DOI: 10.1016/j.corsci.2009.11.038 (2010).

“Analysis of thin impurity doped layers in anodic alumina and anodic tantala films by glow discharge time-of-flight mass spectrometry”, I. Molchan, G. E. Thompson, P. Skeldon, N. Trigoulet, A. Tempez and P. Chapon, Transactions of the Institute of Metal Finishing, 88 (3), 154-157, DOI: 10.1179/174591910X12692576434617 (2010).

63.

“Electron and photon based spatially resolved techniques”, X. Zhou and G. E. Thompson, In B. Cottis et al (Ed.), Shreir`s Corrosion, 1405-1429 (2010)

64.

“Solid-state welding of aeroengine materials”, M. Preuss and P. Threadgill, In R. Blockley and W. Shyy (Ed.), Encyclopedia on Aerospace Engineering ,2355-2368 (2010)

65.

“Simulation of joining operations A: Rotational welding”, P. J. Withers and M. Preuss, In D. U. Furrer and S. L. Semiatin (Ed.), ASM International Handbook, 22,432-455 (2010)

66.

“New metallic materials for aeroengines - or understanding what we use today”, M. Preuss, Engine Yearbook. (2010)

67.

“Sol-gel coatings for corrosion protection of 1050 aluminium alloy”, Y. Liu, G. E. Thompson, P. Skeldon, Electrochimica Acta, 55 (10), 3518-3527, DOI: 10.1016/j.electacta.2010.01.074 (2010).

68.

“Influence of applied potential on titanium oxide nanotube growth”, M. Curioni, D. J. Leclere, P. Skeldon, P. Falaras, G. E. Thompson , Journal of The Electrochemical Society, 157, 12, DOI: 10.1149/1.3494155 (2010).

69.

“Material interactions in a novel pinless tool approach to friction stir spot welding thin aluminium sheet”, Y. Chen, B. Laurent, P. B. Prangnell, Metallurgical and Materials Transactions A, 42, 5, 1266-1282, DOI: 10.1007/s11661-010-0514-x (2010).

75.

“Volume expansion factor and growth efficiency of anodic alumina formed in sulphuric acid”, F. Zhou, A. K. M. Al-Zenati, A. Baron-Wiecheć, M. Curioni, S. Garcia-Vergara, H. Habazaki, P. Skeldon, G. E. Thompson, Journal of the Electrochemical Society, 158 (6), C202-C214, DOI: 10.1149/1.3578028 (2011).

76.

“A combined approach to microstructure mapping of an Al-Li AA2199 Friction Stir Weld”, A. Steuwer, M. Dumont, J. Altenkirch, S. Birosca, A. Deschamps, P. B. Prangnell, P. J. Withers, Acta Materialia, 59 (8), 3002-3011, DOI: 10.1016/j.actamat.2011.01.040 (2011).

77.

“Microstructure simulation and ballistic behaviour of weld zones in friction stir welds in high strength aluminium 7xxx plate”, A. Sullivan, C. Derry, J. D. Robson, I. Horsfall, P. B. Prangnell, Materials Science and Engineering: A, 528 (9), 3409-3422, DOI: 10.1016/j.msea.2011.01.019 (2011).

78.

“Material interactions in a novel pinless tool approach to friction stir spot welding thin aluminium sheet”, D. Bakavos, Y. C. Chen, L. Babout and P. B. Prangnell, Metallurgical and Materials Transactions A, 42A (5), 1266-1282, DOI: 10.1007/s11661-010-0514-x (2011).

79.

“Ultrasonic spot welding of aluminium to steel for automotive applications”, F. Haddadi, Y. C. Chen, and P. B. Prangnell, microstructure and optimisation, Materials Science and Technology, 27 (3), 617-624, DOI: 10.1179/026708310X520484 (2011).

80.

“Effect of zinc coatings on joint properties and interface reaction in aluminium to steel ultrasonic spot welding”, F. Haddadi, D. Strong and P. B. Prangnell, The Minerals, Metals and Materials Society (JOM), 64 (3), 407-413, DOI: 10.1007/s11837-012-0265-9 (2011).

81.

“Solid state joining of metals by linear friction welding: a literature review”, I. Bhamji, M. Preuss, P. L. Threadgill, A. C. Addison, Materials Science and Technology, 27 (1), 2-12, DOI: 10.1179/026708310X520510 (2011).

70.

“Simulation of rotational welding operations”, P. J. Withers, M. Preuss, ASM Handbook, Volume 22B - Metals Process Simulation, 432-455, (2010).

71.

“Corrosion of dissimilar alloys: electrochemical noise”, M. Curioni, R. Cottis, M. Di Natale and G. E Thompson, Electrochimica Acta, 56 (18), 6318-6329, DOI: 10.1016/j.electacta.2011.05.034 (2011).

72.

“Electrochemical noise analysis on multiple dissimilar electrodes: theoretical analysis”, M. Curioni, R. Cottis, M. Di Natale and G. E. Thompson, Electrochimica Acta, 56 (27), 10270-10275, DOI: 10.1007/s10800-011-0295-y (2011).

82.

“Effect of precipitate shape on slip and twinning in magnesium alloys” J. D. Robson, N. Stanford, M. R. Barnett, Acta Materialia, 56 (5), 11, DOI: 10.1016/j.actamat.2010.11.060 (2011).

73.

“Reducing the energy cost of protective anodizing”, M. Curioni, P. Skeldon, J. Ferguson and G. E. Thompson, Journal of Applied Electrochemistry, 41 (7), 773-785, DOI: 10.1007/s10800-011-0295-y (2011).

83.

“Effect of extrusion conditions on microstructure, texture, and yield asymmetry in Mg-6Y-7Gd-0.5 wt%Zr alloy”, J. D. Robson, A. M. Twier, G. W. Lorimer, P. Rogers, Materials Science and Engineering A, 528 (24), 7247-7256, DOI: 10.1016/j.msea.2011.05.075 (2011).

74.

“Glass-like CexOy sol-gel coatings for corrosion protection of aluminium and magnesium alloys” N. Rosero-Navarro, M. Curioni, Y. Castro, M. Aparicio, G. E. Thompson, A Surface and Coatings Technology, 206 (2-3), 257-264, DOI: 10.1016/j.surfcoat.2011.07.006 (2011).

84.

“Application of X-ray microtomography to analysis of cavitation in AZ61 magnesium alloy during hot deformation”, H. M. M. A. Rashed, J. D. Robson, P. S. Bate, B. Davis, Materials Science and Engineering A, 528 (6), 9, DOI: 10.1016/j.msea.2010.11.083 (2011).

85.

“Particle effects on recrystallization in magnesium–manganese alloys: Particle pinning”, J. D. Robson, D. T. Henry, B. Davis.

Materials Science and Engineering: A, 528 (12), 8, DOI: 10.1016/j.msea.2011.02.030 (2011).

86.

“Surface topography evolution through production of aluminium offset lithographic plates”, B. Rivett, E. V. Koroleva, F. J. Garcia-Garcia, J. Armstrong, G. E. Thompson and P. Skeldon, Wear, 270, 204-217, DOI: 10.1016/j.wear.2010.10.061 (2011).

87.

88.

89.

90.

91.

92.

93.

“Comparison of nanotube formation on zirconium in fluoride/glycerol electrolytes at different anodizing potentials” F. Muratore, A. Baron-Wiecheć, A. Gholinia, T. Hashimoto, P. Skeldon and G. E. Thompson, Electrochimica Acta, 58, 389-398, DOI: 10.1016/j.electacta.2011.09.062 (2011).

“Growth of nanotubes on zirconium in glycerol/fluoride electrolytes”, F. Muratore, A. Baron-Wiechéc, T. Hashimoto, A. Gholinia, P. Skeldon and G. E. Thompson, Electrochimica Acta, 56, 10500-10506, DOI: 10.1016/j.electacta.2010.12.089 (2011).

“Effect of ageing in the electrolyte and water on porous films on zirconium”, F. Muratore, T. Hashimoto, P. Skeldon, G. E. Thompson, Corrosion Science, 53, 2299-2305, 10.1016/j.corsci.2011.03.014 (2011).

“Volume expansion factor and growth efficiency of anodic alumina formed in sulphuric acid”, F. Zhou, A. K. Mohamed Al-Zenati, A. Baron-Wiecheć, M. Curioni, S. J. Garcia-Vergara, H. Habazaki, P. Skeldon and G. E. Thompson, Journal of the Electrochemical Society, 158, C202-C214, 10.1149/1.3578028 (2011).

“Depth profiling analysis of barrier-type anodic aluminium oxide films formed on substrates of controlled roughness”, N. Trigoulet, N. Tuccitto, I. Delfanti, A. Licciardello, I. S. Molchan, P. Skeldon, G. E. Thompson, A. Tempez and P. Chapon, Surface and Interface Analysis, 43, 183-186, DOI: 10.1016/j.msea.2010.11.083 (2011).

“Effect of microplasma modes and electrolyte composition on micro-arc oxidation coatings on titanium for medical applications”, O.P. Terleeva, P. Sharkeev, A. I. Slonova, I. V. Mironov, E. V. Legostaeva, I. A. Khlusov, E. Matykina, P. Skeldon, and G. E. Thompson, Surface and Coatings Technology, 205, 1723-1729, DOI: 10.1016/j.msea.2011.02.030 (2011).

“Control of morphology and surface wettability of anodic niobium oxide microcones formed in hot phosphate-glycerol electrolytes”, S. Yang, H. Habazaki, T. Fujii, Y. Aoki, P. Skeldon and G. E. Thompson, Electrochimica Acta, 56, 7446-7453, 10.1016/j.electacta.2011.07.005 (2011).

94.

“Growth of porous anodic alumina films in hot phosphate-glycerol electrolyte”, S. Yang, Y. Aoki, P. Skeldon, G. E. Thompson and H. Habazaki, Journal of Solid-State Electrochemistry, 15, 689-696, 10.1007/s10008-010-1141-6 (2011).

95.

“Incorporation and migration of phosphorus species within anodic films on an Al-W alloy”, S. J. Garcia-Vergara, I. S. Molchan, F. Zhou, H. Habazaki, D. Kowalski, P. Skeldon and G. E. Thompson, Surface and Interface Analysis, 43, 893-902, 10.1149/1.3499218 (2011).

96.

“Anodic film formation on AA 2099-T8 aluminum alloy in tartaric-sulfuric acid”, X. Zhou, Y. Ma, G. E. Thompson, M. Curioni, T. Hashimoto, P. Skeldon, P. Thomson and M. Fowles, Journal of the Electrochemical Society, 158, C17-C22, DOI: 10.1149/1.3523262 (2011).

97.

“Discontinuities in the porous anodic film formed on AA2099-T8 aluminium alloy”, Y. Ma, X. Zhou, G. E. Thompson, M. Curioni, X. Zhong, E. Koroleva, P. Skeldon, P. Thomson, M. Fowles, Corrosion Science, 53, 4141-4151, DOI: 10.1016/j.corsci.2011.08.023 (2011).

98.

“Formation and composition of nanoporous films on 316L stainless steel by pulsed polarization”, J. Doff, P. E. Archibong, G. Jones, E. V. Koroleva, P. Skeldon, G. E. Thompson, Electrochimica Acta, 56, DOI: 10.1016/j.electacta.2011.01.038 (2011).

99.

“Effect of cooling rate and substrate thickness on spallation of alumina scale on Fe Cr alloy”, C. Zhu, X. Zhao, I. S. Molchan, G. E. Thompson and P. Xiao, Materials Science and Engineering A, 528, 8687-8693, DOI: 10.1016/j.msea.2011.08.044 (2011).

100. “Corrosion of AA2024-T3 Part III: Propagation”, A. Glenn, T. Muster, C. Luo, X. Zhou, G. E Thompson, A. Boag, and A. Hughes, Corrosion Science, 53 (1), 40-50, DOI: 10.1016/j.corsci.2010.09.035 (2011).

101. “Characterisation of plasma electrolytic oxidation coatings on Zircaloy-4 formed in different electrolytes with AC current regime”, Y. Cheng, E. Matykina, P. Skeldon and G. E. Thompson, Electrochimica Acta, 56, 8467-8476.

DOI: 10.1016/j.electacta.2011.07.034 (2011).

102. “Corrosion of AA2024-T3 part II: co-operative corrosion”, A. Boag, A. M. Glenn, D. McCulloch, T. H. Muster, C. Ryan, C. Luo, X. Zhou, G. E. Thompson and A. E. Hughes, Corrosion Science, 53, 27-39. DOI:10.1016/j.corsci.2010.09.030 (2011).

103. “A silanol-based nanocomposite coating for protection of AA2024 aluminium alloy”, E. Gonzalez, J. Pavez, I. Azocar, J. H. Zagal, F. Melo, X. Zhou, G. E. Thompson and M. A. Páez, Electrochimica Acta, 56, 7586-7595.

DOI:10.1016/j.electacta.2011.06.082 (2011).

104. “The characterisation and performance of Ce(dbp)3-inhibited epoxy coatings”, J. Mardel, S. J. Garcia, P. A. Corrigan, T. Markley, A. E. Hughes, T. H. Muster, D. Lau, T. G. Harvey, A .M. Glenn, P. A. White, S. G. Hardin, J. M. C. Mol, C. Luo, X. Zhou, G. E. Thompson, Progress in Organic Coatings, 70, 91-101, DOI:10.1016/j.porgcoat.2010.10.009 (2011).

105. “Near-surface deformed layers on rolled aluminium alloys”, X. Zhou, Y. Liu, G. E. Thompson, G. M. Scamans, P. Skeldon and J. A. Hunter, Metallurgical and Materials Transactions A, 42, 1373-1385, DOI:10.1007/s11661-010-0538-2 (2011).

113. “High strength aluminium alloys: microstructure, corrosion and principles of protection”, A. E. Hughes, N. Birbilis, J. C. M. Mol, S. J. Garcia, X. Zhou and G. E. Thompson, InTech Publications, In Z. Ahmad (Ed.), 223-262 (1), DOI: 10.5772/18766 (2012).

114. “Single-step fabrication of metal nanoparticle loaded mesoporous alumina through anodizing of a commercial aluminum alloy”, Y. Ma, X. Zhou, G. E. Thompson, M. Curioni, T. Hashimoto, P. Skeldon, and E. Koroleva, Electrochemical and Solid-State Letters, 15 (1), E4-E6, DOI: 10.1149/2.019201esl (2012).

115. “Effect of wall thickness transitions on texture and grain structure in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A Antonysamy, P. B. Prangnell and J. Meyer, Materials Science Forum, 706 - 709, 205-2010, DOI: 10.4028/www.scientific.net/MSF.706-709.205 (2012).

106. “Distribution of intermetallics in an AA2099-T8 aluminium alloy extrusion”, Y. Ma, X. Zhou, G. E. Thompson, T. Hashimoto, P. Thomson and M. Fowles, Materials Chemistry and Physics, 126, 46-53, DOI:10.1016/j.matchemphys.2010.12.014 (2011).

116. “The effect of high strain rate deformation on intermetallic reaction during ultrasonic welding aluminium to magnesium”, A. Panteli, J. D. Robson, I Brough and P. B. Prangnell, Materials Science and Engineering A, 556, 31-42; DOI:10.1016/j.msea.2012.06.055 (2012).

107. “Characterisation of magnesium oxide and its interface with α-Mg in Mg-Al based alloys”, Y. Wang, Z. Fan, X. Zhou and G. E. Thompson, Philosophical Magazine Letters, 91, 516-529, DOI:10.1080/09500839.2011.591744 (2011).

117. “Interactions between zirconium and manganese dispersoid-Forming elements on their combined addition in Al-Cu-Li alloys”, D. Tsivoulas, J. D. Robson, C. Sigli, P. B. Prangnell, Acta Materialia, 60, 5245–5259.

DOI:10.1016/j.actamat.2012.06.012 (2012).

108. “On the impact of second phase particles on twinning in magnesium alloys”, N. Stanford, J. Geng, J. D. Robson, M. R. Barnett, Magnesium Technology 2011, 289-293, DOI: 10.1002/9781118062029.ch55 (2011).

109. “Mechanisms of joint formation in ultrasonic spot welding aluminium automotive sheet” Y. C. Chen, P. B. Prangnell, D. Bakavos, Supplemental Proceedings: Materials Processing and Energy Materials, Volume 1, 735 – 742, DOI: 10.1002/9781118062111.ch85 (2011).

110. “Control of morphology and surface wettability of anodic niobium oxide microcones formed in hot phosphate-glycerol electrolytes”, H. Habazaki, F. Takashi, A. Yoshitaka, P. Skeldon, G. E. Thompson, S. Yang, Electrochimica Acta, 56, 22, 7446-7453, DOI: 10.1016/j.electacta.2011.07.005 (2011).

111. “In-Situ observation and modelling of intergranular cracking in polycrystalline alumina”, D. Gonzalez, M. Aswad, J. Quinta Da Fonseca, P. J. Withers, J. T. Marrow, Key Engineering Material, 465, 560-563, DOI: 10.4028/www.scientific.net/KEM.465.560 (2011).

112. “Inertia friction welding (IFW) for aerospace applications”, M.M. Attallah, M. Preuss, Welding and Joining of Aerospace Materials, 25-74, DOI: 10.1533/9780857095169.1.25 (2011).

118. “Microstructure and performance of a biodegradable Mg–1Ca–2Zn–1TCP composite fabricated by combined solidification and deformation processing”, D.-B. Liu, Y. Huang, P. B. Prangnell, Materials Letters, 82, 7-9, DOI: 10.1016/j.matlet.2012.05.035 (2012).

119. “Modelling intermetallic phase formation in dissimilar metal ultrasonic welding of aluminium and magnesium alloys”, J. D. Robson, A. Panteli, P. B. Prangnell, Science and Technology of Welding and Joining, 17, 447-453, DOI: 10.1179/1362171812Y.0000000032 (2012).

120. “Interface structure and bonding in abrasion circle friction stir spot welding: A novel approach for rapid welding aluminium alloy to steel automotive sheet”, Y. C. Chen, A. Gholinia, P. B. Prangnell, Materials Chemistry and Physics, 134, 459-463. DOI:10.1016/j.matchemphys.2012.03.017 (2012).

121. “Optimisation of aluminium to magnesium ultrasonic spot welding”, A. Panteli, Y. C. Chen, D. Strong, X. Zhang and P. B. Prangnell, Journal of Materials, 64 (3), 414-420, DOI:10.1007/s11837-012-0268-6 (2012).

122. “HAZ development and accelerated post-weld natural ageing ultrasonic spot welding aluminium 6111-T4 automotive sheet,” Y. C. Chen, D. Bakavos, A. Gholinia, P. B. Prangnell, Acta Materialia, 60, 2816-2828.

DOI:10.1016/j.actamat.2012.01.047 (2012).

123. “Influence of temperature upon the texture evolution and mechanical behaviour of Zircaloy-4”, P. Honniball, M. Preuss, J. Quinta da Fonseca, Materials Science Forum, 702-703, 834-837. DOI:10.4028/www.scientific.net/MSF.702-703.834 (2012).

124. “In situ observation on the influence of β grain growth on texture evolution during phase transformation in Ti-6A-4V”, G. C. Obasi, R. J. Moat, D. G. Leo Prakash, W. Kockelmann, J. Quinta da Fonseca and M. Preuss, Materials Science Forum, 702-703, 854-857, DOI:10.4028/www.scientific.net/MSF.702703.854 (2012).

125. “Effect of β grain growth on variant selection and texture memory effect during α → β → α phase transformation in Ti–6Al–4V”, G.C. Obasi, S. Birosca, J. Quinta da Fonseca, and M. Preuss, Acta Materialia, 60(3), 1048-1058.

DOI:doi:10.1016/j.actamat.2011.10.038 (2012)

132. “Inertia friction welding for aerospace applications”, M. Attallah and M. Preuss. In M.C. Chaturvedi (Ed.), Welding and Joining of Aerospace Materials, 25-108, Cambridge: Woodhead Publishing, 25-74, DOI: 10.1533/9780857095169.1.25 (2012).

133. “Linear Friction Welding in Aerospace Engineering”, I. Bhamji, A. C. Addison, P. L Threadgill and M. Preuss, In M.C. Chaturvedi (Ed.), Welding and Joining of Aerospace Materials, 384-415, Cambridge: Woodhead Publishing (2012).

134. “Characterization of MEA degradation for an open air cathode PEM fuel cell”, R. Silva, T. Hashimoto, G. E. Thompson, and C. Rangel, International Journal of Hydrogen Energy, DOI:10.1016/j.ijhydene.2011.12.110 (2012).

135. “Enrichment of alloying elements in aluminum: A scanning kelvin probe approach”, S. Garcia-Vergara, P. Skeldon, G. E. Thompson, G. Williams, and H. McMurray, Journal of The Electrochemical Society, 159(9), C428-C433.

DOI:10.1149/2.057209jes (2012).

126. “Influence of lead on the microstructure and corrosion behavior of melt-conditioned, twin-roll-cast AZ91D magnesium alloy”, S. Pawar, X. Zhou, G. E. Thompson, J .D. Robson, I. Bayandorian, G. Scamans and Z. Fan, Corrosion, 68 (6), 548-556, DOI: 10.5006/i0010-9312-68-6548 (2012).

136. “Contamination of stainless steel in an electrospray ionization source”, J. Doff, D. Douce, G. Jones, E. Koroleva, P. Skeldon, and G. E. Thompson, Applied Surface Science, DOI:10.1016/j.apsusc.2012.02.014 (2012).

127. “Effect of NH4HF2 on deposition of alkaline electroless Ni-P coatings as chromium-free pretreatments for magnesium”, A. A. Zuleta, E. Correa, G. E. Thompson, M. Curioni, T. Hashimoto, P. Skeldon and E. Koroleva, Corrosion Science, (55), 194-200, DOI:10.1016/j.corsci.2011.10.028 (2012).

137. “18O distributions in porous anodic alumina by plasma profiling time-of-flight mass spectrometry and nuclear reaction analysis”, A. Baron Wiechec, A. Tempez, P. Skeldon, P. Chapon, and G. E. Thompson, Surface and Interface Analysis, DOI:10.1002/sia.5032 (2012).

128. “Effects of density and electrolyte temperature on pore generation in anodic alumina formed in oxalic acid.”

F. Zhou, A. Baron-Wiecheć, S. J. Garcia-Vergara, M. Curioni, H. Habazaki, P. Skeldon and G. E. Thompson, Electrochimica Acta, (59), 186-195, DOI:10.1016/j.electacta.2011.10.052 (2012).

138. “Oxidation states of molybdenum in oxide films formed in sulphuric acid and sodium hydroxide”, I. Okonkwo, J. Doff, A. Baron-Wieche, G. Jones, E. Koroleva, P. Skeldon, and G. E. Thompson, Thin Solid Films, DOI:10.1016/j.tsf.2012.05.031 (2012).

129. “The impact of melt-conditioned twin roll casting on the downstream processing of an AZ31 magnesium alloy”, I. Bayandorian, Y. Huang, Z. Fan, S. Pawar, X. Zhou and G. E. Thompson, Metallurgical and Materials Transactions, A, 43, 1035-1047, DOI:10.1007/s11661-011-1006-3 (2012).

130. “Study of localized corrosion in AA2024-T3 aluminium alloy using electron tomography”, X. Zhou, C. Luo, T. Hashimoto, A. E. Hughes, G. E. Thompson, Corrosion Science, 58, 299-306, DOI:10.1016/j.corsci.2012.02.001 (2012).

131. “Analysis of thin and thick films”, Members of the EC EMPDA STREP Consortium, M.S. Lee (Ed.), Applied Handbook of Mass Spectrometry, Chapter 41, 943-959, DOI: 10.1002/9781118180730.ch41 (2012).

139. “Observations of intergranular corrosion in AA2024-T351: The influence of grain stored energy”, C. Luo, X. Zhou, G. E. Thompson, and A. Hughes, Corrosion Science, DOI:10.1016/j.corsci.2012.04.005 (2012).

140. “Ion migration and film morphologies in anodic alumina films formed in selenate electrolyte”, A. Baron-Wiecheć, O. Ekundayo, S. Garcia-Vergara, H. Habazaki, H. Liu, P. Skeldon, and G. E. Thompson, Journal of The Electrochemical Society, 159(7), C312-C317, DOI:10.1149/2.044207jes (2012).

141. “The effect of nickel on alloy microstructure and electrochemical behaviour of AA1050 aluminium alloy in acid and alkaline solutions”, F. Garcia-Garcia, P. Skeldon, G. E. Thompson, G. C. Smith, Electrochimica Acta, DOI:10.1016/j.electacta.2012.04.106 (2012).

142. “Plasma electrolytic oxidation and corrosion protection of Zircaloy-4”, Y. Cheng, E. Matykina, R. Arrabal, P. Skeldon, and G. E. Thompson, Surface and Coatings Technology, DOI:10.1016/j.surfcoat.2012.01.011 (2012).

143. “The influences of microdischarge types and silicate on the morphologies and phase compositions of plasma electrolytic oxidation coatings on Zircaloy-2”, Y. Cheng, F. Wu, E. Matykina, P. Skeldon, and G. E. Thompson, Corrosion Science, DOI:10.1016/j.corsci.2012.03.017 (2012).

144. “Porous anodic film formation on Al-Ti alloys in sulphuric acid”, V. Nettikaden, H. Liu, P. Skeldon, and G. E. Thompson, Corrosion Science, DOI:10.1016/j.corsci.2011.12.035 (2012).

145. “Porous anodic film growth on a Zr-W Alloy”, F. Muratore, A. Baron-Wieche, T. Hashimoto, A. Gholinia, H. Habazaki, P. Skeldon, and G. E. Thompson, Electrochemical and Solid-State Letters, 15(5), C8-C11. DOI:10.1149/2.005206esl (2012).

146. “Simulating the galvanic coupling between S-Al2CuMg phase particles and the matrix of 2024 aerospace aluminium alloy”, L. Lacroix, C. Blanc, N. Pébère, G. E. Thompson, B. Tribollet, and V. Vivier, Corrosion Science, 64, 213-221, DOI: 10.1016/j.corsci.2012.07.020 (2012).

147. “Growth and field crystallisation of anodic oxide films on Ta-Nb alloys”, S. Komiyama, E. Tsuji, Y. Aoki, H. Habazaki, M. Santamaria, F. Di Quarto, P. Skeldon and G. E. Thompson.

Journal of Solid State Electrochemistry, (16), 1595-1604.

DOI:10.1007/s10008-011-1565-7 (2012).

148. “Formation of self-organised nanoporous anodic films on type 304 stainless steel”, K. Kure, Y. Konno, E. Tsuji, H. Shoji, P. Skeldon, G. E. Thompson and H. Habazaki, Electrochemistry Communications, (21), 1-4, DOI:10.1016/j.elecom.2012.05.003 (2012).

149. “Inhomogeneous mesoscopic honeycomb optical media for enhanced cathode- and under-X-ray luminescence”, N. V. Gaponenko, M. V. Rudeko, V. S. Pustovarov, S. V. Zvonarev, A. I. Slesarev, I. S. Mochan, G. E. Thompson and E. A. Stepanova, Journal of Applied Physics, (111), DOI: 10.1063/1.4717740 (2012).

150. “The influence of rolling temperature on texture evolution and variant selection during α → β → α phase transformation in Ti–6Al–4V”, G.C. Obasi, S. Birosca, D.G. Leo Prakash, J. Quinta da Fonseca, M. Preuss. Acta Materialia, 60, 6013-6024, DOI: 10.1016/j.actamat.2012.07.025 (2012).

151. “Linear friction welding of aluminum to copper”, I. Bhamji, R.J. Moat, M. Preuss, P.L Threadgill, A.C. Addison and M.J. Peel, Science and Technology of Welding and Joining, 17 (4), 314-320, DOI: 10.1179/1362171812Y.0000000010 (2012).

152. “Linear friction welding of aluminum to magnesium”, I. Bhamji, M. Preuss, R. J. Moat, P. L Threadgill and A. C. Addison, Science and Technology of Welding and Joining, 17 (5), 368-374 DOI: 10.1016/j.mechmat.2014.12.001 (2012).

153. “Microstructural and residual stress development due to inertia friction welding in Ti-6246”, M. M. Attallah, M. Preuss, C. Boonchareon, A. Steuwer, J. E. Daniels, D. J. Hughes, C. Dungey and G. J. Baxter, Metallurgical and Materials Transactions A, 43 (9), 3149-3161, DOI: 10.1007/s11661-012-1116-6 (2012).

154. “In situ neutron diffraction study of texture evolution and variant selection during the α → β → α phase transformation in Ti–6Al–4V”, G. C. Obasi, R. J. Moat, D. G. Leo Prakash, W. Kockelmann, J. Quinta da Fonseca, M. Preuss, Acta Materialia, 60 (20), 7169-7182, DOI: 10.1016/j.actamat.2012.09.026 (2012).

155. “Observations of intergranular corrosion in AA2024-T3: The influence of grain stored energy”, C. Luo, X. Zhou, A. E. Hughes, G. E. Thompson, Corrosion Science, 61, 35-44, DOI: 10.1016/j.corsci.2012.04.005 (2012).

156. “Microstructural modelling for friction stir welding of high strength aluminum alloys”, J. D. Robson, and L. Campbell, Materials Science Forum, 706, 1008-1013, DOI: 10.4028/www.scientific.net/MSF.706-709.1008 (2012).

157. “Anodic film growth on Al-Li-Cu alloy AA2099-T8”, Y. Ma, X. Zhou, G. E Thompson, M. Curioni, P. Skeldon, X. Zhang, Z. Sun, C. Luo, Z. Tang and F. Lu, Electrochimica Acta, 80, 148-159, DOI: 10.1016/j.electacta.2012.06.126 (2012).

158. “Anodic growth of titanium oxide: Electrochemical behaviour and morphological evolution”, A. Mazzarolo, M. Curioni, A. Vicenzo, P. Skeldon and G. E. Thompson, Electrochimica Acta, 75, 288-295, DOI: 10.1016/j.electacta.2012.04.114 (2012).

159. “Formation of protective anodic oxides on aluminium by low voltage anodizing in sulphuric acid with cerium nitrate and tartaric acid additions”, M. Curioni, A. Zuleta, E. Correa, X. Pan, A. Baron-Wiecheć, P. Skeldon, J. Castao, F. Echeverra and G. E. Thompson, Transactions of the Institute of Metal Finishing, 90 (6), 290-297, DOI: 10.1179/0020296712Z.00000000059 (2012).

160. Effect of surface morphology changes of Ti-6Al-4V alloy modified by laser treatment on GDOES elemental depth profiles”, I. S. Molchan, S. Marimuthu, A.Mhich, Z. Liu, T. Hashimoto, G. E. Thompson, D. Whitehead, Z. B. Wang, P. Mativenga, L. Li, C. Grafton-Reed, I. H. Leaver, S. Cheetham, and S. Dilworth, Journal of Analytical Atomic Spectrometry, 28, 150-155, DOI: 10.1039/c2ja30186e (2012).

161. “Durability and corrosion of aluminium and its alloys: overview, property space, techniques and developments”, N. L. Suliman, X. Zhou, N. Birbilis, A. E. Hughes, J. M. C. Mol, S. J. Garcia, X. Zhou, and G. E. Thompson, Aluminium Alloys, New Trends in Fabrication and Applications (ed. Z. Ahmad), Chapter 2, INTECH Publications, ISBN 980-953-307-512-4 December (2012).

162. “Interfacial reaction during dissimilar joining of aluminum alloy to magnesium and titanium alloys”, A. Panteli, C. Q. Zhang, D. Baptiste, E. Cai, P. B. Prangnell, J. D. Robson, ICAA13: 13th International Conference on Aluminum Alloys, 761-770, DOI: 10.1002/9781118495292.ch112 (2012).

163. “Plastic strain mapping with sub-micron resolution using digital image correlation”, J. Quinta da Fonseca, F. Di Gioacchino, Experimental Mechanics, 53, 5, 743-754, DOI: 10.1007/s11340-012-9685-2 (2012).

164. “Formation of self-organized nanoporous anodic films on type 304 stainless steel”, Y. Konno, E. Tsuji, P. Skeldon, G. E. Thompson, H. Habazaki, Electrochemistry Communications, 21, 04, DOI: 10.1016/j.elecom.2012.05.003 (2012).

165. “Origin of streaks on anodized aluminium alloy extrusions”, Y. Ma, X. Zhou, G. E. Thompson, J-O. Nilsson, M. Gustavsson and A. Crispin, Transactions of the Institute of Metal Finishing, 91, 11-16, DOI: 10.1179/0020296712Z.00000000075 (2013).

166. “Advances in X-ray diffraction contrast tomography: flexibility in the setup geometry and application to multiphase materials”, P. Reischig, A. King, L. Nervo, N. Viganó, Y. Guilhem, W. J. Palenstijn, K. J. Batenburg, M. Preuss and W. Ludwig, Journal of Applied Crystallography, 46, 297-311, DOI: 10.1107/S0021889813002604 (2013).

167. “The effect of a paint bake treatment on joint performance in friction stir spot welding AA6111-T4 sheet using a pinless tool”, Y. C. Chen, S.F. Liu, D. Bakavos, and P. B. Prangnell, Materials Chemistry and Physics, 141 (2-3), 768-775, DOI: 10.1016/j.matchemphys.2013.05.073 (2013).

168. “In situ observation of texture and microstructure evolution during rolling and globularization of Ti–6Al–4V”, J. L. W. Warwick, N.G. Jones, I. Bantounas, M. Preuss, D. Dye, Acta Materialia, 61 (5), 1603-1615, DOI: 10.1016/j.actamat.2012.11.037 (2013).

171. “Reducing mechanical asymmetry in wrought magnesium alloys”, J. D. Robson, Materials Science Forum, 765, 580-584, DOI: 10.4028/www.scientific.net/MSF.765.580 (2013).

172. “Visualisation of carbon nanoparticle distributions in polymer composites using voltage contrast and energy contrast imaging in SEM”, Y. Liu, X. Zhou, J. Carr, C. Butler, S. Mills, J. O`Connor, E. McAlpine, T. Hashimoto, G. E. Thompson, G. Scamans, P. Howe, M. A. McCool and N. S. Malone, Polymer, 54, 330-340, DOI: 10.4028/www.scientific.net/MSF.765.580 (2013).

173. “New evidence on the role of catalase in Escherichia coli-mediated biocorrosion”, S .Baeza, N .Vejar, M. Gulppi, M. Azocar, F. Melo, A. Monsalve, J. Pinto, C. Vasquez, J. Pavez, J. H .Zagal, X. Zhou, G. E. Thompson and M. A. Páez, Corrosion Science, 67, 32-41, DOI: 10.1016/j.corsci.2012.09.047 (2013).

174. “The effectiveness of surface coatings on preventing interfacial reaction during ultrasonic welding of aluminum to magnesium”, A. Panteli, J. D. Robson, Y. C. Chen and P. B. Prangnell, Metallurgical and Materials Transactions A, DOI: 10.1007/s11661-013-1928-z (2013).

175. “Constituent particles and dispersoids in an Al-Mn-Fe-Si alloy studied in three-dimensions by serial sectioning”, J. D. Robson, J. da Fonseca, L. Dwyer, T. Hashimoto, G. E. Thompson and N. Kamp, Materials Science Forum, 765, 451-455, DOI: 10.4028/www.scientific.net/MSF.765.451 (2013).

176. “Anodizing of aluminum in sulfuric acid/boric acid mixed electrolyte”, L. Zhang, G. E. Thompson, M. Curioni and P. Skeldon, Journal of the Electrochemical Society, 160 (4), DOI: 10.1149/2.032306jes (2013).

177. “Plasma electrolytic oxidation of coupled light metals”, A. Baron-Wiecheć, M. Curioni, R. Arrabal, E. Matykina, P. Skeldon and G. E. Thompson, Transactions of the Institute of Metal Finishing, 91 (2), 107-112, DOI: 10.1179/0020296712Z.00000000083 (2013).

178. “Microstructural modification arising from alkaline etching and its effect on anodizing behavior of Al-Li-Cu alloy”, Y. Ma, X. Zhou, G. E. Thompson, X Zhang, C. Luo, M. Curioni and H. Liu, Journal of the Electrochemical Society, 160 (3), C111-C118, DOI: 10.1149/2.043303jes (2013).

169. “The effect of beta grain coarsening on variant selection and texture evolution in a near-beta Ti alloy”, G. C Obasi, J. Quinta da Fonseca, D. Rugg and M. Preuss, Materials Science and Engineering A, 576, 272-279, DOI: 10.1016/j.msea.2013.04.018 (2013).

179. “Interpretation of electrochemical noise generated by multiple electrodes”, M. Curioni, R.A. Cottis and G. E. Thompson, Corrosion, 69, 158, DOI: 10.5006/0701 (2013).

170. “Surface texture formed on AA2099 Al–Li–Cu alloy during alkaline etching”, Y. Ma, X. Zhou, G. E. Thompson, P. Skeldon. (2013). Corrosion Science, 66, 292-299, DOI: 10.1016/j.corsci.2012.09.032 (2013).

180. “Near-surface deformed layer and its evolution on AA3104 aluminium alloy”, K. Li, X. Zhou, G. E. Thompson, J. A. Hunter and Y. Yuan, Materials Science Forum, 765, 358-362, DOI: 10.4028/www.scientific.net/MSF.765.358 (2013).

181. “Novel environmentally-friendly coatings for aerospace alloys”, J. M. Harris, X. Zhou, G. E. Thompson, P. P. Scott, X. Zhang, Z. Shi and Z. Sun, Materials Science Forum, 765, 693-697, 10.4028/www.scientific.net/MSF.765.693 (2013).

182. “Analysis of molecular monolayers adsorbed on metal surfaces by glow discharge optical emission spectrometry”, I. S. Molchan, G. E. Thompson, P. Skeldon, A. Licciardello, N. Tuccitto and A. Tempez, Journal of Analytical Atomic Spectrometry, 28, 121-126, DOI: 10.1039/c2ja30247k (2013).

183. “Microstructure and microgalvanic corrosion of an extruded Mg-Gd-Y-Zr magnesium alloy”, J. P. Li, P. Wang, Y. C. Guo, G. E. Thompson, X. Zhou, S. Zhong and T. Hashimoto, Materials Science Forum, 765, 683-687, DOI: 10.4028/www.scientific.net/MSF.765.683 (2013).

184. “Galvanic corrosion between magnesium alloys and steel”, J. Janiec-Anwar, G. E. Thompson, X. Zhou, M. Curioni, M. Turski and T. Wilks, Materials Science Forum, 765, 648653, DOI: 10.4028/www.scientific.net/MSF.765.648 (2013).

185. “Reliability of the estimation of polarization resistance of corroding electrodes by electrochemical noise analysis: Effects of electrode asymmetry”, M. Curioni, P. Skeldon and G. E. Thompson, Electrochimica Acta, 105, 642-653, DOI: 10.1016/j.electacta.2013.04.119 (2013).

186. “3-D tomography by automated in-situ block face ultramicrotome imaging using an FEG-SEM to study complex corrosion protective paint coatings”, A. Trueman, S. Knight, J. M. Colwell, T. Hashimoto, J. Carr, P. Skeldon and G. E. Thompson, Corrosion Science, 75, 376-385, DOI: 10.1016/j.corsci.2013.06.021 (2013).

187. “Relating grain misorientation to the corrosion behaviour of low copper 7xxx aluminium alloys”, A. Cassell, G. E. Thompson, X. Zhou, T. Hashimoto and G. Scamans, Materials Science Forum, 765, 623-628, DOI: 10.4028/www.scientific.net/MSF.765.623 (2013).

188. “Microstructure, corrosion and wear performance of plasma electrolytic oxidation coatings formed on Ti-6Al-4V alloy in silicate-hexametaphosphate electrolyte”, Ying-liang Cheng, Xiang-Quan Wu, Zhi-gang Xue, E. Matykina, P. Skeldon, G. E. Thompson, Surface and Coatings Technology, 217, 129-139, DOI:10.1016/j.surfcoat.2012.12.003 (2013).

189. “Extending the life of light alloy components: microstructure, corrosion, inhibition and performance assessment”, M.Curioni, A. C. Balaskas, T.Hashiomoto, A. I. Egbeolu, and G.E.Thompson, Materials Science Forum, 765, 597, DOI: 10.4028/www.scientific.net/MSF.765.597 (2013).

190. “Three dimensional imaging of light metals using serial block face scanning electron microscopy (SBFSEM)”, T. Hashimoto, G. E. Thompson, M. Curioni, X. Zhou, P. Skeldon, Materials Science Forum, 765, 501, DOI: 10.4028/www.scientific.net/MSF.765.501 (2013).

191. “Tailoring of the solid state properties of Al-Nb mixed oxides: a photoelectrochemical study”, M. Santamaria, F. Di Franco, F. Di Quarto, P. Skeldon and G. E. Thompson, Journal of Physical Chemistry, 117, 4201-4210, DOI: 10.1021/jp312008m (2013).

192. “Tribological behaviour of electroless Ni-B coatings on magnesium and AZ91D alloy”, E. Correa, A. A. Zuleta, L.Guerra, M. Goméz Botero, J. G. Castaño, F. Echeverría, H. Liu, P. Skeldon and G. E. Thompson, Wear 305, 115-123, DOI: 10.1016/j.wear.2013.06.004 (2013).

193. “Formation of electroless Ni-B on bifluoride-activated magnesium and AZ91D alloy”, E. Correa, A. A. Zuleta, L. Guerra, J. G. Castaño, F. Echeverría, A. Baron-Wiechec, P. Skeldon and G. E. Thompson, Journal of the Electrochemical Society, 232, 784-794, DOI: 10.1149/2.012309jes (2013).

194. “Effect of fluoride ions on plasma electrolytic oxidation of AZ61 magnesium alloy”, A. Nemcová, P. Skeldon, G. E. Thompson, B. Pacal, Surface and Coatings Technology, 232, 827-838, DOI: 10.1016/j.surfcoat.2013.06.107 (2013).

195. “Coating development during electroless Ni-B plating on magnesium and AZ91D alloy”, E. Correa, A. A. Zuleta, L. Guerra, M. A. Gómez, J. G. Castaño, F. Echeverría, H. Lui, A. Baron-Wiechec, T. Hashimoto, P. Skeldon and G. E. Thompson, Surface and Coatings Technology, 232, 784-794, DOI: 10.1016/j.surfcoat.2013.06.100 (2013).

196. “Observation of self-assembled layers of alkyl phophonic acid on aluminium using low-voltage scanning electron microscopy”, H. Sato, T. Fujii, E. Tsuji, Y. Aoki, K. Shimizu, P. Skeldon, G. E. Thompson and H. Habazaki, Surface Interface Analysis, 45 (10), 1441-1445, DOI: 10.1002/sia.5217 (2013).

197. “An alternative to the use of a zero resistance ammeter for electrochemical noise measurement: Theoretical analysis, experimental validation and evaluation of electrodes asymmetry”, M. Curioni, A. C. Balaskas and G. E. Thompson, Corrosion Science, 77, 281-291, DOI: 10.1016/j.corsci.2013.08.014 (2013).

198. “Application of electrochemical noise analysis to corroding aluminium alloys”, M. Curioni, R. A. Cottis and G. E. Thompson, In press, Surface and Interface Analysis, 45 (10), 1564-1569, DOI: 10.1002/sia.5173 (2013).

199. “Revealing the 3D internal structures of aluminium and its alloys”, T. Hashimoto, X. L. Zhong, M. Curioni, X. Zhou, P. Skeldon, P. J. Withers and G. E. Thompson, Surface and Interface Analysis, 45 (10), 1536-1542, DOI: 10.1002/sia.5221 (2013).

200. “Optimization of anodizing cycles for enhanced performance”, M. Curioni, T. Gionfini, A. Vicenzo ,P. Skeldon, and G. E. Thompson, Surface and Interface Analysis, 45 (10), 1485-1489, DOI: 10.1002/sia.5222 (2013).

201. “Microstructure and corrosion behaviour of lean 7xxx aluminium alloy”, A. M. Cassell, G. E. Thompson, X. Zhou, A. Afseth, H. Dunlop and M-A. Kulas, Surface and Interface Analysis, 45 (10), 1604-1609, DOI: 10.1002/sia.5226 (2013).

202. “Investigation of dealloying by ultra-high resolution nanotomography”, T. Hashimoto, M. Curioni, X. Zhou, J. Mancuso, P. Skeldon and G. E. Thompson, Surface and Interface Analysis, 45 (10), 1548-1552, DOI: 10.1002/sia.5176 (2013).

203. “Comparison of the behaviours of chromate and sol–gel coatings on aluminium”, Y. Liu, Z. Feng, J. Walton, G. E. Thompson, P. Skeldon and X. Zhou, Surface and Interface Analysis, 45 (10), 1446-1451, DOI: 10.1002/sia.5206 (2013).

204. “Anodizing of AA6063 aluminium alloy profiles; generation of regions of dark appearance”, Y. Ma, X. Zhou, G. E. Thompson, J-O. Nilsson, M. Gustavsson and A. Crispin, Surface and Interface Analysis, 45 (10), 4179-1484, DOI: 10.1002/sia.5219 (2013).

205. “Grain stored energy and the propagation of IGC in AA2xxx aluminium alloys”, C. Luo, Y. Ma, T. Hashimoto, X. Zhou, G. E. Thompson, P. Skeldon and A. E. Hughes, Surface and Interface Analysis, 45 (10), 1543-1547, DOI: 10.1002/sia.5218 (2013).

206. “Influence of near-surface deformed layers on filiform corrosion of painted AA3104 aluminium alloy”, Y. Liu, T. Hashimoto, X. Zhou, G. E. Thompson, G. Scamans, W. M. Rainforth and J. A. Hunter, Surface and Interface Analysis, 45 (10), 1553-1557, DOI: 10.1002/sia.5232 (2013).

207. “Assessment of surface reactivity of aluminium AA1050 alloy”, M. Witkowska, G. E. Thompson, T. Hashimoto and E. Koroleva, Surface and Interface Analysis, 45 (10), 1585-1589, DOI: 10.1002/sia.5271 (2013).

208. “Surface treatment of aluminium automotive sheet: mythology and technology”, G. Scamans, P. R. Andrews, C. Butler, A. Hall, G. E. Thompson, Y. Ma and X. Zhou, Surface and Interface Analysis, 45 (10), 1430-1434, DOI: 10.1002/sia.5279 (2013).

211. “Comparison of the effect of individual and combined Zr and Mn additions on the fracture behaviour of Al-Cu-Li alloy AA2198 rolled sheet”, D. Tsivoulas, P. B. Prangnell, Metallurgical and Materials Transactions A, 45 (3), 1338-1351, DOI: 10.1007/s11661-013-2103-2 (2013).

212. “Effect of microstructure on the corrosion behaviour of extruded heat exchanger aluminium alloys”, A. Laferrere, N. Parson, X. Zhou and G. E. Thompson, Surface and Interface Analysis, 45, 1597-1603, DOI: 10.1002/sia.5282 (2013).

213. “Anodizing of aluminium in sulphuric acid/boric acid mixed electrolyte”, P. Skeldon, G. E. Thompson, M. Curioni and L. Zhang, Journal of the Electrochemical Society, 160, C179-C184, DOI: 10.1149/2.032306jes (2013).

214. “New findings on properties of plasma electrolytic coatings from study of an Al-Li alloy”, Y. Cheng, Z. Xue, Q. Wang, X. Q. Wu, P. Skeldon and G. E. Thompson, Electrochimica Acta, 107, 358-376, DOI: 10.1016/j.electacta.2013.06.022 (2013).

215. “Ion-ion interaction in two-dimensional nanoporous alumina filled with cubic YAlO3:Tb3+ matrix”, A. Podhorodecki, N.V. Gaponenko, G. Zatryb, I. S. Molchan, M. Motyka, J. Scrafinczuk, I. W. Golacki, L. S. Khoroshko, J. Misiewicz and G. E. Thompson, Journal of Physics D: Applied Physics, 46, 355302-355312, DOI: 10.1088/0022-3727/46/35/355302 (2013).

216. “Antibiofouling properties of sol-gel type polymers for aluminium alloys: biocorrosion protection against Pseudomonas Aeruginosa”, N. D. Vejar, M. I. Azocar, L. A. Tamayo, E. Gonzalez, J. Pavez, J. H. Zagal, X. Zhou, F. Santibanez, G. E. Thompson and M. A. Paez, International Journal of Electrochemical Science, 8, 12062-12077, ISSN: 1452-3981 (2013).

217. “Modelling competitive continuous and discontinuous precipitation”, J. D. Robson, Acta Materialia 61 (20), 7781-7790, DOI: 10.1016/j.actamat.2013.09.017 (2013).

218. “The effect of aluminium on deformation and twinning in Alpha Titanium: the 45° case”, A. Fitzner, D. G. Prakash, J. Quinta da Fonseca, M. Preuss, M. J. Thomas and S. Y. Zhang, Materials Science Forum 765, 549-553, DOI: 10.1016/j.actamat.2015.09.048 (2013).

209. “Tracer study of pore initiation in anodic alumina formed in phosphoric acid”, A. Baron-Wiecheć, M. G. Burke, T. Hashimoto, H. Liu, P. Skeldon, G. E. Thompson, H. Habazaki, J. Ganem, and I. C. Vickridge, Electrochimica Acta, 113, 302-312, DOI: 10.1016/j.electacta.2013.09.060 (2013).

219. “Measurement of strain and lattice rotation in the particle deformation zone”, L. C. L. Ko and J. Quinta da Fonseca, Materials Science Forum 753, 21-24, DOI: 10.4028/www.scientific.net/MSF.753.21 (2013).

210. “The effect of integrating rolling deformation with wire arc additive manufacture of Ti-6Al-4V - on grain size and texture refinement”, A. A. Antonysamy, F. Martina, P. A. Colegrove, S.W. Williams and P. B. Prangnell, Metallurgical and Materials Transactions A (2013).

220. “Evolution of near-surface deformed layers during hot rolling of AA3104 aluminium alloy”, Y. Liu, M. Frolish, W. Rainforth, X. Zhou, G. E. Thompson, G. Scamans, and J. Hunter, Surface and Interface Analysis, 180-184, DOI: 10.1002/sia.5232 (2013).

221. “Finite element modelling of the inertia friction welding of dissimilar high-strength steels”, M. Attallah, M. Preuss, P. H. Shipway, T. H. Hyde, S. Bray, C. J. Bennett, Metallurgical and Materials Transactions A, 44, 11, 5054 – 5064, DOI: 10.1007/s11661-013-1852-2 (2013).

222. “The effect of β phase on microstructure and texture evolution during thermomechanical processing of α + β titanium alloy”, D. G. Prakash, P. Honniball, D. Rugg, P. J. Withers, J. Quinta da Fonseca, M. Preuss, Acta Materialia, 61, 9, 3200 – 3213, DOI: 10.1016/j.actamat.2013.02.008 (2013).

223. “On the three-dimensional structure of wc grains in cemented carbides”, I. Brough, P. Hedströma, J. Odqvist, A. Borgenstama, J. Ågrena, A. Gholiniab, B. Winiarski, P. J. Withers, G. E. Thompson, K. Mingard, M. G. Gee, Acta Materialia, 61, 13, 4726-4733, DOI: 10.1016/j.actamat.2013.05.008 (2013).

224. “Three-dimensional observation and image-based modelling of thermal strains in polycrystalline alumina”, A. King, M. Mostafavi, P. Reischig, S. Rolland du Roscoat, W. Ludwig, J. Quinta da Fonseca, P. J. Withers, T. J. Marrow, D. Gonzalez, Acta Materialia, 61, 20, 7521 – 7533, DOI: 10.1016/j.actamat.2013.06.005 (2013).

225. “Residual stresses and tetragonal phase fraction characterisation of corrosion tested zircaloy-4 using energy dispersive synchrotron x-ray diffraction”, A. Ambard, S. Lyon, R. A. Cottis, M. Preuss, Journal of Nuclear Materials, 443, 03, 436-443, DOI: 10.1016/j.jnucmat.2013.07.053 (2013).

226. “Effect of build geometry on the β-grain structure and texture in additive manufacture of Ti-6Al-4V by selective electron beam melting”, P. B. Prangnell, A. A. Antonysamy, J. Meyer, Materials Characterization, 84, 153 – 168, DOI: 10.1016/j.matchar.2013.07.012 (2013).

227. “The effect of γ′ size and alloy chemistry on dynamic strain ageing in advanced polycrystalline nickel base superalloys”, J. Quinta Da Fonseca, B. Grant, E. M. Francis, M. Preuss, Materials Science and Engineering. A, Structural Materials: Properties, Microstructure and Processing, 54-61, DOI: 10.1016/j.msea.2013.02.027 (2013).

228. “Visualisation of conductive filler distributions in polymer composites using voltage and energy contrast imaging in SEM”, X. Zhou, J. Carr, C. Butler, S. L. Mills, J. O'Connor, E. McAlpine, T. Hashimoto, G. E. Thompson, G. M. Scamans, P. Howe, M. A. McCool, Polymer, 54, 1, 330-340, DOI: 10.1016/j.polymer.2012.11.018 (2013).

229. “Microstructural characterisation and corrosion behaviour of electroless Ni-W-P deposits of mixed nanocrystalline/ amorphous structures”, R. X. Guo, F. Veijo, G. E. Thompson, Z. Liu, H. Liu, Transactions of the IMF, 91, 2, 101-106, DOI: 10.1179/0020296712Z.00000000087 (2013).

230. “Evolution of near-surface deformed layers on AA3104 aluminium alloy”, X. Zhou, G. E. Thompson, J. A. Hunter, Y. Y. Die, L. Kai, Materials Science Forum, 765, 358-362, DOI: 10.4028/www.scientific.net/MSF.765.358 (2013).

231. “Mechanical and microstructural characterization of percussive arc welded hyper-pins for titanium to composite metal joining”, D. Strong, C. Octav, J. Meyer, P. B. Prangnell, Materials Science Forum, 765, 771-775, DOI: 10.4028/www.scientific.net/MSF.765.771 (2013).

232. “Antibiofouling properties of sol-gel type polymers for aluminium alloys: bio corrosion protection against pseudomonas aeruginosa”, M. Azocar, L. Tamayo, E. Gonzalez, J. Pavez, M. Gulppi, X. Zhou, G. E. Thompson, Vejar, N. D, International Journal of the Electrochemical Society, 8, 12062-12077, 10.1016/j.msea.2013.05.021 (2013).

233. “Crystallisation and performance characteristics of hightemperature annealed electroless Ni-W-P coatings”, Y. Liu, H. L. Yao, G. E. Thompson, Z. Liu, Crystal Research and Technology, 49, 03, 178-189, DOI: 10.1002/crat.201300375 (2013).

234. “Microstructural characterization and mechanical properties of high power ultrasonic spot welded aluminum alloy AA6111–TiAl6V4 dissimilar joints”, C. Q. Zhang, J. D. Robson, O. Ciuca and P. B. Prangnell, Materials Characterization, 97, 83-91, DOI: 10.1016/j.matchar.2014.09.001 (2014).

235. “Influence of orientation on twin nucleation and growth at low strains in a magnesium alloy”, M. R. Barnett, A. Ghaderi, J. Quinta da Fonseca and J. D. Robson, Acta Materialia, 80, 380-391, DOI: 10.1016/j.actamat.2014.07.013 (2014).

236. “Anisotropy and asymmetry of yield in magnesium alloys at room temperature”, J. D. Robson, Metallurgical and Materials Transactions A 45 (11), 5226-5235, DOI: 10.1007/s11661-014-2453-4 (2014).

237. “Evaluating the effect of yttrium as a solute strengthener in magnesium using in situ neutron diffraction”, N. Stanford, R. Cottam, B. Davis and J. D. Robson, Acta Materialia 78, 1-13, DOI: 10.1016/j.actamat.2014.06.023 (2014).

238. “Controlling interfacial reaction during dissimilar metal welding of aluminium alloys”, L. Wang, Y. Wang, C. Q. Zhang, L. Xu, J. D. Robson and P. B. Prangnell, Materials Science Forum 794, 416-421, DOI: 10.4028/www.scientific.net/MSF.794-796.416 (2014).

239. “The effect of hot deformation on dispersoid evolution in a model 3xxx alloy”, J. D. Robson, T. Hill, N. Kamp, Materials Science Forum 794, 697-703, DOI: 10.4028/www.scientific.net/MSF.794-796.697 (2014).

240. “Texture evolution during wire drawing of Mg-RE alloy”, M. Chatterton, J. D. Robson and D. Henry, Magnesium Technology, 251-256, DOI: 10.1002/9781118888179.ch48 (2014).

241. “A new model for discontinuous and continuous precipitation in AZ91 magnesium alloy”, J. D. Robson, Materials Science Forum 461-466, DOI: 10.4028/www.scientific.net/MSF.783-786.461 (2014).

242. “Effect of rare-earth additions on the texture of wrought magnesium alloys: the role of grain boundary segregation”, J. D. Robson, Metallurgical and Materials Transactions A 45 (8), 3205-3212, DOI: 10.1007/s11661-013-1950-1 (2014).

243. “Contribution of twinning to low strain deformation in a Mg alloy”, M. R. Barnett, A. Ghaderi and J. D. Robson, Metallurgical and Materials Transactions A 45 (8), 3213-3221, DOI: 10.1007/s11661-013-2029-8 (2014).

244. “Electrochemical characteristics of a carbon fibre composite and the associated galvanic effects with aluminium alloys”, Z. Liu, M. Curioni, P. Jamshidi, A. Walker, P. B. Prangnell, G. E. Thompson and P. Skeldon, Applied Surface Science, 314, 233-244, DOI: 10.1016/j.apsusc.2014.06.072 (2014).

245. “The effect of Mn and Zr dispersoid-forming additions on recrystallization resistance in Al–Cu–Li AA2198 sheet”, D. Tsivoulas and P. B. Prangnell, Acta Materialia 77, 1-6, DOI: 10.1016/j.actamat.2014.05.028 (2014).

246. “Dissimilar metal laser spot joining of steel to aluminium in conduction mode”, G. Pardal, S. Meco, S. Ganguly, S. Williams and P. B Prangnell, International Journal of Advanced Manufacturing Technology, 73, 365-373, DOI: 10.1007/s00170-014-5802-y (2014).

247. "Heterogeneous nucleation of α-Al grain on primary α-AlFeMnSi intermetallic investigated using 3D SEM ultramicrotomy and HRTEM", W. Yang, S. Ji, X. Zhou, G. E. Thompson I. Stone, G. Scamans and Z. Fan, Metallurgical and Materials Transactions A 45, 3971-3980, DOI: 10.1007/s11661-014-2346-6 (2014).

248. “The impact of machining on the corrosion behaviour of AA7150-T651 aluminium alloy”, B. Liu and X. Zhou, Materials Science Forum, 794-796, 217-222, DOI: 10.4028/www.scientific.net/MSF.794-796.217 (2014).

249. “The behaviour of magnesium during free corrosion and potentiodynamic polarization investigated by real-time hydrogen measurement and optical imaging”, M. Curioni, Electrochimica Acta, 120, 284, DOI: 10.1016/j.electacta.2013.12.109 (2014).

250. “Evaluation of inhibitor performance by electrochemical methods: comparative study of nitrate salts”, A. C. Balaskas, M. Curioni and G. E. Thompson, Journal of Electrochemical Society, 161, C389, DOI: 10.1149/2.0711409jes (2014).

251. “Development of cerium-rich layers on anodic films formed on high-purity aluminium and AA7075 T6 alloy”, I. Gordovskaya, T. Hashimoto, J. Walton, M. Curioni, G. E. Thompson and P. Skeldon, Journal of the Electrochemical Society, 161, 14, C601, DOI: 10.1149/2.0091501jes (2014).

252. “Influence of plasma electrolytic oxidation on fatigue performance of AZ61 magnesium alloy”, A. Nemcova, P. Skeldon, G. E. Thompson, S. Morse and B. Pacal, Corrosion Science, 82, 58-66, DOI: 10.1016/j.corsci.2013.12.019 (2014).

253. “Effect of chloride ions in plasma electrolytic oxidation of titanium”, P. Skeldon, G. E. Thompson, T. Hashimoto and S. Aliasghari, ECS Electrochemistry Letters, 3, C17-C20, DOI: 10.1149/2.002405eel (2014).

254. “Morphological control of anodic crystalline TiO2 nanochannel films for use in size-selective photocatalytic decomposition of organic compounds”, E. Tsuji, Y. Taguchi, Y. Aoki, T. Hashimoto, P. Skeldon, G. E. Thompson and H. Habazaki, Applied Surface Science, 301, 500-507, DOI: 10.1016/j.apsusc.2014.02.113 (2014) 255. “Correlative tomography”, T. L. Burnett, S. A. McDonald, A. Gholinia, R. Geurts, M. Janus, T. Slater, S. Haigh, C. Ornek, F. Almuaili, D. Engelberg, G. E. Thompson and P. J. Withers, Nature Scientific Reports 4, Article Number 4711, DOI: 10.1038/srep04711 (2014).

256. “Quantitative 3D in-situ study of the opening of a short fatigue crack in a magnesium alloy”, M. Mostafavi, T. Hashimoto, G. E. Thompson and T. J. Marrow, International Journal of Fatigue,66, 183-193, DOI: 10.1016/j.ijfatigue.2014.04.003 (2014).

257. “Revelation of intertwining organic and inorganic fractal structures in polymer coatings”, A. E. Hughes, A. Trinchi, F. F. Chen, Y. S. Yang, I. S. Cole, S. Sellaiyan, J. Carr, P. D. Lee, G. E. Thompson and T. Q. Xiao, Advanced Materials, 26, 4504-4508, DOI: 10.1002/adma.201400561 (2014).

258. “Formation of barrier-type anodic films on ZE41 alloy in a fluoride/glycerol electrolyte”, J. M. Hernández-López, A. Nemcova, X. L. Zhong, H. Liu, M. A. Arenas-Vara, S. Haigh, G. Burke, P. Skeldon and G. E. Thompson, Electrochimica Acta, 130, 124-131, DOI: 10.1016/j.electacta.2014.05.147 (2014).

259. “Discoloration of anodized AA6063 aluminium alloy”, Y. Ma, X. Zhou, J. Wang, G. E. Thompson, W. Huang, J. O Nilsson, M. Gustavsson and A. Crispin, Journal of the Electrochemical Society, 161, C312-C320, DOI: 10.1149/2.065406jes (2014).

260. “Efficient growth of anodic films on magnesium in organic electrolytes containing fluoride and water”, H. Habazaki, F. Kataoka, E.i Tsuji, Y. Aoki, S. Nagata, P. Skeldon and G. E. Thompson, Electrochemistry Communications, 46, 30-32, DOI: 10.1016/j.elecom.2014.06.011 (2014).

261. “Characterization of anodic oxide growth on commercially pure titanium in NaTESI electrolyte”, Z. Liu, H. Liu, X. Zhong, T. Hashimoto, G. E. Thompson and P. Skeldon, Surface and Coatings Technology, 258, 1025-1031, DOI: 10.1016/j.porgcoat.2014.07.001 (2014).

262. “CO2 capture efficiency, corrosion properties and ecotoxicity evaluation of amine solutions involving newly synthesized ionic liquids”, X. L. Papatryfon, N. S. Heliopoulos, I. S. Molchan, L. F. Zubeir, N. D. Bezemer, M. K. Arfanis, A. G. Kontos, V. Likodimos, B. Iliev, G. Em. Romanos, P. Falaras, K. Stamatakis, K. G. Beltsios, M. C. Kroon, G. E. Thompson, J. Klöckner and T. J. S. Schubert, Industrial & Engineering Chemistry Research, 30, 12083-12102, DOI: 10.1021/ie501897d (2014).

263. “Plasma electrolytic oxidation of titanium in phosphate/silicate electrolyte and tribological performance of the coatings”, S. Aliasghari, P. Skeldon and G. E. Thompson, Applied Surface Science, 316, 463-476, DOI: 10.1021/ie501897d (2014).

264. “Anodic oxide film growth on thin magnetron sputterdeposited titanium layer”, Z. Liu, H. Liu, T. Hashimoto, G. E. Thompson and P. Skeldon, Materials Characterisation, 98, 102-106, DOI 10.1016/j.matchar.2014.10.012 (2014).

265. “Staining and embedding of human chromosomes for 3D serial block face scanning electron microscopy”, M. Yusuf, B. Chen, T. Hashimoto, A. Estardarte G. E. Thompson and I. K. Robinson, Biotechniques International Journal of Life Science Methods, 57, 302-307, DOI: 10.2144/000114236 (2014).

266. “3D characterization of trans- and inter-lamellar fatigue crack in (α + β) Ti alloy”, L. Babout, Ł. Jopek and M. Preuss, Materials Characterization, 98 (0), 130-139, DOI: 10.1016/j.matchar.2014.10.017 (2014).

267. “A method for accurate texture determination of thin oxide films by glancing-angle laboratory X-ray diffraction”, A. Garner, M. Preuss, P. Frankel, Journal of Applied Crystallography, 47 (2), 575-583, DOI: 10.1107/S1600576714000569 (2014).

268. “In situ synchrotron studies of reversible and irreversible nonelastic strain in a two-phase TiAl alloy”, F. A. Garcia-Pastor, H. Jiang, D. Hu, X. Wu, P. J. Withers and M. Preuss, Metallurgical and Materials Transactions, 45 (2), 607-618, DOI: 10.1007/s11661-013-2024-0 (2014).

269. “Iron redistribution in a zirconium alloy after neutron and proton irradiation studied by energy-dispersive X-ray spectroscopy (EDX) using an aberration-corrected (scanning) transmission electron microscope”, E. M. Francis, A. Harte, P. Frankel, S. J. Haigh, D. Jädernäs, J. Romero, L. Hallstadius and M. Preuss, Journal of Nuclear Materials, 454 (1-3), 387-397, DOI: 10.1016/j.jnucmat.2014.08.034 (2014).

270. “Influence of orientation on twin nucleation and growth at low strains in a magnesium alloy”, M.R Barnett, A. Ghaderi, JQ da Fonseca and J. D. Robson, Acta Materialia, 80, 380-391, DOI: 10.1016/j.actamat.2014.07.013 (2014).

271. “Peak broadening anisotropy in deformed face-centred cubic and hexagonal close-packed alloys”, T. H Simm, P. J Withers and J. Quinta da Fonseca, Applied Crystallography, 47 (5), DOI: 10.1107/S1600576714015751 (2014).

272. “Comparison between a near-field and a far-field indexing approach for characterization of a polycrystalline sample volume containing more than 1500 grains”, L. Nervo, A. King, J. P Wright, W. Ludwig, P. Reischig and J. Quinta da Fonseca, Journal of Applied Crystallography, 47 (4), 1402-1416, DOI: 10.1107/S160057671401406X (2014).

273. “Modeling Twin Clustering and Strain Localization in Hexagonal Close-Packed Metals”, G. Timár, and J. Quinta da Fonseca.

Metallurgical and Materials Transactions, A, 1-8, DOI: 10.1007/s11661-014-2547-z (2014).

274. “A systematic study of antibacterial silver nanoparticles: efficiency, enhanced permeability, and cytotoxic effects”, H. Liu, H. L. Yao, Y. Liu, G. E. Thompson, Z. Liu, Journal of Nanoparticle Research, 49, 02, 178-189, DOI: 10.1007/s11051-014-2465-4 (2014).

275. “The effect of cooling rate from solution on the lattice misfit during isothermal aging of a Ni-base superalloy”, L. Tamayo, N. Vejar, G. Gomez, X. Zhou, G. E. Thompson, E. Cerda, Journal of Nanoparticle Research, 45, 5, 2436-2444, DOI: 10.1007/s11661-014-2197-1 (2014).

276. “The effect of annealing on the corrosion behaviour of 444 stainless steel for drinking water applications”, C. Bitondo, M. Curioni, A. Bossio, F. Bellucci, Corrosion Science, 87, 6-10, DOI: 10.1016/j.corsci.2014.06.025 (2014).

277. “Wear-resistant coatings formed on Zircaloy-2 by plasma electrolytic oxidation in sodium aluminate electrolytes”, J. Cao, Z. Peng, Q. Wang, E. Matykin, P. Skeldon, G. E. Thompson, Y. Cheng, Electrochimica Acta, 116, 453-466, DOI: 10.1016/j.electacta.2013.11.079 (2014).

278. “A quantitative three-dimensional in situ study of a short fatigue crack in a magnesium alloy”, M. Mostafavi, T. Hashimoto, G. E. Thompson, T. J. Marrow, International Journal of Fatigue, 66, 183-193, DOI: 10.1016/j.ijfatigue.2014.04.003 (2014).

279. “Modelling the effect of elastic and plastic anisotropies on stresses at grain boundaries”, I. Simonovski, P. J. Withers, J. Quinta Da Fonseca, D. Gonzalez, International Journal of Plasticity, 61, 49-63, DOI: 10.1016/j.ijplas.2014.03.012 (2014).

280. “Release of silver and copper nanoparticles from polyethylene nanocomposites and their penetration into Listeria monocytogenes”, P. A. Zapata, N. J. Vejar, M. A. Gulppi, X. Zhou, G. E. Thompson, F. M. Rabagliati, L. A. Tamayo, Materials Science and Engineering: C, 40, 24-31, DOI: 10.1016/j.msec.2014.03.037 (2014).

281. “Three-dimensional analysis of the spatial distribution of iron oxide particles in a decorative coating by electron microscopic imaging”, T. Hashimoto , F. Vergeer , A. Burgess, G. E. Thompson, I. Robinson, Progress in Organic Coatings, 77, 6, 1069-1072, DOI: 10.1016/j.porgcoat.2014.03.005 (2014).

282. “The application of multiscale quasi 4D CT to the study of SrCrO4 distributions and the development of porous networks in epoxy-based primer coatings”, A. Trinchi, F. F. Chen, Y. S. Yang, I. S. Cole, J. Carr, P. D. Lee, G. E. Thompson, A. E. Hughes, Progress in Organic Coatings, 77, 11, |19461956, DOI: 10.1016/j.porgcoat.2014.07.001 (2014).

283. “Corrosion behaviour of mild steel in 1-alkyl-3methylimidazolium tricyanomethanide ionic liquids for CO2 capture applications”, G. E. Thompson, P. Skeldon, R. Lindsay, L. Vlassis, G. Romanos, I. S. Molchan, RSC Advances, 4, 11, DOI: 10.1039/c3ra45872e (2014).

284. “Characterization of abnormal grain coarsening in Alloy 718”, M. Preuss, J. Quinta Da Fonseca, T. Witulski, T. Gregor, MATEC Web of Conferences, 14, DOI: 10.1051/matecconf/20141407004 (2014).

285. “Laser nanocrystallisation and corrosion behaviour of electroless Ni-W-P coating with high phosphorus content”, G. E. Thompson, H. L. Yao, F. Viejo, G. Harrison, Z. Liu, H. Liu, Transactions of the IMF, 92, 4, 212-217, DOI: 10.1179/0020296714Z.000000000171 (2014).

286. “Influence of galvanized coatings on abrasion circle friction stir spot welding aluminium to steel for automotive applications”, P. B. Prangnell, L. S. Fang, Y. C. Chen, Materials Science Forum, 783-786, 1741-1746, DOI: 10.4028/www.scientific.net/MSF.783-786.1741 (2014).

287. “Texture formation in flow formed ferritic steel tubes and the influence of the process parameters”, G. Timar, M. Tuffs, J. Quinta Da Fonseca, M. Preuss, D. Tsivoulas, Materials Science Forum, 783-786, 2602-2607, DOI: 10.4028/www.scientific.net/MSF.783-786.2602 (2014).

288. “Systematic evaluation of the advantages of static shoulder fsw for joining aluminium”, H. Wu, Y. C. Chen, D. Strong, P. B. Prangnell, Materials Science Forum, 794-796, 407-412, DOI: 10.4028/www.scientific.net/MSF.794-796.407 (2014).

289. “Heterogeneous Zr solute segregation and Al 3 Zr dispersoid distributions in Al–Cu–Li alloys”, D. Tsivoulas and J. D. Robson, Acta Materialia, 93, 73-86, DOI: 10.1016/j.actamat.2015.03.057 (2015)

290. “Characterisation and modelling of defect formation in direct-chill cast AZ80 alloy” D. Mackie, J. D. Robson, P. J. Withers and M. Turski, Materials Characterization, 104, 116-123, DOI: 10.1016/j.matchar.2015.03.033 (2015).

291. “Coating design for controlling b phase imc formation in dissimilar Al-Mg-metal welding”, Y. Wang, L. Wang, J. D. Robson, B. M. Al-Zubaidy and P. B. Prangnell, Friction Stir Welding and Processing VIII, 171, DOI: 10.1002/9781119093343.ch19 (2015).

292. “Critical assessment 9: wrought magnesium alloys”, J. D. Robson, Materials Science and Technology, 31 (3), 257-264, DOI: 10.1179/1743284714Y.0000000683 (2015).

293. “Effect of traces of silicon on the formation of Fe-rich particles in pure magnesium and the corrosion susceptibility of magnesium”, L. Yang, X. Zhou, S. M Liang, R. Schmid-Fetzer, Z. Fan and G. Scamans, Journal of Alloys and Compounds, 619, 396-400, DOI: 10.1016/j.jallcom.2014.09.040 (2015).

294. “Stationary shoulder FSW for joining high strength aluminium alloys”, H. Wu, Y-C, Chen, D. Strong and P. B. Prangnell, Journal of Materials Processing Technology, 221, 187-196, DOI: 10.1016/j.jmatprotec.2015.02.015 (2015).

295. “Modelling of the thermal field in dissimilar alloy ultrasonic welding”, P. Jedrasiak, H. R. Shercliff, Y. C. Chen, L. Wang, P. B. Prangnell and J. D. Robson, Journal of Materials Engineering and Performance, 24, 799-807, DOI: 10.1007/s11665-014-1342-8 (2015).

296. “Delamination of near-surface layer on cold rolled AlFeSi alloy during sheet forming”, J. Wang, X. Zhou, G. E. Thompson, J. A. Hunter and Y. Yuan, Materials Characterization, 99, 109-117, DOI: 10.1016/j.matchar.2014.11.011 (2015).

297. “Near-surface microstructure on twin-roll cast 8906 aluminium alloy”, J. Wang, X. Zhou, G. E. Thompson, J. A. Hunter and Y. Yuan, Metallurgical and Materials Transactions A, 46, 2688-2695, DOI: 10.1007/s11661-015-2877-5 (2015).

298. “Corrosion behaviour of pure magnesium with low impurity content but high corrosion rate in 3.5 wt% NaCl solution”, L. Yang, X. Zhou, M. Curioni, S. Pawar, H. Liu, Z. Fan and G. E. Thompson, Journal of Electrochemical Society, 162, C362-368, DOI: 10.1149/2.1041507jes (2015).

299. “Study of the metallurgy of dissimilar Ti-6Al-4V – Stainless Steel linear fiction welded joints”, F. Impero, F. Scherillo, A. Astarita, K. A. Beamish, M. Curioni, A. Squillace and X. Zhou, Key Engineering Materials, 651-653, 1427-1432, DOI: 10.1002/maco.201307476 (2015).

300. “Investigation of the microstructure and the influence of iron on the formation of Al8Mn5 particles in twin roll cast AZ31 magnesium alloy”, S. Pawar, X. Zhou, G. E. Thompson and T. Hashimoto, Journal of Alloys and Compounds, 628, 195-198, DOI: 10.1016/j.jallcom.2014.12.028 (2015).

310. “Scanning transmission electron microscopy for morphology analysis of anodic oxide film on titanium”, Z. Liu, T. Hashimoto, I-L. Tsai, G. E. Thompson, P. Skeldon and H. Liu, Vacuum, 115, 19-22, DOI: 10.1016/j.vacuum.2015.01.027 (2015).

301. “Effect of near-ambient temperature changes on the galvanic corrosion of an AA2024-T3 and mild steel couple”, U. Donatus, G. E. Thompson and X. Zhou, Journal of Electrochemical Society, 161, C42-C46, DOI: 10.1149/2.0551501jes (2015).

311. “Formation of grooved and porous coatings on titanium by plasma electrolytic oxidation in H2SO4 / H3PO4 electrolytes and effects of coating morphology on adhesive bonding”, O. A. Galvis, D. Quintero, J. G. Castano, H. Liu, G. E. Thompson, P. Skeldon and F. Echeverria, Surface and Coatings Technology, 269, 238-249, DOI: 10.1016/j.surfcoat.2015.02.036 (2015).

302. “Grain refining mechanism in the Al/Al-Ti-B system”, Z. Fan, W. Yang, Y. Zhang, T. Qin, X. Zhou, G. E. Thompson, T. Pennycook and T. Hashimoto, Acta Materialia, 84, 292-304, DOI: 10.1016/j.actamat.2014.10.055 (2015).

303. “Corrosion behaviour of stainless steel-titanium alloy linear friction welding joints: galvanic coupling”, M. Curioni, A. Astarita, A. Squillace, X. Zhou, F. Bellucci, G. E. Thompson and K. Beamish, Materials and Corrosion, 66 (2), 111-117, DOI: 10.1002/maco.201307476 (2015).

304. “Efficiency of anodizing of an Al-Cu alloy in sulphuric acid under low potentials”, B. Mingo, A. Nemcova, D. Hamad, R. Arrabal, E. Matykina, M. Curioni, P. Skeldon and G. E. Thompson, Transaction of the Institute of Metal Finishing, 93 (2), 18-23, DOI: 10.1179/0020296714Z.000000000217 (2015).

305. “Correlation between electrochemical impedance spectroscopy measurements and corrosion rate of magnesium investigated by real-time hydrogen measurement and optical imaging”, M. Curioni, F. Scenini, T. Monetta and F. Bellucci, Electrochimica Acta, 166 (1), 372-384, DOI: 10.1016/j.electacta.2015.03.050 (2015).

306. “Effect of magnesium and titanium on the cathodic behaviour of aluminium in nitric acid”, F. J. Garcia-Garcia, T. Y. Chiu, P. Skeldon and G. E. Thompson, Surface and Interface Analysis, 47, 30-36, DOI: 10.1002/sia.5640 (2015).

307. “Formation of porous anodic oxide film on titanium in phosphoric acid electrolyte”, Z. Liu and G. E. Thompson, Journal of Materials Engineering and Performance, 24, 59-66, DOI: 10.1007/s11665-014-1262-7 (2015).

312. “Role of oxide stress in the initial growth of self-organized porous aluminum oxide”, Ö. Çapraz, P. Shrotriya, P. Skeldon, G. E. Thompson and K. R. Hebert, Electrochimica Acta, 167, 404-411, DOI: 10.1016/j.electacta.2015.03.017 (2015).

313. “A comparison of plasma electrolytic oxidation of Ti-6Al-4V and Zircaloy 2 alloys in a silicate-hexametaphosphate electrolyte”, Y. Cheng, Z. Peng, X. Wu, Z. Cao, P. Skeldon and G. E. Thompson, Electrochimica Acta, 165, 303-313, DOI: 10.1016/j.electacta.2015.03.020 (2015).

314. “Study of the effect of cadmium on the bimetallic corrosion behaviour of AA2024T3 and mild steel couple”, U. Donatus, G. E.Thompson and Z. Liu, Journal of Materials Engineering and Performance, 24, 1897-1905, DOI: 10.1007/s11665-015-1472-7 (2015).

315. “Chemical etching behaviour of titanium in methanol-ethanol electrolyte”, Z. Liu, I-L. Tsai, G. E. Thompson, H. Liu and U.Donatus, Materials Chemistry and Physics, 160, 329, DOI: 10.1016/j.matchemphys.2015.04.045 (2015).

316. “Growth of barrier-type anodic films on magnesium in ethylene glycol electrolytes containing fluoride and water”, H. Habazaki, F. Kataoka, K. Shazad, E. Tsuji, Y. Aoki, S. Nagata, P. Skeldon and G. E. Thompson, Electrochimica Acta, 179, 402 - 410, DOI: 10.1016/j.electacta.2015.02.168 (2015).

308. “High growth rate, wear-resistant coatings on an Al-Cu-Li alloy by plasma electrolytic oxidation in concentrated aluminate electrolytes”, J. Cao, Y. Cheng, Z. Peng, M. Mao, P. Skeldon and G. E Thompson, Surface and Coatings Technology, 269, 74-82, DOI: 10.1016/j.surfcoat.2014.12.078 (2015).

317. “The corrosion protection of AA2024-T3 aluminium alloy by leaching of lithium-containing salts from organic coatings”, P. Visser, Y. Liu, X. Zhou, T. Hashimoto, G. E. Thompson, S. B. Lyon, L. G. J. Van der Ven, A. J. M. C. Mol and H. A. Terryn, Faraday Discussions (Royal Society of Chemistry), 180, 511 (2015).

309. “Factors controlling stress generation during the initial growth of porous anodic aluminium oxide”, O. Capraz, P. Shrotriya, P. Skeldon, G. E. Thompson and K. R. Hebert, Electrochimica Acta,159, 16-22, DOI: 10.1016/j.electacta.2015.01.183 (2015).

318. “Evolution of a laser shock peened residual stress field locally with foreign object damage and subsequent fatigue crack growth”, S. Zabeen, M. Preuss and P. J. Withers, Acta Materialia, 83, 216-226, DOI: 10.1039/C4FD00237G (2015).

319. “Grain breakup during elevated temperature deformation of an HCP metal”, P. Honniball, M. Preuss, D. Rugg, and J. Quinta Da Fonseca, Metallurgical and Materials Transactions A, 46 (5), 2143-2156, DOI: 10.1016/j.actamat.2014.09.032 (2015).

320. “Residual stresses due to foreign object damage in laser-shock peened aerofoils: simulation and measurement”, B. Lin, S. Zabeen, J. Tong, M. Preuss and P. J. Withers, Mechanics of Materials, 67 (12), 2908-2913, DOI: 10.1007/s11837-0151627-x (2015).

329. “Modelling of intermetallic compounds growth between dissimilar metals”, P. B. Prangnell, L. Wang, J. D. Robson, Metallurgical and Materials Transactions A, 4106-4114, DOI: 10.1007/s11661-015-3037-7 (2015).

330. “Effect of low temperature sensitization on the susceptibility to intergranular corrosion in AA5083 aluminium alloy”, X. Zhou, W. Wei, S. Gonzalez, T. Hashimoto, P. B. R. Rajan, G. E. Thompson, Materials and Corrosion, DOI: 10.1002/maco.201508589 (2015).

321. "Structure of the copper-enriched layer introduced by anodic oxidation of copper-containing aluminum alloy” T. Hashimoto, X. Zhou, G. E. Thompson and P. Skeldon, Electrochimica Acta, 179, 394-401, DOI: 10.1016/j.electacta.2015.01.133 (2015).

331. “Correlation between localized plastic deformation and localized corrosion in AA2099 aluminum-lithium alloy”, Y. Ma, X. Meng, Y. Liao, L. Chai, Y. Yi, X. Zhang, X. Zhou, DOI: 10.1002/sia.5817 (2015).

322. "FIB-SEM investigation on corrosion propagation of Al-Li alloy in sodium chloride solution” Corrosion Engineering, Science and Technology, C. Luo, M. Gao, Z. Sun, X. Zhang, Z. Tang and X. Zhou, 50 (5), 390 - 396, DOI: 10.1179/1743278214Y.0000000235 (2015).

332. “The influence of prolonged natural aging on the subsequent artificial aging response of the AA6111 automotive alloy”, A. Abouarkoub, X. Zhou, T. Hashimoto, G. Scamans, G. E. Thompson, Metallurgical and Materials Transactions A, 46 (9), 4380-4393, DOI: 10.1007/s11661-015-3043-9 (2015).

323. “Effect of current density and behaviour of second phases in anodizing of a Mg-Zn-RE alloy in a fluoride/glycerol/water electrolyte”, A. Němcová, I. Kuběna, M. Šmíd, H. Habazaki, P. Skeldon and G. E. Thompson, Journal of Solid State Electrochemistry, 179, 394-401, DOI: 10.1007/s10008-015-2864-1 (2015).

333. “In-service sensitization of a microstructurally heterogeneous AA5083 alloy”, G. E. Thompson, W. Wei, S. Gonzalez, T. Hashimoto, X. Zhou, Materials and Corrosion, DOI: 10.1002/maco.201508507 (2015).

324. “XCT analysis of the influence of process parameters on defect population in Ti-6Al-4V components manufactured by selective electron beam melting”, S. Tammas-Williams, H. Zhao, F. Leonard, F. Derguti, I. Todd and P. B. Prangnell, Journal of Material Characterisation, 102, 47 - 61, DOI: 10.1007/s10008-015-2864-1 (2015).

325. “Crystallographic defects induced localised corrosion in AA2099-T8 aluminium alloy”, Y. Ma, X. Zhou, W. Huang, Y. Liao, X. Chen, X. Zhang and G. E. Thompson, Corrosion Engineering, Science and Technology, 50 (6), 420-424, DOI: 10.1179/1743278214Y.0000000237 (2015).

326. “Modelling data acquisition during electrochemical noise measurements for corrosion studies”, M. Curioni, T. Monetta, and F. Bellucci, Corrosion Reviews, 33 (4), 187-194, DOI: 10.1515/corrrev-2014-0047 (2015).

334. “Understanding the galvanic interactions between AA2024T3 and mild steel using the scanning vibrating electrode technique”, U. Donatus, H. Liu, X. Zhou, Z. Liu, G. E. Thompson, Materials Chemistry and Physics, 161, 228-236, DOI: 10.1016/j.matchemphys.2015.05.040 (2015).

335. “Analyses of the sequential stages of corrosion on aa2024t3 using the scanning vibrating electrode technique (SVET)”, G. E. Thompson, U. Donatus, H. Liu, D. Elabar, Journal of Materials Engineering and Performance, 24 (10), 3808-3814, DOI: 10.1007/s11665-015-1701-0 (2015).

336. “The effect of post-anodizing rinsing on the morphology and composition of porous and nanotubular anodic films generated on titanium”, P. Skeldon, G. E. Thompson, T. V. Molchan, X. Zhong, I. S. Molchan, Electrochimica Acta, 176, 1233-1238, DOI: 10.1016/j.electacta.2015.07.061 (2015).

327. "Localized corrosion in AA2099-T83 aluminium-lithium alloy: the role of intermetallic particles”, Materials Chemistry and Physics, Y. Ma , X. Zhou, W. Huang, G. E. Thompson, X. Zhang, C. Luo, Z. Sun, 161, 201-210, DOI: 10.1016/j.matchemphys.2015.05.037 (2015).

337. “Formation of a trivalent chromium conversion coating on AA2024-T351 alloy”, G. E. Thompson, P. Skeldon, J. Qi, T. Hashimoto, J. Walton, X. Zhou, T. Hashimoto, Journal of the Electrochemical Society, 163 (2), C25-C35, DOI: 10.1149/2.0771602jes (2015).

328. “Characterization of anodic oxide film growth on Ti6Al4V in NaTESi electrolyte with associated adhesive bonding behaviour”, G. E. Thompson, Z. J. Liu, X. Zhong, H. Liu, I. L. Tsai, U. Donatus, Electrochemica Acta, 182, 482-492, DOI: 10.1016/j.electacta.2015.09.089 (2015).

338. “Corrosion inhibition of aluminium and AA2014-T6 alloy by strontium chromate”, P. Skeldon, Z. Liu, Z. Feng, X. Zhou, G. E. Thompson, S. B. Lyson, S. Gibbon, D. Graham, Surface and Interface Analysis, 122-1238, DOI: 10.1002/sia.5845 (2015).

339. “The role of intermetallics on the corrosion initiation of twin roll cast AZ31 magnesium alloy”, G. E. Thompson, S. Pawar, X. Zhou, G. Scamans, Z. Fan, Journal of the Electrochemical Society, 162, DOI: 10.1149/2.0291509jes (2015).

340. “Antibacterial and Non-cytotoxic Effect of Nanocomposites Based in Polyethylene and Copper Nanoparticles”, X. Zhou, L. A. Tamayo, P. A. Zapata, M. Azocar, X. Zhou, G.E. Thompson, M. A. Paez, Journal of Materials Science: Materials in Medicine, 26 (129), 1-5, DOI: 10.1007/s10856-015-5475-6 (2015).

341. “Corrosion susceptibility of dissimilar friction stir welds of AA5083 and AA6082 alloys”, X. Zhou, U. Donatus, G. E. Thompson, J. Wang, A. Cassell, K. Beamish, Materials Characterization, 107, 85-97, DOI: 10.1016/j.matchar.2015.07.002 (2015).

342. “Effect of sulphate impurity in chromic acid anodizing of aluminium”, P. Skeldon, G. E. Thompson, A. Nemcova, T. Hashimoto, D. Elabar, Corrosion Science, 100, 377-385, DOI: 10.1016/j.corsci.2015.08.019 (2015).

343. “Features in aluminium alloy grains and their effects on anodizing and corrosion”, G. E. Thompson, U. Donatus, D. Elabar, T. Hashimoto, S. Morsch, Surface Coatings Technology, 277, 91-98, DOI: 10.1016/j.surfcoat.2015.07.034 (2015).

349. “Effectiveness of 2-mercaptobenzothiazole, 8-hydroxyquinoline and benzotriazole as corrosion inhibitors on AA 2024-T3 assessed by electrochemical methods”, A. C. Balaskas, M. Curioni, G. E. Thompson, Surface and Interface Analysis, 47 (11), 1029-1039, DOI: 10.1002/sia.5810 (2015).

350. “Modelling and visualisation of material flow in friction stir spot welding”, P. B. Prangnell, A. Reilly, H. R. Shercliffe, Y. C. Chen, Journal of Materials Processing Technology, 473-474, DOI: 10.1016/j.jmatprotec.2015.06.021 (2015).

351. “Novel use of glow discharge optical emission spectroscopy (GDOES) to study corrosion of AA2024-T3 in the presence and absence of inhibitors”, G. E. Thompson, R. V. Bingham, Surface and Interface Analysis, 47 (12), 1098-1108, DOI: 10.1002/sia.5854 (2015).

352. “The mechanism of hydrogen evolution during anodic polarization of aluminium”, M. Curioni, F. Scenini, Electrochimica Acta, 180, 712-721, DOI: 10.1016/j.electacta.2015.08.076 (2015).

353. “Passivation behaviour of 304 stainless steel in an ionic liquid with a fluorinated anion”, G. E. Thompson, I. S. Molchan, J. Walton, P. Skeldon, A. Tempez, S. Legendre, Applied Surface Science, 357 (Part A), 37-44, DOI: 10.1016/j.apsusc.2015.08.189 (2015).

344. “Trivalent chromium conversion coating formation on aluminium”, P. Skeldon, J. Qi, T. Hashimoto, T. Hashimoto, J. Walton, X. Zhou, G. E. Thompson, Surface and Coatings Technology, 280, 317-329, DOI: 10.1016/j.surfcoat.2015.09.024 (2015).

354. “Anodizing behaviour of friction stir welded dissimilar aluminium alloys”, P. Skeldon, X. Zhou, U. Donatus, G. E. Thompson, Journal of The Electrochemical Society, 162 (2), C657-C665, DOI: 10.1149/2.0651512jes (2015).

345. “Flow patterns in friction stir welds of AA5083 and AA6082 alloys”, G. E. Thompson, X. Zhou, U. Donatus, J. Wang, K. Beamish, Materials and Design, 83, 203-213, 10.1016/j.matdes.2015.06.006 (2015).

355. “Quantitative characterization of porosity and determination of elastic modulus for sintered micro-silver joints”, G. E. Thompson, J. Carr, X. Milhet, P. Gadaud, S. A. Boyer, P. Lee, Journal of Materials Processing Technology, 225, 19-23, DOI: 10.1016/j.jmatprotec.2015.03.037 (2015).

346. “Behaviour of alloying elements during anodizing of Mg-Cu and Mg-W in fluoride/glycerol electrolyte”, P. Skeldon, M. S. Palagonia, A. Němcová, I. Kuběna, M. Šmíd, S. Gao, H. Liu, X. L. Zhong, S. J. Haigh, M. Santamaria, F. Di Quarto, H. Habazaki, G. E. Thompson, Electrochemical Society Journal, 162 (9), 487-494, DOI: 10.1149/2.0761509jes (2015).

356. “Elevated temperature, in situ micromechanical characterization of a high temperature ternary shape memory alloy”, G. E. Thompson, J. M. Wheeler, C. Niederberger, R. Raghavan, M. Weaver, J. Michler, The Journal of The Minerals, Metals & Materials Society, 67 (12), 2908-2913, DOI: 10.1007/s11837-015-1627-x (2015).

347. “Microstructure and corrosion properties of the plasma MIG welded AA5754 automotive alloy”, A. Abouarkoub, G. E. Thompson, X. Zhou, G. Scamans, Journal of Minerals and Materials Characterization and Engineering, 3, 318-325, DOI: 10.4236/jmmce.2015.34034 (2015).

357. “The kinematics of deformation and the development of substructure in the particle deformation zone”, J. Quinta da Fonseca, L. Ko, Iop Conference Series: Materials Science and Engineering, 89 (1), DOI: 10.1088/1757-899X/89/1/012012 (2015).

348. “The role of crack branching in stress corrosion cracking of aluminium alloys”, G. E. Thompson, T. L. Burnett, N. J. H. Holyroyd, G. M. Scamans, X. Zhou, P. J. Withers, Surface and Interface Analysis, 47 (11), 1029-1039, DOI: 10.1515/corrrev-2015-0050 (2015).

358. “Surface modifications of stainless steel to minimise contamination in mass spectrometers”, G. E. Thompson, J. Abda, D. Douce, G. Jones, P. Skeldon, Applied Surface Science, 357 (Part A), 593-602, DOI: 10.1016/j.apsusc.2015.08.209 (2015).

359. “The interaction of grain refinement and ageing in magnesium–zinc–zirconium (ZK) alloys”, J. D. Robson, C. Paa-Rai, Acta Materialia, 95, 010-019, DOI: 10.1016/j.actamat.2015.05.012 (2015).

360. “Coating design for controlling β phase IMC formation in dissimilar Al-Mg metal welding”, Y. Wang, L. Wang, J. D. Robson, B. Al-Zubaidy, P. B. Prangnell, Friction Stir Welding and Processing VIII, 352-358, DOI: 10.1002/9781119093343.ch19 (2015).

361. “Automated multi-scale microstructure heterogeneity analysis of selective electron beam melted Ti-6Al-4V components”, H. Zhao, A. A. Antonysamy, J. Meyer, S. T. Williams, P. B. Prangnell, TMS2015 Supplemental Proceedings, 429-436, DOI: 10.1002/9781119093466.ch54 (2015).

362. “Integration of deformation processing with additive manufacture of Ti-6Al-4V components for improved β grain structure and texture”, TMS2015 Supplemental Proceedings, Sidhu, J, A. Wescott, P. B. Prangnell, J. Donoghue, 437-444, DOI: 10.1002/9781119093466.ch55 (2015).

363. “Microstructural origin of localized corrosion in anodized AA2099-T8 aluminium-lithium alloy”, X. Chen, X. Zhou, Y. Yi, Y. Liao, W. Huang, Y. Ma, Surface and Interface Analysis, DOI: 10.1002/sia.5856 (2015).

364. “The propagation of localized corrosion in Al-Cu-Li alloy”, X. Zhou, Y. Ma, G. E. Thompson, C. Luo, Z. Sun, X. Zhang, Z. Tang, X. Zhang, Surface and Interface Analysis, DOI: 10.1002/sia.5890 (2015).

365. “Effect of current density and behaviour of second phases in anodizing of a Mg-Zn-RE alloy in a fluoride/glycerol/water electrolyte” A. Němcová, I. Kuběna, M. Šmíd, H. Habazaki, P. Skeldon , G. E. Thompson, Journal of Solid State Electrochemistry, 20, 4, 1155-1165, DOI: 10.1007/s10008015-2864-1 (2015).

366. “Spallation behaviour of alumina scale formed on FeCrAlY alloy after isothermal oxidation”, X. Zhao, Y. C. Chen, Y. Zhao, P. Xiao, I. S. Molchan, G. E. Thompson, C. Zhu, Oxidation of Metals, DOI: 10.1007/s11085-015-9602-z (2015).

367. “Microstructure and texture evolution during thermomechanical processing of β-quenched Zr”, D.G. L. Prakash, M. Preuss, M. Dahlbäck, J. Quinta da Fonseca, Acta Materialia, 88, 389-401, DOI: 10.1016/j.actamat.2014.12.033 (2015).

368. “Structure and transport in coatings from multiscale computed tomography of coatings - new perspectives for electrochemical impedance spectroscopy modelling?”, A. Trinchi, F. Chen, Y. Yang, S. Sellaiyan, J. Carr, P. Lee, G. E. Thompson, Electrochimica Acta, 1-8, DOI: 10.1016/j.electacta.2015.10.183 (2015).

369. “Identifying suboxide grains at the metal-oxide interface of a corroded Zr-1.0%Nb alloy using (S)TEM, transmission-EBSD and EELS”, H. Jing, A. Garner, N. Ni, A. Gholinia, R. J. Nicholls, S. Lozano-Perez, F. Frankel, M. Preuss, Micron, 69, 35-42, DOI: 10.1016/j.micron.2014.10.004 (2015).

370. “In situ synthesis of PbS nanocrystals in polymer thin films from lead (ii) xanthate and dithiocarbamate complexes: evidence for size and morphology control”, McNaughter, P. D, Y. Zhongjie, Y. Chen, J. R. Brent, J. Rafferty, P. O’Brien, S. J. Haigh, G. E. Thompson, Chemistry of Materials, 27, 6, 2127-2136, DOI: 10.1021/cm504765z (2015).

371. “Microscopic study of the corrosion behaviour of mild steel in ionic liquids for CO2 capture applications”, G. E. Thompson, R. Lindsay, P. Skeldon, T. Schubert, J. Walton, G. Romanos, I. S. Molchan, RSC Advances, 5, 4, 35181-35194, DOI: 10.1039/C5RA01097G (2015).

372. “Corrosion resistance of graphene directly and locally grown on bulk nickel substrate by laser irradiation”, F. Yu, M. Curioni, X. H. Ye, Z. Lin, H. J. Zhang, Z. Liu, M. L. Zong, RSC Advances, 5, 45, 35384-35390, DOI: 10.1039/C5RA01267H (2015).

373. “The role of intermetallics on the corrosion initiation of twin roll cast AZ31 Mg alloy”, X. Zhou, G. E. Thompson, G. Scamans, Z. Fan, S. Pawar, Journal of the Electrochemical Society, 162, 9, C442-C448, DOI: 10.1149/2.0291509jes (2015).

374. “Effects of reagent purity on plasma electrolytic oxidation of titanium in an aluminate-phosphate electrolyte”, A. Nemcova, A. Gholinia, P. Skeldon, G. E. Thompson, S. Aliasghari, Transactions of the IMF, 94, 1, DOI: 10.1080/00202967.2015.1121692 (2015).

375. “Durability and corrosion of aluminium and its alloys: overview, property space, techniques and developments”, X. Zhou, G. E. Thompson, N. L. Sukiman, N. Birbilis, A. E. Hughes, S. J. Garcia, Aluminium Alloys, New Trends in Fabrication and Applications, chapter 2, 47-98, DOI: 10.5772/53752 (2015).

376. “Continuous and discontinuous localized corrosion of a 2xxx aluminium-copper-lithium alloy in sodium chloride solution”, C. Luo, S. P. Albu, X. Zhou, Z. Sun, X. Zhang, Z. Tang and G. E. Thompson, Journal of Alloys and Compounds, 658, 61-70, DOI: 10.1016/j.jallcom.2015.10.185 (2016).

377. “The effect of aluminium on twinning in binary alpha-titanium”, A. Fitzner, D. Prakash, M. Thomas, S. Y. Zhang, J. Kelleher, P. Manuel, M. Preuss, J. Quinta Da Fonseca, Acta Materialia, 103, 341-351, DOI: 10.1016/j.actamat.2015.09.048 (2016).

378. “Effect of interfacial reaction on the mechanical performance of steel to aluminium dissimilar ultrasonic spot welds”, P. B. Prangnell, L. Xu, L. Wang, Y. C. Chen, J. D. Robson, Metallurgical and Materials Transactions A, 334-346, DOI: 10.1007/s11661-015-3179-7 (2016).

385. “Effect of low levels of sulphate on the current density and film morphology during anodizing of aluminium in chromic acid”, P. Skeldon, D. Elabar, T. Hashimoto, J. Qi, G. E. Thompson, Electrochimica Acta, In press (2016).

379. “Influence of water immersion post-treatment parameters on trivalent chromium conversion coatings formed on AA2024-T351 alloy”, J. Qi, T. Hashimoto, G. E. Thompson, Journal of the Electrochemical Society, 163 (5), C131-C138, DOI: 10.1149/2.0221605jes (2016).

386. “Quantification of the influence of increased pre-stretching on microstructure-strength relationships in the Al-Cu-Li alloy AA2195”, P. B. Prangnell, B. I. Rogers, Acta Materialia, In press (2016).

380. “Grain boundary segregation of rare-earth elements in magnesium alloys”, J. D. Robson, S. J. Haigh, B. Davis, D. Griffiths, Metallurgical and Materials Transactions A, 47 (1), 522-530, DOI: 10.1007/s11661-015-3199-3 (2016).

381. “Protective film formation on AA2024-T3 aluminium alloy by leaching of lithium carbonate from an organic coating”, Y. Liu, P. Visser, X. Zhou, S. B. Lyon, T. Hashimoto, M. Curioni, A. Gholinia, G. E. Thompson, G. Smyth, S. R. Gibbon, D. Graham, J. M. C. Mol, H. Terryn, Journal of the Electrochemical Society, 163, C45-C32, DOI: 10.1149/2.0021603jes (2016).

382. “Dissimilar ultrasonic spot welding of aerospace aluminium alloy AA2139 to titanium alloy TiAl6V4”, J. D. Robson, P. B. Prangnell, C. Q. Zhang, Journal of Materials Processing Technology, 231, 382-388, DOI: 10.1016/j.jmatprotec.2016.01.008 (2016).

387. “The effect of nickel on the electrochemical behaviour of AA1050 alloys in nitric acid solution”, P. Skeldon, F. J. Garcia-Garcia, G. E. Thompson, Surface and Interface Analysis, In press (2016).

388. “Influence of coating morphology on adhesive bonding of titanium pre-treated by plasma electrolytic oxidation”, P. Skeldon, G. E. Thompson, A. Nemcova, S. D. Aliasghari, Surface and Coatings Technology, In press (2016).

389. “The effectiveness of hot isostatic pressing for closing porosity in titanium parts manufactured by selective electron beam melting”, P. B. Prangnell, S. Tammas-Williams, I. Todd, P. J. Withers, Metallurgical and Material Transactions. A, In press (2016).

383. “Investigation of S phase (Al2CuMg) dealloying by high resolution 2D and 3D electron imaging”, P. Skeldon, T. Hashimoto, X. Zhang, X. Zhou, S. J. Haigh, G. E. Thompson, Corrosion Science, 103, 157-164, DOI: 10.1016/j.corsci.2015.11.013 (2016).

390. “The effectiveness of combining rolling deformation with wire-arc additive manufacture on b-grain refinement and texture modification in Ti-6Al-4V”, P. B. Prangnell, J. M. Donoghue, A. A. Antonysamy, F. Martina, P. A. Colegrove, S. W. Williams, Materials Characterization, In press and online (2016).

384. “3D imaging by serial block face scanning electron microscopy for materials science using ultramicrotomy”, T. Hashimoto, G. E. Thompson, X. Zhou, P. J. Withers, Ultramicroscopy, 163, 6-18, 10.1016/j.ultramic.2016.01.005 (2016).

391. “3D corrosion characterization of rheocast aluminium alloy A356-T6.1.”, P. Skeldon, B. Mingo, R. Arrabal, A. Pardo, E. Matykina, Materials Characterization, In press (2016).

conFErEncE PAPErS; PrESEnTEd And In ProcEEdIngS

1.

“Friction spot welding multi-material automotive body structures”, P. B. Prangnell, LATEST Multi-materials Workshop, Manchester (2010).

2.

“Influence of water on growth of anodic zirconium oxide nanotubes in glycerol/fluoride electrolytes”, F. Muratore, A. Baron-Wiecheć, P. Skeldon and G. E. Thompson, 61st Annual Meeting of the International Society of Electrochemistry, Nice (2010).

12.

“Influence of water on growth of anodic zirconium oxide nanotubes in glycerol/fluoride electrolytes”, The 61st Annual Meeting of the International Society of Electrochemistry, A. Baron Wiechec, F. Muratore, P. Skeldon, G. E. Thompson, Nice, France (2010).

13.

“Effect of build geometry on texture and grain structure development in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A. Antonysamy, P. B. Prangnell and J. Meyer, Thermec, Quebec (2011).

14.

“Friction spot welding dissimilar materials with rapid cycle times”, P. B. Prangnell, Y. C. Chen, F. Haddadi, N. Iqbal and J. D. Robson, Thermec, Quebec (2011).

15.

“Effect of wall thickness on grain structure and texture during additive layer manufacturing Ti-6Al-4V by electron beam selective melting”, A. Antonysamy, P. B. Prangnell and J. Meyer, Technology developments in Titanium, Rotherham (2011).

16.

“Effect of zinc coatings on joint properties and interface reaction in aluminium to steel ultrasonic spot welding”, F. Haddadi, D. Strong and P. B. Prangnell, TMS, San Diego, Sup. Proc. Vol. 1, Materials Processing and Energy Materials, 735-742 (2011).

3.

“Uso de trazadores metálicos en el estudio del crecimiento de peláculas nanoporosas en aluminio”, S. J. Garcia-Vergara and P. Skeldon, 6th Encuentro Nacional de Materiales. Medellin, Colombia (2010).

4.

“Environmentally-friendly anodizing of aluminium alloys for aerospace”, G. E. Thompson, M. Curioni, E. Koroleva, P. Skeldon, T. Hashimoto and X. Zhou, Australasian Corrosion Association, Corrosion and Prevention, Adelaide (2010).

5.

“Electrochemical methods to assist corrosion control of lightweight alloys”, M. Curioni and G. E. Thompson, Workshop on light weight metal corrosion and modeling for corrosion prevention, Rome (2010).

6.

“Quantification of microstructural homogeneity and the mechanisms of particle refinement during FSP of Al-Si alloys”, C. Y. Chan and P. B. Prangnell, 8th Int. Friction Stir Welding Symposium, Timmendorfer Strand, Germany (2010).

17.

“Optimisation of aluminium to magnesium ultrasonic spot welding”, A. Panteli, Y. C. Chen, D. Strong, Xiaoyun Zhang and P. B. Prangnell, TMS, San Diego, Sup. Proc. Vol. 1, Materials Processing and Energy Materials, 735-742 (2011).

7.

“Optimisation of short cycle time friction spot welding of thin aluminium automotive sheet”, D. Bakavos, C. Y. Chan, L. Babout, and P. B. Prangnell, 8th Int. Friction Stir Welding Symposium, Timmendorfer Strand, Germany (2010).

18.

8.

“Energy efficient spot welding of light alloys and dissimilar materials”, P. B. Prangnell, Advances in Metals Manufacturing Technology, SMEA, Sheffield (2010).

“Mechanisms of joint formation in ultrasonic spot welding aluminium automotive sheet”, in symposium, D. Bakavos, Y. C. Chen and P. B. Prangnell, TMS, San Diego, Sup. Proc.

Vol. 1, Materials Processing and Energy Materials, 735-742 (2011).

19.

9.

“Loss of high angle boundary area during annealing a cryo-SPD processed Al-alloy with a nano-scale lamellar grain structure”, Y. Huang, G. H. Zahid and P. B. Prangnell, 4th Internaional Conference on Recrystallisation and Grain Growth, REX&GG, Sheffield (2010).

“Environmentally-friendly anodizing of aluminium alloys”, G. E. Thompson, M. Curioni, P. Skeldon, X. Zhou and E. Koroleva, 2nd International Conference on Surface Finishing of Light Aluminium, Paris (2011).

20.

“In-situ observation and modelling of intergranular cracking in polycrystalline alumina”, Materials Structure and Micromechanics of Fracture VI, Brno, Czech Republic (2011).

21.

“Application of nuclear resonance analysis and narrow resonance profiling in understanding porous film growth on aluminium”, A. Baron-Wiecheć, P. Skeldon, G. E. Thompson, J. J. Ganem and I. C. Vickridge, International Workshop on High-Resolution Depth Profiling, Paris (2011).

22.

“Direct deposition of electroless Ni-P coatings on magnesium from basic and acid baths”, A. Zuleta, E. Correa, M. Sepulveda, J. G. Castaño, F. Echeverría, P. Skeldon and G. E. Thompson. Presented at Eurocorr 2011, Stockholm, Sweden (2011).

10.

“Material constitutive behaviour and microstructure study on aluminium alloys for friction stir welding”, H. Wang, P. Colegrove, H. M. Mayer, L. Campbell and R.D. Robson, Advanced Materials Research, 89-91, 615-620 (2010).

11.

“Feasibility study of short cycle time friction stir spot welding thin sheet al to ungalvanised and galvanized steel”, P. B. Prangnell, Y. C. Chen, H. Farid, 8th International Friction Stir Welding Symposium, Timmendorfer Strand, Germany (2010).

23.

“Direct electroless nickel-boron plating on commercial purity magnesium”, E. Correa, A. Zuleta, M. Sepulveda, J. G. Castaño, F. Echeverría, P. Skeldon and G. E. Thompson.

(2011). Presented at Eurocorr 2011, Stockholm, Sweden (2011).

24.

“Contamination of surfaces in mass spectrometers”, J. Doff, G. Jones, D. Douce, E.V. Koroleva, P. Skeldon and G. E. Thompson. Presented at Isranalytica, 14th Annual Meeting of the Israel Analytical Chemistry Society.

Tel Aviv, Israel (2011).

25.

“Crystallographic pitting in 3XXX aluminium alloys”, A. Laferrere, N. Parson, X. Zhou and G. E. Thompson.

Presented at Eurocorr. Stockholm, Sweden (2011).

26.

“Hydrogen production from sodium borohydride on a Ni-Ru catalyst; an electrochemisal study”, C. M. Rangel, V. R. Fernanded, M. J. F. Ferreira, A. M. F. R. Pinto, T. Hashimoto and G. E. Thompson. Presented at 4th World Hydrogen Technologies Convention. Glasgow (2011).

27.

28.

29.

“Polypyrrole films on aluminium from acid electrolytes: synthesis and characterisation”, L. C. Scienza and G. E. Thompson. Presented at 27th World Congress of the Polymer Processing Society. Marrakech, Morocco (2011).

“Characterisation of MEA degradation for an open air cathode PEM fuel cell”, R. A. Silva, T. Hashimoto, G. E. Thompson. Presented at III Iberian Symposium on Hydrogen, Fuel Cells and Advanced Batteries. Zaragoza, Spain (2011).

“Tomography of localised corrosion in AA2024 aluminium alloy”, X. Zhou, C. Luo, T. Hashimoto, E. Koroleva, A. E. Hughes, G. E. Thompson and P. Withers. Presented at International Corrosion Congress. Perth, Australia (2011).

34.

“Abrasion circle friction spot welding for rapid FSSW Al to steel automotive sheet”, P. B. Prangnell, 9th International Symposium on Friction Stir Welding, Huntsville, Alabama, USA (2012).

35.

“Assessment by X-ray CT of the effects of geometry and build direction on defects in titanium ALM parts”, F. Léonard, S. Tammas-Williams , P. B. Prangnell, I. Todd, P. J. Withers, in Symposium, Conference on Industrial Computed Tomography, Wels, Austria (2012).

36.

“Accelerated post-weld natural ageing in ultrasonic welding aluminium 6111-T4 automotive sheet”, Y. C. Chen and P. B. Prangnell, In Symposium 13th International Conference on Aluminum Alloys (ICAA13) Edited by: H. Weiland, A. D. Rollett, W.A. Cassada, TMS, Pittsburgh, PA (2012).

37.

“Interfacial reaction during dissimilar joining of aluminum alloy to magnesium and titanium alloys”, J. D. Robson, A. Panteli, C. Q. Zhang, D. Baptiste, E. Cai, P. B. Prangnell, In Symposium 13th International Conference on Aluminum Alloys (ICAA13) Edited by: H. Weiland, A.D. Rollett, W.A. Cassada, TMS, Pittsburgh, PA (2012).

38.

“Interface structure and bonding in rapid dissimilar FSSW of al to steel automotive sheet”, Y. C. Chen and P. B. Prangnell, In Symposium 13th International Conference on Aluminum Alloys (ICAA13) Edited by: H. Weiland, A. D. Rollett, W. A. Cassada, TMS, Pittsburgh, PA (2012).

39.

“Optimization of anodizing cycles for enhanced performance”, M. Curioni, T. Gionfini, P. Skeldon, E. Koroleva and G. E. Thompson, ASST 2012, Italy (2012).

40.

“Application of electrochemical noise analysis to corroding aluminium alloys”, M. Curioni, R. A. Cottis and G. E. Thompson, ASST 2012, Italy (2012).

30.

“On the impact of second phase particles on twinning in magnesium alloys”, M. R. Barnett, N. Stanford, J. Geng, and J. D. Robson, 2011, in TMS 2011, 289-293 (2011).

41.

“Measurement of electrochemical noise: Do we really need a zero resistance ammeter?”, M. Curioni, ECG-COMON 2012, Petten, Netherlands (2012).

31.

“Effect of build geometry on texture and grain structure development in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A. Antonysamy, P. B. Prangnell and J. Meyer, Thermec, Quebec, Canada (2011).

42.

“Environmentally-friendly anodizing of aluminium alloys for aerospace”, G. E. Thompson, M. Curioni, E. V. Koroleva, P. Skeldon, T. Hashimoto and X. Zhou, Corrosion and Prevention 2010, Adelaide, Australia (2010).

32.

“Influence of build geometry on beta grain structure and texture during additive layer manufacture (ALM) of Ti-6Al-4V by electron beam selective melting”, A. A. Antonysamy, P. B. Prangnell and J. Meyer, Titanium Conference (2011).

43.

“Revealing the 3D internal structures of aluminium and its alloys”, T. Hashimoto, X. L. Zhong, M. Curioni, X. Zhou, P. Skeldon, P. J. Withers and G. E. Thompson, ASST 2012, Italy (2012).

33.

“Microstructure formability relationships in new generation high strength aluminium automotive alloys”, R. A. Nolan, M-A. Kulas, J. Quinta da Fonseca and P. B. Prangnell, Euromat (2012).

44.

“Nanotomography for understanding the dealloying of second phase particles in aluminium alloys”, T. Hashimoto, X. Zhou, M. Curioni, P. Skeldon and G. E. Thompson, ASST 2012, Italy (2012).

45.

“Progress of galvanic corrosion in Elektron 21 magnesium alloy”, J. Janiec-Anwar, G. E. Thompson, X. Zhou, M. Turski, T. Wilks and T. Hashimoto, 9th International Conference on Magnesium Alloys and their Applications, Vancouver, Canada (2012).

56.

“Mechanical and microstructural characterization of percussive arc welded hyper-pins for titanium to composite metal joining, in LMT2013”, R. J. Oluleke, D. Strong, O. Ciuca, J Meyer, A. De Oliveira and P. B. Prangnell, 6th Int. Symp. on Light Metals Technology (2013).

46.

“Microstructure and corrosion resistance of eximer laser melted Elektron 21 rare-earth magnesium alloy”, A. Shekhe, Z. Liu, P. Skeldon and G. E. Thompson, 9th International Conference on Magnesium Alloys and their Applications, Vancouver, Canada (2012).

57.

“The effect of temperature on the formability of a high strength aluminum automotive”, R. A. Nolan, M-A. Kulas, P. B. Prangnell, J. Quinta da Fonseca, MS&T 2013, Materials Science and Technology 2013, Montreal, Canada (2013).

58.

47.

“Thermal modelling of Al-Al and Al-steel friction stir spot welding”, P. Jedrasiak, A Reilly, H. R. Shercliff, G. J. McShane, Y. C. Chen and P. B. Prangnell, In Mathematical Modelling of Weld Phenomena 10, Austria (2012).

“Grain structure evolution in alumnium to steel ultrasonic spot welding”, F. Haddadi, P. B. Prangnell, MS&T 2013, Montreal, Canada (2013).

59.

“Advanced aluminium extrusion technology”, McCool, N. S. Malone, J. O’Connor, P. Howe, S. Mills, G. E. Thompson, Y. Liu, X. Zhou, M. Curioni, E. McAlpine, G. Scamans, C. Butler, Aluminium International Today (2013).

60.

“Friction welding of titanium alloys: addressing the structural integrity issues through process optimization”, M. M Attallah, M. Preuss, S. E. Bray, Proceedings of the 1st International Joint Symposium on Joining and Welding, Osaka, Japan, 313-315, DOI: 10.1533/978-1-78242-164-1.313 (2013).

61.

“The effect of aluminium on deformation and twinning in alpha titanium: the 45° case”, A. Fitzner, D. G. Prakash, J. Quinta da Fonseca, M. Preuss, M. J. Thomas, S. Y. Zhang, Materials Science Forum, 765, 549-553 (2013).

62.

“3D characterisation of short fatigue crack in titanium”, S. Birosca, F. A. Garcia-Pastor, M. Karadge, J. Y. Buffiere, M. Preuss, 6246, ICF12, Ottawa (2009), published (2013).

63.

“Measurement of strain and lattice rotation in the particle deformation zone”, L. C. L. Ko and J. Quinta da Fonseca, Materials Science Forum, 753, 21-24 (2013).

64.

“Assessment of the advantages of static shoulder FSW for joining aluminium aerospace alloys”, H. Wu, Y. C. Chen, D. Strong, P. B. Prangnell, THERMEC 2013, Las Vegas, USA (2013).

65.

“The effect of chloride as catalyst layer contaminant on the degradation of PEMFCs”, T. I. Pavia, T. Hashimoto, M. J. Plancha, G. E. Thompson, C. M. Rangel, IV Iberian Symposium on Hydrogen, Fuel Cells and Advanced Batteries, Estoril, Portugal, June (2013).

66.

“Terbium luminescence under X-rays from YAlO3 composite deposited on porous anodic alumina”, N. V. Gaponenko , V. S. Kortov, V. A. Pustovarov , L. S. Khoroshko, A. M. Asharif, I. S. Molchan, G. E. Thompson, A. Podhorodecki, G. Zatrub, J. Misiewicz, Microwave and Telecommunication Technology (CriMiCo), 23rd International Crimean Conference, Crimea, Ukraine (2013).

48.

“Novel approaches to modelling metal flow in friction stir spot welding”, A Reilly, H.R. Shercliff, G.J. McShane, Y. C. Chen and P. B. Prangnell, In Mathematical Modelling of Weld Phenomena 10, Austria (2012).

49.

“Assessment of the advantages of static shoulder FSW for joining aluminium aerospace alloys”, H. Wu, Y. C. Chen, D. Strong, and P. B. Prangnell, Thermec, Las Vegas, USA (2013).

50.

“Estudio del proceso de formacion de recubrimientos electroless Ni-P sobre el magnesio”, A. Zuleta, E. Correa, M. Sepulveda, L. Guerra, J. G. Castano, F. Echeverria, P. Skeldon and G. E. Thompson, Congresso Internacional de Materiales, Medellin, Colombia (2013).

51.

“Enhanced photo- and under X-ray luminescence from Xerogels embedded in mesoporous anodic alumina”, N. Gaponenko, V. Kortov, V. Pustovarov, S. Zvonarev, A. Slesarev, M. V. Rudenko, L. S. Khoroshko, A. M. Asharif, I. Molchan, G. E. Thompson, A. Podhorodecki, J. Misiewicz, and S. Prislopskii, International Porous and Powder Materials Symposium, Turkey (2013).

52.

“A study of mixed inhibitors for corrosion protection of AA2024 T3 aluminium alloy”, A. C. Balsakas, M. Curioni, G. E. Thompson and G. Kordas, Eurocorr, Estoril, Portugal (2013).

53.

“Corrosion testing of aerospace components by electrochemical noise analysis”, M. Curioni, Z. Wang, A. C. Balaskas, E. Rahimi and G. E. Thompson, Eurocorr, Estoril, Portugal (2013).

54.

“Reliability of noise resistance for the estimation of corrosion rate”, M. Curioni and G. E. Thompson, Eurocorr, Estoril, Porugal (2013).

55.

“Influence of galvanized coatings on abrasion circle friction stir spot welding aluminium to steel for automotive applications”, Y. C. Chen, S-F Liu and P. B. Prangnell, Thermec (2013).

67.

“Effect of strain rate on the evolution of dispersoid particles in Al-Mn-Fe-Si Alloy during hot deformation”, T. Hill, J. D. Robson, N. Kamp, Light Metals Technology 2013, UK (2013).

78.

“The influence of hot forming on the microstructure and corrosion behaviour of AZ31B magnesium alloys”, A. Juliawati, X. Zhou, G. E. Thompson, O. E Fakir and J. Dear, Eurocorr, Pisa, Italy (2014).

68.

“Constituent particles and dispersoids in an Al-Mn-Fe-Si alloy studied in three-dimensions by serial sectioning”, L. Dwyer, J. D. Robson, J. Quinta da Fonseca, N. Kamp, T. Hashimoto, G. E. Thompson, Light Metals Technology 2013, UK (2013).

79.

“A new model for discontinuous and continuous precipitation in AZ91 magnesium alloy”, J. D. Robson, Materials Science Forum 783, 461-466 (2014).

80.

69.

“Reducing mechanical asymmetry in wrought magnesium alloys”, J. D. Robson, Light Metals Technology 2013, UK (2013).

“The impact of machining on the corrosion behaviour of AA7150-T651 aluminium alloy”, B. Liu and X. Zhou, Materials Science Forum, 794-796, 217-222 (2014).

81.

“Texture evolution during wire drawing of Mg-RE alloy”, M. Chatterton, J. D. Robson, D. Henry, Magnesium Technology Symposium, TMS 2014, San Diego, USA (2014).

82.

“The effect of temperature on the formability of a high strength aluminium automotive”, P. Prangnell, R. Nolan, J. Quinta Da Fonseca, M. A. Kulas, Materials Science and Technology 2014, Pittsburgh, USA (2014).

83.

“Porous anodic oxides for corrosion protection of aerospace alloys: microstructure optimization and evaluation of performance“, M. Curioni, A. Balaskas, P. Skeldon and G. E. Thompson, ASST 2015, Madeira, Portugal (2015).

84.

“The propagation of localized corrosion in Al-Cu-Li alloy”, X. Zhang, X. Zhou, Y. Ma, G. E. Thompson, C. Luo, Z. Sun, and Z. Tang, Proceedings of the 7th International Conference on Aluminium Surface Science and Technology, Madeira, Portugal (2015).

85.

“Correlation between localized plastic deformation and localized corrosion in AA2099 aluminium-lithium alloy”, W. Huang, Y. Ma, X. Zhou, X. Meng, Y. Liao, L. Chai, Y. Yi, X. Zhang, Proceedings of the 7th International Conference on Aluminium Surface Science and Technology, Madeira, Portugal (2015).

86.

“Microstructural origin of localized corrosion in anodized AA2099-T8 aluminium-lithium alloy”, Y. Ma, X. Chen, X. Zhou, Y. Yi, Y. Liao, W. Huang, Proceedings of the 7th International Conference on Aluminium Surface Science and Technology, Madeira, Portugal (2015).

87.

“Influences of sulphur impurity on chromic acid anodizing”, D. Elabar, A. Nemcova, P. Skeldon, G. E. Thompson, Proceedings of the 7th International Conference on Aluminium Surface Science and Technology, Madeira, Portugal (2015).

88.

“In-situ high temperature EBSD analysis of the effect of a deformation step on the alpha to beta transition in additive manufactured Ti6Al4V”, J. M. Donoghue, J. Quinta Da Fonseca and P. B. Prangnell, Ti-2015: The 13th World Conference on Titanium, On CD (2015).

70.

71.

72.

73.

74.

75.

“Controlling interfacial reaction during dissimilar metal welding of aluminium alloys”, L. Wang, Y. Wang, C. Zhang, L. Xu, J. D. Robson and P. B. Prangnell, Materials Science Forum, 794-796, 416-42 (2014).

“Systematic evaluation of the advantages of static shoulder fsw for joining aluminium”, H. Wu, Y. C. Chen, D. Strong and P. B. Prangnell, Materials Science Forum, 794-796, 407-412 (2014).

“Effect of grain boundary diffusion on growth kinetics of intermetallic compounds between Al alloys and other alloys”, L. Wang, Y. Wang, L. Xu, C. Zhang, J. D. Robson and P. B. Prangnell, Materials Science & Technology Conference and Exhibition 2014, Pittsburgh, PA, 1851-1858 (2014) “Assessment of rapid refill FSSW for 6111-T4 aluminium automotive alloys”, B. Mohysen Al-Zubaidy, Y. C. Chen and P. B. Prangnell, 14th International Friction Stir Welding Symposium, Beijing, China, Publ. TWI, On CD (2014) “Dissimilar friction spot welding of aluminium and magnesium for automotive applications using novel approaches - abrasion circle FSSW and refill FSSW”, Y. C. Chen, B. Mohysen Al-Zubaidy and P. B. Prangnell in 14th International Friction Stir Welding Symposium, Beijing, China, Publ. TWI On CD (2014).

“Analysis of the advantages of stationary shoulder friction stir welding in near-net shape joining high strength aerospace aluminium alloy AA7050-T7651”, H. Wu, Y. C. Chen and P. B. Prangnell, 14th International Friction Stir Welding Symposium, China, Publ. TWI On CD (2014).

76.

“Corrosion behaviour of magnesium electrodes investigated by real-time hydrogen measurement”, M.Curioni, T.Monetta and F.Bellucci, Proceedings of Eurocorr (2014).

77.

“A unique approach of GDOES for improving scanning electron microscopic imaging”, K. Kawano, K. Shimizu and G. E. Thompson, GD Day 2014 Symposium, Horiba, France (2014).

89.

“The origin and implications of microstructural banding in additive manufacture with Ti6Al4V by plasma wire deposition”, H. Zhao, J. M. Donoghue, S. Tammas-Williams and P. B. Prangnell, Ti-2015: The 13th World Conference on Titanium, On CD (2015).

90.

“Predicting the influence of porosity on the fatigue performance of titanium components manufactured by selective electron beam melting”, S. Tammas-Williams, J. Donoghue and P. B. Prangnell, Ti-2015: The 13th World Conference on Titanium, On CD (2015).

91.

92.

93.

“Automated multi-scale microstructure heterogeneity analysis of selective electron beam melted TiAl6V4 components”, H. Zhao, A. A. Antonysamy, J. Meyer, O. Ciuca, S. W. Williams and P. B. Prangnell, TMS 2015, Additive Manufacturing Symposium, Supplementary Proceedings, 429-435, DOI: 10.1002/9781119093466.ch54 (2015).

“Integration of deformation processing with additive manufacture of Ti-6Al-4V components for improved β grain structure and texture, additive manufacturing”, J. Donoghue, J. Sidhu, A. Wescott and P. B. Prangnell, TMS 2015, Additive Manufacturing Symposium Supplementary proceedings, 437-444, DOI: 10.1002/9781119093466.ch55 (2015).

“Coating design for controlling phase IMC formation in dissimilar Al-Mg metal welding, friction stir welding and processing symposium VIII”, Y. Wang, L. Wang, J. D. Robson, B. M. Al-Zubaidy and P. B. Prangnell, 171-179, TMS, DOI: 10.1002/9781119093343.ch19 (2015).

94.

“In-situ high temperature EBSD analysis of the effect of a deformation step on the alpha to beta transition in additive manufactured Ti6Al4V”, P. B. Prangnell, J. M. Donoghue, J. Quinta Da Fonseca, Ti-2015: The 13th World Conference on Titanium, San Diego, CA (2015).

95.

“Effect of sulphate impurity in chromic acid anodizing of aluminium”, P. Skeldon, D. Elabar, A. Nemcova, G. E. Thompson, 7th International Conference on Aluminium Surface Science and Technology, Madeira, Portugal (2015).

96.

“Effect of ionic fluids with imidazolium and lactam-based cations on corrosion of mild steel”, I. S. Molchan, G. E. Thompson, P. Skeldon, R. Lindsay, G. Romanos, International Forum on Recent Developments of CCS Implementation, Athens, Greece (2015).

97.

“Microstructural origin of localized corrosion in anodized AA2099-T8 aluminium-lithium alloy”, X. Zhou, Y. Ma, X. Chen, Y. Yi, Y. Lao, W. Huang, 7th International Conference on Aluminium Surface Science and Technology, Madeira, Portugal (2015).

98.

“Effect of microstructure on the tensile strength of Ti6Al4V specimens manufactured using Additive Manufacturing Electron Beam Process”, P. B. Prangnell, T. Machry, D. Eatock, J. Meyer, A. A. Antonysam, A. Ho, Euro PM2015 Congress and Exhibition, Reims, France (2015).

99.

“Effect of microstructure on the tensile strength of Ti6Al4V specimens manufactured using Additive Manufacturing Electron Beam Process”, P. B. Prangnell, T. Machry, D. Eatock, J. Meyer, A. A. Antonysam, A. Ho, Euro PM2015 Congress and Exhibition, Reims, France. In press (2016).

PrESTIgE, AwArdS And InVITEd LEcTurES Prestige Professor G. E. Thompson Description of Membership: Fellow, Royal Academy of Engineering (FREng) Date Applicable: Annually

Professor P. Skeldon Description of Membership: Member of the Electrochemical Society Date Applicable: 2010 - present

Professor G. E. Thompson Description of Membership: Fellow, Electrochemical Society, New Jersey, USA (FECS) Date Applicable: Annually

Professor J. D. Robson Description of Membership: Manchester Metallurgical Society (Vice President) Date Applicable: 2011 - Present

Professor G. E. Thompson Description of Membership: Fellow, Institute of Materials, Minerals and Mining (FIMMM) Date Applicable: Annually Professor G. E. Thompson Description of Membership: Fellow, Institution of Corrosion (FICorr) Date Applicable: Annually Professor G. E. Thompson Description of Membership: Fellow, Institute of Metal Finishing (FIMF) Date Applicable: Annually Professor P. B. Prangnell Description of Membership: Thermec Conference Organisation Date Applicable: Annually Professor J. D. Robson Description of Membership: EPSRC College Peer review Date Applicable: Annually Professor M. Preuss Description of Membership: Member of the ILL Sub-Committee for the Upgrade Endurance Programme Date Applicable: Annually Professor M. Preuss Description of Membership: Chair of the Science and Technology Advisory Panel a New Engineering Instrument at the European Spallation Source, Lund, Sweden Date Applicable: Annually Professor M. Preuss Description of Membership: Member of the ILL Scientific Council Date Applicable: Annually Professor G. E. Thompson Description of Membership: Editorial Board Member of Corrosion Science Date Applicable: 1992 – Present Professor G. E. Thompson Description of Membership: Editorial Board Member of Anti Corrosion Methods and Materials Date Applicable: 1997 – Present Professor G. E. Thompson Description of Appointment: Officer of the Order of the British Empire (OBE) for research activities of relevance to the defence industries June 2000 Professor G. E. Thompson Description of Membership: Editorial Board Member of Electroplating and Finishing Date Applicable: 2005 – Present Professor J. D. Robson Description of Membership: Light Metals Board, IOM3 Date Applicable: 2005 - Present Professor M. Preuss Description of Membership: Titanium Information Group (TIG) Member Date Applicable: 2009 - Present Dr M. Curioni Description of Membership: Member of NACE International Date Applicable: 2009 – present Dr M. Curioni Description of Membership: Member of Electrochemical Society Date Applicable: 2009 – present

Professor M. Preuss Editorial Role: Section Editor of Encyclopaedic for Aerospace Engineering covering High Temperature Materials Date Applicable: Dec 2011 - ongoing Professor J. D. Robson Description of Membership: Co-chair and Organizer of Magnesium Technology Symposium, EuroMat Date Applicable: 2011 Professor X. Zhou Description of Membership: Ontario Centre of Excellence Assessment Panel Date Applicable: 2012 Professor X. Zhou Description of Election: Elected Fellow for the Institute of Materials Date Elected: August 2012 Professor X. Zhou Description of Election: Elected Fellow for the Institute of Corrosion Date Elected: April 2012 Professor X. Zhou Description of Membership: International Advisory Panel, 9th International Conference on Magnesium Alloys and their Applications, Vancouver, Canada Date Applicable: 2012 Professor X. Zhou Description of Membership: ICAA14 International Organizing Committee Member Date Applicable: 2012 - 2014 Dr J. Quinta Da Fonseca Description of Election: Election to ISIS Beam Time Access Panel Date Elected: August 2012 for 2 years Dr M. Curioni Description of Membership: Member of Institute of Corrosion Date Applicable: 2012 – present Professor G.E.Thompson Description of Membership: International Organising Committee Member for ASST Conference 2014.

Date Applicable: 2013 Professor G. E. Thompson Description of Membership: Member of the Scientific Board, Advances in Materials Science Date Applicable: 2013 – present Dr J. Quinta Da Fonseca Description of Membership: Advanced Sheet Forming committee of the IOM3 Date Applicable: 2013 – present Professor M. Preuss Description of Membership: Member of the Scientific Advisory Committee Laboratory Nuclear Materials at the Paul Scherrer Institute, Switzerland.

Date Applicable: 2013 – present Professor M. Preuss Description of Membership: Member of the Jules Horowitz Test Reactor UK steering committee. Date Applicable: 2013 – present

Professor M. Preuss Description of Membership: EPSRC College for Reviewing Proposals Date Applicable: 2010 - Present

Professor P. B. Prangnell Description of Membership: Light Metals Session Chair: Euromat 2015 Date Applicable: Sept 2015

Professor P. Skeldon Description of Membership: Member of the Electrochemical Society Date Applicable: 2010 - present

Professor X. Zhou Description of Membership: IOM3 Light Metals Board Date Applicable: 2015 – present

Awards Professor J. D. Robson Description of Award: IOM3 Grunfeld Memorial Award and Medal 2011 Awarding Body: IOM3 Date Awarded: March 2011 Dr A. Antonysamy Description of Award: Winner of the Best Research Poster at the 'National Level Conference on Technology Developments in Titanium' Awarding Body: Titanium Information Group TIG-UK Date Awarded: April 2011 Dr J. Wang Description of Award: 1st Prize in the EPSRC LATEST2 Symposium Poster Competition 2011 Awarding Body: The University of Manchester Date Awarded: May 2011 Dr K. Li Description of Award: 1st Prize in The University of Manchester PGR Conference Poster Competition 2011 Awarding Body: The University of Manchester Date Awarded: May 2011 Dr K. Li Description of Award: 3rd Prize in Young Lecture Competition 2012 Awarding Body:IOM3 North West Date Awarded: March 2012

Mr A. Balaskas Description of Award: 2nd Prize in the Materials Research Exchange Poster Competition 2014 Awarding Body: Materials KTN Coventry Date awarded: February 2014 Dr. David Griffiths Description of Award: Materials Literature Review Prize of IOM3 Awarding Body: IOM3 Date awarded: March 2014 Ms B. Liu Description of Award: 1st Prize, Poster Competition, The 14th International Conference on Aluminium Alloys Awarding Body: ICAA14 Date awarded: June 2014 Professor G. E. Thompson Description of Award: Doctor Honoris Causa Awarding Body: Universidad de Santiago de Chile Date awarded: November 2014 Professor J. D. Robson Description of Award: 2015 Hume-Rothery Prize Awarding Body: IOM3 Date awarded: July 2015

Dr A. Lafferrere and Mr J. Smith Description of Award: IOM3 Colin Humphrey’s Education Award 2012 Awarding Body: IOM3 Date Awarded: March 2012 Dr A. Němcová Description of Award: 1st Prize in the 15th International Corrosion and Corrosion Protection of Metals Conference Poster Competition Awarding Body: ICCPM Date Awarded: October 2012 Dr C. Zhang Description of Award: 1st Prize in the EPSRC LATEST2 Researcher Symposium Poster Competition 2012 Awarding Body: The University of Manchester Date Awarded: October 2012 Ms B. Liu Description of Award: 3rd Prize in Young Lecture Competition 2013 Awarding Body: IOM3 Date Awarded: March 2013

Professor George Thompson receiving the degree of “Doctor Honoris Causa” from the University of Santiago de Chile

Professor M. Preuss Description of Award: IOM3 Grünfeld Memorial Award and Medal 2013 Awarding Body: IOM3 Date Awarded: March 2013 Dr. J. Janiec-Anwar Description of Award: 3rd Prize in The University of Manchester PGR Conference Poster Competition 2013 Awarding Body: The University of Manchester Date Awarded: May 2013 Dr. C. Zhang Description of Award: 2nd Prize in The University of Manchester PGR Conference Poster Competition 2013 Awarding Body: The University of Manchester Date Awarded: May 2013 Ms B. Liu Description of Award: 1st Prize in The University of Manchester PGR Conference Poster Competition 2013 Awarding Body: The University of Manchester Date Awarded: May 2013 Dr M. Curioni, Professor P. Skeldon and Professor G. E. Thompson Description of Award: Co-recipients of the Jim Kape Memorial Medal of the Institute of Metal Finishing 2013 Awarding Body: IOM3 Date Awarded: August 2013

Dr Alphons Antonysamy receiving his award for best research poster at the 'National Level Conference on Technology Developments in Titanium', on behalf of the Chairman of the Titanium Information Group

Invited Lectures Professor J. D. Robson Invited Lecture: PRICM Conference, Cairns, Australia (August 2010) Professor J. D. Robson Invited Lecture: IPSUS Summer School, Germany (August 2010) Professor J. D. Robson Invited Lecture: OPTIMoM Conference, Cambridge, UK (September 2010) Professor J. D. Robson Invited Lecture: MagNet Conference, Canada (October 2010) Professor G. E. Thompson Invited Lecture: “Reducing the energy cost of anodizing”, Australasian Corrosion Association, Melbourne, Australia (November 2010) Professor G. E. Thompson Plenary Lecture: “Environmentally-friendly anodizing of aluminium alloys for aerospace”, Corrosion and Prevention Conference, Adelaide, Australia (November 2010) Professor M. Preuss Invited Lecture: “So you think you understand deformation in metals?”

Imperial College London, UK (January 2011) Professor J. D. Robson Invited Lecture: Thermec Conference, Quebec, Canada (August 2011) Professor P. B. Prangnell Invited Lecture: “Friction spot welding dissimilar materials with rapid cycle times”, Thermec, Quebec, Canada (August 2011) Professor P. B. Prangnell Invited Lecture: “Effect of build geometry on texture and grain structure development in additive layer manufacture (ALM) of Ti-6Al-4V”, Thermec, Quebec, Canada (August 2011) Professor J. D. Robson Invited Lecture: EuroMat Conference, France (September 2011)

Professor M. Preuss Invited Lecture: “Variant selection in titanium alloys”, Titanium European Conference, Bristol, UK (March 2012) Professor X. Zhou Invited Lecture: “Corrosion control of aluminium alloys for aircraft application”, The 2nd International Symposium on Aeronautical Engineering, Santiago, Chile (March 2012) Professor G. E. Thompson Invited Lecture: “In-SEM tomography (nano- and micro-tomography with 3View and XuM capabilities)”, FESI-UK Forum for Engineered Structural Integrity Conferences and Related Continuing Professional Development, Manchester, UK (April 2012) Professor G. E. Thompson Invited Lecture: “Revealing the three dimensional internal structure of aluminium alloys”, Aluminium Surface Science and Technology Symposium (ASST VI), Sorrento, Italy (May 2012) Professor J. D. Robson Invited Lecture: Magnesium Technology Conference, Canada (July 2012) Professor J. D. Robson Invited Lecture: Welding Summer School, Leicester, UK (August 2012) Professor X. Zhou Invited Lecture: “Initiation and propagation of IGC in AA2xxx aluminium alloys”, Airbus, UK (August 2012) Professor M. Preuss Invited Lecture: “Titanium and related research - materials performance”, Bao steel and IMR, Shenyang, China (September 2012) Dr J. Quinta da Fonseca Invited Lecture: IMR, Shenyang, China (September 2012) Professor X. Zhou Invited Lecture: “New observation of intergranular corrosion in aluminium alloy”, The 16th Asian Pacific Corrosion Control Conference, Kaohsiung, Taiwan (October 2012)

Professor J. D. Robson Invited Lecture: European Conference on Aluminium Alloys (ECAA), Germany (October 2011)

Dr J. Quinta da Fonseca Invited Lecture: IOM3, Surrey, UK (October 2012)

Professor G. E. Thompson Invited Lecture: “Environmentally-friendly anodizing of aluminium alloys”, 2nd International Conference on Light Metal Surface Finishing, Paris, France (November 2011)

Professor X. Zhou Invited Lecture: “Nanotomography of Localized Corrosion in Aluminium Alloys”, China State Key Laboratory for Marine Corrosion and Protection, Beijing, China (November 2012)

Professor X. Zhou Invited Lecture: “Nanotomography of localised corrosion in aluminium alloys”, The Australian Research Council (ARC) Centre of Excellence for Design in Light Metals Annual Conference, Melbourne, Australia (November 2011)

Dr J. Quinta da Fonseca Invited Lecture: IOM3, Surrey, UK (December 2012)

Professor G. E. Thompson Plenary Lecture: “Fundamental studies to assist development of environmentally-friendly anodizing treatments on aluminium alloys”, China (Ningbo) International Forum on Advanced materials and Commercialization, Ningbo (December 2011) Professor X. Zhou Invited Lecture: “Electron tomography of aluminium alloys”, Constellium, Grenoble, France (December 2011) Professor P. B. Prangnell “Effect of build geometry on texture and grain structure development in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A. Antonysamy, P. B. Prangnell and J. Meyer, Thermec 2011, Quebec, Canada, Materials Science Forum, V706-709, 205-210, doi:10.4028/www.scientific.net/MSF.706-709.205 (2012) Professor G. E. Thompson Plenary Lecture: “Fundamental studies to assist development of environmentally-friendly coatings on aluminium alloys”, Materials Science and Engineering Symposium, Doha, Qatar (February 2012) Professor X. Zhou Invited Lecture: “Near-surface microstructure and anodic film growth on aluminium alloys”, Sapa Technology Centre, Sapa Group (February 2012) Professor J. D. Robson Invited Lecture: The Minerals, Metals and Materials Society (TMS), Florida, USA (March 2012)

Professor P. B. Prangnell “Loss of high angle boundary area annealing a cryo-spd processed aluminium ally with a nano-scale lamellar grain structure”, Y. Huang, G. H. Zahid and P. B. Prangnell, 4th International Conference on Recrystallisation and Grain Growth, REX&GG, Sheffield, UK, Materials Science Forum, 715-716, 219-226 (2012) Professor J. D. Robson Invited Lecture: Constellium CRV, Grenoble, France (January 2013) Professor M. Preuss Invited Lecture: “Variant selection in titanium alloys”, BARC seminar series, Mumbai, India (February 2013) Professor G. E. Thompson Invited Lecture: “Presentation of LATEST2 to Light Metals Workshop with Brunel University” Uxbridge, UK (April 2013) Professor J. D. Robson Invited Lecture: Magnesium Technology Workshop, Madrid, Spain (May 2013) Professor X. Zhou Plenary Lecture: “New development in research for corrosion resistant film on aluminium alloys”, The 3rd International Conference, Aluminium 21-Coatings, St Petersburg, Russia (June 2013) Dr J. Quinta da Fonseca Invited Lecture: Constellium, Grenoble, France (June 2013) Professor G. E. Thompson Plenary Lecture: “Development of environmentally-friendly anodizing conditions”, Italian Metallurgical Society, Naples, Italy (July 2013)

Professor J. D. Robson Invited Lecture: Light Metals Technology Conference, Windsor, UK (July 2013) Professor X. Zhou Invited Lecture: “Environmentally-friendly surface treatment for Al-Li alloy”, Beijing Institute of Aeronautical Materials, Beijing, China (August 2013) Professor X. Zhou Invited Lecture: “Grain boundary precipitation and corrosion behaviour of Al-Li alloy”, Constellium, Grenoble, France (September 2013) Professor X. Zhou Invited Lecture: “Electrochemical methods and surface analysis in corrosion research”, Vrije Universiteit Brussel, Belgium (September 2013) Professor G. E. Thompson Invited Lecture: “LATEST2 programme grant activities”, Light Metals Board, Institute of Materials, Minerals and Mining, London, UK (September 2013) Professor M. Preuss Invited Lecture: “Fundamental deformation mechanisms in Ni superalloys” Rolls-Royce, Derby, UK, (September 2013) Professor G. E. Thompson Invited Lecture: “Overview of recycling research at TARF-LCV meeting”, Coventry, UK (October 2013) Professor J. D. Robson Invited Lecture: “A new model for discontinuous and continuous precipitation in AZ91 magnesium alloy”, Thermec Conference, USA (December 2013) Professor G. E. Thompson Invited Lecture: “Environmentally-friendly anodizing of aluminium alloys”, Hatfield Memorial Lecture, Sheffield, UK (December 2013) Professor P. B Prangnell Invited Lecture: “Assessment of the advantages of static shoulder FSW for joining aluminium aerospace alloys”, Thermec, Las Vegas, USA (December 2013) Professor M. Preuss Invited Lecture: “Effect of macrozones and alloying chemistry on strain heterogeneity in titanium alloys”, TMS, San Diego, California, USA (February 2014)

Dr T. Burnett “Understanding engineering failures from the component-scale to the nano-scale using 3D imaging”, Advanced Engineering Open Conference 2014, Birmingham, UK (2014) Dr J. Quinta da Fonseca Invited Lecture: “The evolution of deformation patterning in two FCC metals with difference stacking fault energies” TMS 2015, Orlando, USA (March 2015) Professor G. E. Thompson Invited Lecture: “Influences of sulphur impurity on chromic acid anodizing”, Aluminium Surface Science and Technology (ASST VII), Madeira, Portugal (May 2015) Dr M. Curioni Invited Lecture: ‘’Looking closely at magnesium corrosion: electrochemical methods, real-time optical imaging and hydrogen measurement’’, 17th Topical Meeting of the International Society of Electrochemistry (Multiscale Analysis of Electrochemical Systems), Saint-Malo, France (June 2015) Professor X. Zhou Invited Lecture: “Tailoring aluminium alloy surface for transportation applications”, The 1st America’s Conference on Aluminium alloys, Toronto, Canada (August 2015) Dr J. Quinta da Fonseca Keynote Lecture: “ The kinematics of deformation and the development of substructure in the particle deformation zone” Risoe International Symposium (September 2015) Professor M. Preuss Invited Lecture: “A study of early deformation twinning in a titanium alloy by x-ray diffraction contrast tomography”, MS&T, Columbus, Ohio, USA (October 2015) Professor X. Zhou Invited lecture: “Tailoring the surface of light alloys for adhesive bonding and painting”, 5th Global Automotive Lightweight Materials conference, Birmingham, UK (April 2016) Professor X. Zhou Invited lecture: “Corrosion and protection of lightweight automotive alloys”, International Conference Automotive Corrosion Protection, Berlin, Germany (February 2016).

Professor P. B. Prangnell Keynote opening address: “Antonysamy, EBSD analysis to understand additive manufacturing (3D printing) in titanium: RMS – Electron Backscatter Diffraction Meeting”, London (March 2014) Professor M. Preuss Invited Lecture: “Fundamentals of titanium alloys in context of dwell fatigue”, CECAM, Lugano, Switzerland (April 2014) Professor J. D. Robson Invited Lecture: "The effect of hot deformation on dispersoid evolution in a model 3xxx alloy”, ICAA14, Norway (June 2014) Professor X. Zhou Invited Lecture: “Anodic film formation on new generation aerospace aluminium alloys”, The 65th Annual Meeting of the International Society of Electrochemistry, Lausanne, Switzerland (August 2014) Professor M. Preuss Invited Lecture: “Irradiation growth mechanisms in Zr alloys studied by ultrahigh resolution EDX spectrum imaging and synchrotron x-ray diffraction”, Zirconium Workshop, Oxford, UK (September 2014) Professor M. Preuss Invited Lecture: “Irradiation growth mechanisms in Zr alloys studied by ultrahigh resolution EDX spectrum imaging and synchrotron x-ray diffraction”, European MRS, Warsaw, Poland (September 2014) Professor J. D. Robson Invited Lecture: “Microstructural modelling for design of magnesium alloys”, OPTIMoM conference, Pembroke College, Oxford, UK (September 2014) Professor G.E Thompson Invited Lecture: “Manchester materials activities and LATEST2 review to USACH”, Santiago, Chile (November 2014) Professor J. D. Robson “Improving formability and joining of light alloys through metallurgical understanding”, Advanced Engineering Open Conference 2014, Birmingham, UK (2014)

Professor X. Zhou delivering an invited lecture on “Nanotomography of Localised Corrosion in Aluminium Alloys”.

humAn cAPITAL ImPAcT

A high priority for the EPSRC LATEST2 Programme Grant was to help address the skills gap in metallurgical and corrosion science training, to contribute to the future generation skills base for academia and industry and to help provide the globally competitive and innovative materials engineers needed by the UK manufacturing sector.

During the lifetime of the award, there was on going development and progression of both students and researchers. Specifically, one of our Co-Investigators has been awarded an EPSRC Leadership Fellowship and promoted to Professor of Metallurgy. A second has been promoted to Reader, and then Professor, a third has been promoted to Senior Lecturer and then Professor, and one of our Post Doctoral Researchers has been promoted to LATEST2 Research Fellow and then Lecturer, in recognition of their achievements.

The EPSRC LATEST2 Programme Grant has successfully attracted high quality students and researchers, the majority of whom are now progressing with their careers either within academia or within industry.

On the following pages are some examples of profiles of the early careers destinations of LATEST2 students and researchers.

Specifically, my thesis was focused on ‘Microstructure, Texture and Mechanical Property Evolution during Additive Manufacturing of Ti6Al4V Alloy for Aerospace Applications’. I enjoyed the research environment, technical advice and experimental help offered by my Professor/Advisor, laboratory technicians, and more importantly the advanced facilities which were made available to me within the School of Materials at The University of Manchester. I worked utilised the SEM-EBSD, high resolution 3D x-ray Dr. Alphons Anandaraj tomography, high resolution Megellam SEM (which could replace high resolution TEM ANTONYSAMY materials Lead at gKn Aerospace Filton, uK imaging capability), x-ray diffraction for residual stress and texture analysis, tensile testing, etc. During my PhD I had the During my Bachelors degree in metallurgical opportunity to work closely with key engineering at Periyar University in India, I industrial partners such as EADS-Airbus developed an interest in metallurgical (collaborator for PhD work), Bombardier engineering. After graduating I began my Aerospace, TWI, Timet, etc. I also had the working career as a ‘Metallurgical Process opportunity to collaborate with other and Quality Control Engineer’ at TVS Brakes universities such as Cranfield University India Ltd, Foundry Division, Tamilnadu. (via RUAM Project-Ready to Use Additive After 2 years of Foundry experience, I had Manufacturing) and University of Sheffield the opportunity to pursue my Masters (AMRC) in the field of AM in the UK with degree at IIT kharagpur with sponsorship unique multidisciplinary experiments on the from the Ministry of Human Resource leading edge of advanced technology Development of India, where I gained an development. These collaborations helped in-depth understanding of Metallurgical and me to share my thoughts and gain Materials Sciences. I was awarded a DAAD knowledge on the latest advances in scholarship to complete my one year research and development in this area. I was master’s research project at the Technical very pleased with the guidance received and University-Dresden, Germany as a Sandwich the quality of my ‘PhD Thesis’ which I programme between IIT-India and Germany submitted to The University of Manchester Universities. After completing my Masters and has been downloaded more than 600 degree, I worked at Renault-Nissan times within a year from all around the Technology and Business Centre, India as a world (the top 10 countries to download it Materials Engineer/Specialist. After working include the USA, India, Germany, Japan, to standards and specifications set by China, Iran, France, Vietnam, Belgium and material scientists, I realised that I still Singapore). In addition, 7 journals and lacked knowledge of what factors define conference papers have been published and restrict metallic materials in real time out of this research on microstructure and engineering applications. This in fact, mechanical properties of TiAl4V alloys stimulated me to pursue a research course using AM. focused on advanced manufacturing processes and materials and hence I chose to pursue my PhD in the reputed University of Manchester on the fast growing technology of Additive Manufacturing of Ti6Al4V alloys which was sponsored by the EPRSC LATEST Programme Grant, and EADS Innovations Work, UK.

After completing my PhD in May 2012, I obtained a position as Materials Lead at the Additive Manufacturing Centre, GKN Aerospace, Filton, UK in June 2012. Where I am now attempting to industrialise the research topic that I worked on during my PhD, where Ti6Al4V parts are manufactured through an additive manufacturing route for real-time use in aerospace applications.

This work is being carried out under an ecoHVP project (ecologically High Value Parts) with a £10 million investment from GKN and EADS (50-50 % collaboration) including £2 million from the BIS-UK Government. Since Additive manufacturing offers complete design freedom and approximately 30% overall weight reduction of existing parts. I am enjoying being part of big ecoHVP team as Materials Lead and, also since joining I have been involved with 4 other projects as materials advisor and, currently working towards a project leader/managerial position in near future at GKN Aerospace, UK for materials related projects. I am also representing GKN Aerospace as a part of the ASTM F42 Committee working on establishing, reviewing and approving the new standards for additive manufacturing.

I would certainly recommend any industrial researchers or Materials Science and Engineering students to pursue high end research on advanced characterization and manufacturing technologies at The University of Manchester.

Dr Aleksandra Baron-Wiecheć Physicist in culham centre for Fusion Energy (uKAEA), uK

After completing my PhD, my scientific career began when I obtained a position as assistant professor at the Silesian University of Technology in Gliwice, Poland in 2005.

I was involved in a project focused on an investigation of the relationship between structure and thermal crystallization processes of amorphous soft magnetic Fe-based alloys as well as their magnetic features and corrosion behavior.

Dr. Kasra Sotoudeh BEng. mSc, Phd, cSci mImmm Section manager Stainless Steel and non-Ferrous Alloys Section materials group TwI Ltd. cambridge I joined TWI in 2011 and currently work in Cambridge as the Section Manager of Stainless Steel and Non-Ferrous Alloys Section, Materials Group.

I first joined the School of Materials at The University of Manchester in 2008 as a Marie Curie Fellow (IEF for Career Development, FP7). During my time at Manchester I was a frequent user of the Van de Graaff accelerator at the Université Pierre et Marie Curie in Paris, where I used a wide range of Ion Beam Analytical techniques to study the mechanism of anodizing. Thanks to the project I got an opportunity to perform unique multidisciplinary experiments at the edge of electrochemistry and nuclear physics.

After finishing my Marie Curie fellowship in 2010 I was privileged to join the EPSRC LATEST2 Programme Grant and continued my scientific adventure within a vibrant environment created by the LATEST2 Team.

Thanks to the project’s research plan and availability of a variety of equipment I gained invaluable hands-on experience in conducting experiments in electrochemistry and materials/surface science. Thanks to the great knowledge of my supervisors and very helpful colleagues within the LATEST2 team, I have gained not only hands-on experience but also new, and more importantly, transferable skills. I feel fortunate to take

My position requires me to lead a wide range of projects, from rapid turn-round failure investigations to long-term R&D programmes for individual companies, consortia of companies and Governmental programmes in oil and gas, power generation, heavy engineering and transport sectors. I am also involved with consultancy work, including failure analysis and managing and conducting single and joint industrial and research projects with main areas of focus related to materials assessment/selection, microstructure property relationships, welding metallurgy (similar and dissimilar joints) and fabrication cracking, combined with expertise in service performance and failure including corrosion, creep, fracture and resistance to environmentally assisted cracking of metallic materials with particular interest in improving materials qualification and design of duplex stainless steels, titanium, aluminium and nickel alloys.

Before joining TWI, I studied and worked at The Materials Science Centre, The University of Manchester more than 7 years. After completing my MSc in 2005, I pursued a

these important lessons with me. This combined experience gave me a very important confidence for moving to Culham Centre for Fusion Energy (CCFE) and being successful as an independent scientist in a demanding environment.

The Culham Centre for Fusion Energy (CCFE) hosts the world's largest magnetic fusion experiment JET (Joint European Torus), on behalf of its European partners.

The JET facilities are operated for scientists from around Europe, co-ordinated by the EFDA-JET Close Support Unit (under the European Fusion Development Agreement).

I work in the R&D Experimental Department and my work includes responsibility for a wide range of surface analysis techniques applied to materials extracted from JET tokamak, development of links with UK and overseas Universities to encourage participation in exploitation of JET data and also assistance in operation of some of JET diagnostic during plasma campaigns.

PhD in Mechanical Metallurgy of Light Alloys with the thesis title of ‘Fundamental Superplasticity of Aluminium Alloys’. During the course of my PhD, I challenged widely held views on superplasticity, namely grain boundary sliding and slip, and quantitatively demonstrated that superplasticity is primarily a result of diffusion creep. After finishing my PhD I stayed on as a Research Associate with my main areas of focus relating to advance metal forming of a wide range of ferrous and non-ferrous alloy sheets.

Throughout these years, the EPSRC funded Light Alloys Towards Environmentally Sustainable Transport (LATEST) Programme Grants, 1st and 2nd Generation, provided me with financial support and also gave me the opportunity to work with a number of knowledgeable academics based at the School of Materials and collaborate with a number of prominent industrial partners.

The experience has indeed had a significant and positive effect on my personal development and has helped me develop a successful career.

Dr Lexi Panteli consultant in materials Science for clean Energy – Europe Amec, uK Having completed my Masters degree in Biomedical Materials Science at The University of Manchester, I spent three years working for BAE SYSTEMS developing and assessing Radar Absorbing Materials using various Composite and Elastomeric materials. I rejoined the School of Materials in 2009 to study for a PhD in Metallic Materials as part of the Light Alloys Towards Environmentally Sustainable Transport (LATEST2) Research Programme of work, funded by EPSRC.

Dr. Leo Prakash D.G Senior Lecturer materials research center, School of Engineering, university of Swansea, uK

Within the LATEST2 framework I was able to work with knowledgeable supervisors, researchers, students and technicians within the university, and collaborated with many people from other organisations, such as Cranfield University and the Beijing Institute of Aeronautical Materials. I was fortunate to have the opportunity to present my work at conferences in the UK and the USA which, coupled with the diverse backgrounds of my LATEST2 peers, has enabled me to build an international network of fellow metallurgists. The facilities available to me during my PhD allowed me to conduct in depth research into Solid State joining of aluminium to magnesium, the issues facing joining these two materials, and finding potential solutions. I enjoyed working on a project that had genuine focus on both the advancement of scientific knowledge and its application to a real world issue; successful joining of aluminium to magnesium could result in a significant reduction in automotive emissions.

Ultrasonic welding, friction stir welding, scanning electron microscopy, x-ray diffraction and electron backscatter diffraction were amongst the techniques I used, and there were many other advanced facilities available as well. To date, the

research I conducted within my PhD has directly resulted in three published academic papers, with a fourth having been accepted.

After completing my Dr.-Ing. in OvG Universität Magdeburg, Germany and postdoctoral research tenure in University of Oxford. In 2008 I joined the School of Materials, The University of Manchester, as a Research Associate. I have been working on hexagonal metals with a special emphasis on light metals (titanium and magnesium) in close association with the LATEST2 investigators, Dr. João Quinta da Fonseca and Professor Michael Preuss. One of the main aspects of my research has been characterizing and modeling the heterogeneous nature of hexagonal metal deformation and investigating its effects on materials performance. The encouraging support of Joao and Michael, and the vibrant research environment in the

LATEST2/School of Materials offered me the motivation to become an expert in hexagonal metals (titanium, magnesium and zirconium), texture evolution, thermomechanical processing, phase transformations and in a wide range of the state-of-the-art analytical tools, such as EBSD, image correlation, in-situ neutron and X-ray synchrotron diffraction and crystal plasticity finite element modeling.

Furthermore, this also provided me with an opportunity to work on Nuclear Materials (zirconium), with other research groups (Professor Phil Withers), Universities (Sheffield and Birmingham) and Industries (Rolls-Royce plc, Serco and Timet UK).

I currently work for AMEC, Clean Energy – Europe in Warrington, a focused supplier of consultancy, engineering and project management services to its customers in the world's oil and gas, mining, clean energy, environment and infrastructure markets.

My role is as Task Manager for a large project researching the Effect of a Heat Flux on the Corrosion of Zirconium in Nuclear reactors, and I also work as a Structural Integrity Consultant providing safety advice to a naval plant. My PhD developed many of the skills that are necessary in my current job: oral and written communication skills, communicating technical content effectively and undertaking independent research are all essential, as are some of the technical skills I learnt during my studies, such as microscopy.

Rotimi Joseph Oluleke metallurgist at rawwater Engineering company Limited After completing my Bachelors degree in Metallurgical and Materials Engineering in Obafemi Awolowo University, Nigeria, I came to the U.K. to study for a Masters in Materials for Industry in Loughborough University. By this stage, I had developed a strong interest in engineering materials and wanted to undertake a PhD at a world renowned institution.

I decided to come to The University of Manchester as it had a great reputation worldwide in the field and also beyond this, and on a personal note, I had a strong

David Mackie MSc BEng(Hons) materials Engineer Amec oil and gas, uK

recommendation from my mentor who had studied at The University of Manchester in the 1970s in a similar field. On this basis, I accepted an offer to undertake a research PhD on a project titled the â&#x20AC;&#x153;Metallurgical performance of hyper joints in composite to metal joiningâ&#x20AC;? which was sponsored by EPRSC LATEST2 Programme Grant and EADS Innovations Work, UK. I was particularly interested in the project because it offered me the unique experience of direct collaboration with industrial partners like EADs and TWI on a novel means of composite to metal joining. The project involved investigating the use of titanium alloys for making hyper-joint features via different manufacturing routes such as additive layer manufacturing and arcpercussive welding. The project also involved conducting series of mechanical testing to ascertain the performance of such hyper-joints features and modelling using Abaqus FE to simulate experimental observations. I was able to achieve the aims and objectives of the project in part due to the wide range of research facilities provided by the university and most importantly because of the technical advice and assistance offered by both my academic and industrial supervisors.

I currently work with Rawwater Engineering Company Limited (RECL) as a Metallurgist.

RECL is an oil industry flow-assurance company providing specialist testing and consultancy in the fields of well technology, water management, materials science and improved oil recovery. In my role as a Metallurgist for RECL, I am responsible for leading the materials section in alloy development that is being considered for metal to metal sealing in oil well abandonment process. In the short period of time that I have being working for RECL, I have come to appreciate all the skills and knowledge I have gained during the course of my PhD from materials testing, characterisation using the SEM and even reviewing FEA models. Being in a small team, I have been given high level responsibilities including liaising with external product qualification agencies, decision making and project management.

For this and many more, I am deeply grateful to The University of Manchester, EPRSC LATEST2 Programme Grant for giving me the opportunity to undertake my PhD degree successfully which has now given me the right platform to begin my career in engineering and materials science at RECL.

While at The University of Manchester I studied for an MSc in Advanced Engineering Materials which complimented my previous industrial experience and undergraduate Mechanical Engineering degree. After completing my MSc I was offered the opportunity to study for an EngD sponsored by Magnesium Elektron and contributing to the EPSRC LATEST2 Research Programme at The University of Manchester.

Since leaving Manchester I worked as an alloy development metallurgist for Oil and Gas Well Abandonment applications. I was able to undertake this role thanks to the skills I learnt both technical and professional during my studies. Indeed the reputation of The University of Manchester helped me to secure my current position as a Materials Engineer for Amec Oil and Gas, UK. Since commencing this role I have been responsible for carrying out an audit on a forge in Italy and working as part of a multi-disciplined team on maintenance projects for North Sea production platforms.

This combination of industrial and academic working environments made for a very interesting and rewarding research project.

Working on the inspection of cast light alloys I frequently used the facilities of the Manchester X-ray Imaging Facility and electron microscope suite. Combined with the support of the academic staff and fellow students the research degree was a positive experience which has enabled me to secure employment in the UK.

I joined the LATEST2 research program through the Advanced Metallic Systems Centre for Doctoral Training after completing my undergraduate studies in Physics and Chemistry at Durham University.

I wanted to do my PhD level studies in an applied field with industrial relevance, while retaining the freedom and independence to pursue my own research ideas and scientific interests.

Dr. David GriďŹ&#x192;ths Project Leader Stainless Steels and non-Ferrous Alloys TwI Ltd, cambridge, uK.

During my PhD at Manchester University I found I had these freedoms together with access to state of the art equipment and the academic support network needed to carry out outstanding research. My PhD, in forming lightweight magnesium alloys, was sponsored by Magnesium Elektron, a leading magnesium producer. This sponsorship helped to direct my research towards the practical challenges facing the industrial use of magnesium, while the deep understanding of fundamental metallurgy within the academic community at Manchester encouraged a rigorous scientific approach which I have found to be a strong asset in my present job.

After obtaining my PhD degree in Corrosion Science and Engineering from the University of Manchester in 2013, I remained within the institution to begin work as a Research Associate.

Dr. Junjie Wang Surface Scientist Innoval Technology Limited, uK.

During my time at Manchester, I gained skills and experience about surface analysis, surface engineering, corrosion evaluation and microstructure characterisation of aluminium alloys. These have benefited my career development in industry specifically with regards my current employer, Innoval Technology Limited. Thanks to the LATEST2 programme, I had opportunities to collaborate with the world's leading companies including Novelis, Sapa Group and Constellium including research projects about aluminium alloys for automotive, aerospace and packaging applications. By participating in the projects, I developed the skills to solve technical problems, develop new technologies and optimise processes for aluminium industry.

I currently work for TWI, which is a materials, joining and technology organisation, as a Project Leader in the stainless steels and non-ferrous alloys section. I manage a wide range of projects across various materials and processes from brazing lightweight aluminium alloys to dissimilar joining of stainless steels and nickel alloys. Clients vary from individual industrial members to international consortia, such as the RecycAl European collaborative project which I currently manage. Exposure to state of the art equipment and the encouragement and support to attend various international conferences have been critical in developing the confidence, management and interpersonal skills that I now take for granted in my current role.

In May 2015 I joined Innoval Technology Limited, a collaborator of the LATEST2 programme, as Surface Scientist. Innoval Technology Limited provides consultancy and technical support to investors, manufacturers and end-users of aluminium, and other metals, across a broad range of industry sectors including rolling, extrusion, forging and finishing throughout the world.

The skills and experience obtained from the LATEST2 programme, has enabled me to establish myself as a consultant to provide expertise for various developments in surface engineered products and new production processes.

Dr. James Andrew Carr Post-doctoral research Associate manchester x-ray Imaging Facility, School of materials, the university of manchester

Dr. Yingchun Chen Senior research Engineer The manufacturing Technology centre (mTc), coventry, uK

I returned to the University of Manchester in 2011 as a LATEST2 PhD Research Affiliate having completed my first degree in Physics there some years prior. My PhD thesis concerned the quantitative characterization and finite element modelling of 3D image datasets as applied to corrosion and protection. My primary experimental technique involved the sectioning of light alloys and coatings in the chamber of an SEM to produce high resolution 3D images.

I also supported a number of experimental teams at I13 Imaging Beamline at Diamond Light Source, where multidisciplinary researchers use very special kinds of X-rays to do Computed Tomography. This kind of imaging is a very powerful complimentary technique that is applicable to a range of disciplines which has allowed me to collaborate extensively.

I thoroughly enjoyed being part of the LATEST2 research team who are highly skilled and knowledgeable researchers that are a pleasure to work with. I found a huge amount of support from the university and LATEST2 in developing my career. From getting involved in outreach activities to learning new computer programming languages, there was always a way to progress and gain experience. I now hold a PDRA position at the Manchester X-ray Imaging Facility (MXIF) where I'm able to maintain the collaborations I first established during my time at LATEST2.

I am currently using 3D imaging and in-situ micro-mechanical testing rigs to reveal failure mechanisms of materials such as thermal barrier coatings and other porous materials. My greatest achievement to date is the publication of my paper “Quantitative Characterization of Porosity and Determination of Elastic Modulus for Sintered Micro-silver Joints” which is a culmination of a number techniques which I developed during my PhD.

I joined the School of Materials at The University of Manchester in 2009 as a Research Associate focusing on dissimilar materials joining using novel solid state joining techniques. From 2010 to 2015, I was privileged to join the EPSRC LATEST2 project and continued my research in the field of dissimilar materials joining for automotive industry. Thanks to Prof. Phil Prangnell, Dr Joe Robson, Mr David Strong and their excellent team for supporting me in that period at Manchester. With their support, I’ve gained enormous knowledge in the field of material joining and material characterization and obtained many chances to present our research work to the world in very important international conferences like THERMEC, TMS, FSW symposium, ICAA etc. All those experiences are invaluable to me and helped me successfully move on to work in industry in 2015.

In February of 2015, I landed a job at The Manufacturing Technology Centre (MTC) as a senior research engineer and continued my research in the field of solid state joining. The MTC was established in 2010 with the objective of bridging the gap between academia and industry. The MTC has a world leading friction welding capability. Extensive investment has been made in two tri-mode rotary friction welders (125T and 300T) with inertia, direct drive and hybrid capability. These machines have advanced controls, including precision upset and final length control and orientation control. The MTC also has the world’s largest linear friction welding machine, with the benefits of fast cycle times and dissimilar materials joining capability for a range of larger scale cross-sections. I’m currently the technical lead in the field of rotary welding and the project manager of the core research project.

Mr Sam Tammas-Williams Post-doctoral research Associate designing Alloys for resource Efficiency (dArE) The university of Sheffield

Dr. Li Wang Engineer Jaguar Land rover, uK

I joined the LATEST2 research group from within The University of Manchester, having gained my first degree in aerospace engineering from The School of Mechanical, Aerospace and Civil Engineering. Prior to starting my PhD, I completed a master’s level taught course in all aspects of metallurgy as part of the advanced metallic system centre for doctoral training. I choose to do a PhD in the LATEST2 programme because it combined strong contacts to industry with access to high quality laboratory equipment and support staff.

I have recently started work as a PostDoctoral Research Associate at the University of Sheffield on an EPSRC funded program grant, DARE, ‘Designing Alloys for Resource Efficiency’. In addition to the technical abilities I gained during my PhD, the project planning and management skills have proved invaluable in adapting effectively to this new role. I am now co-supervising a group of new PhD and master’s students in their research, which has been made easier by the excellent examples I was set in the LATEST2 program.

I will shortly submit my PhD thesis on the quantification of defects, and their effect on mechanical properties, in titanium components manufactured by selective electron beam melting. My academic supervisor provided me with excellent support throughout my project, encouraging me to challenge myself and in the process develop my skills as a researcher. As a result I have had the opportunity to present at several international conferences and industrial meetings with GKN, Rolls-Royce, and Airbus. Internal seminars prior to this within the LATEST2 group provided me with the confidence to present my work to industrial and scientific leaders in the field.

After completing my PhD in Loughborough University, I was delighted to join the LATEST2 research group as a Research Associate working with Dr Joe Robson for 2 years. My work concerned optimising joining performance between Al alloys and other metals e.g. steels, Mg alloys, and Ti alloys, and developing materials modelling to understand and simulate microstructure evolution. I have to say, this 2-year experience very enjoyable and helpful.

LATEST2 is a large, friendly research group, and I have made many friends here, including some for life. LATEST2 is one of the best research groups in the University of Manchester, perhaps the UK! Here we have advanced equipment, powerful software, and a great deal of expert knowledge with continually emerging ideas. An easy way to improve is working with excellent people and advanced facilities, and LATEST2 provides a platform with both.

With the abilities and experience I gained from LATEST2, I was recruited by Jaguar Land Rover as an Engineer within the joining technologies group. My current job focuses on joining technologies between metals (e.g. Al-Al, or Al-Steel) in the automotive industry, which is similar to the projects I studied within LATEST2. Thanks to the knowledge and experience which I gained from Dr. Joe Robson, Prof. Phil Prangnell, and Dr. Ying-Chun Chen from LATEST2 group, I can successfully resolve problems during the advanced manufacturing stages, and utilise my knowledge of modelling welding processes and Friction Stir Welding and Ultrasonic Welding in my current role within Jaguar Land Rover.

Research Associate and widened my research interests to a variety of issues related to the corrosion protection of Light Alloys. In 2011, with the beginning of the LATEST2, I was awarded a Research Fellowship and in 2014 I was appointed Lecturer in Corrosion and Protection at The University of Manchester.

Dr. Michele Curioni Lecturer in corrosion Protection, The university of manchester After obtaining a BSc and a MSc in Materials Science and Engineering from Politecnico di Milano (Italy), I wanted to experience doing research in a worldleading university and I decided to apply for a PhD at the University of Manchester, where I started in 2006. During my PhD I worked within the LATEST portfolio grant, focussing on the development of new, chromate-free, anodizing treatment for the corrosion protection of aerospace alloys.

After completing my PhD, I remained at the University of Manchester initially as a

My Current work focuses on protective surface treatments for light alloys with particular attention to anodic oxidation and use of environmentally friendly inhibitors to provide long-term active protection. This approach involves the investigation of fundamental and applied aspects of the anodic oxidation such as the effects of the electrical parameters and electrolyte composition on the long term protective behaviour. Understanding the interactions between the microstructural features present on practical alloys and the corrosion environment, in the presence or absence of protective treatments and corrosion inhibitors, is also a key aspect of my research activity.

I also work on the development of advanced electrochemical methods for the assessment and prediction of the corrosion

Institute of Berlin in 2010. The studies instilled an in-depth knowledge of material science, including ceramics polymers and glasses. The focus of my final project was light metals, specifically mechanical anisotropy of extruded and rolled AZ31, accomplished in the Extrusion Research and Development Centre Berlin.

Dr. Arnas Fitzner material Scientist in the Amcc, Advanced metal casting centre, Brunel university, uK I became interested in materials science while working as a trainee in a modern cermet factory of the Guehring group in my hometown Berlin, Germany. Experiences in the sinter plant, the quality management and the R&D department of G-ELIT in Berlin-Wittenau, informed my masters studies in material science at the Technical

The School of Materials at the University of Manchester offered me the chance to continue my research on deformation of light metals during a PhD project. The welcoming LATEST2-team offered a lot of freedom to complete my project, â&#x20AC;&#x153;The Effect of alloying elements on deformation and ductility in Titaniumâ&#x20AC;?. Free access to the vast range of characterisation techniques, from classical metallography and XRD over diverse mechanical testers to electron microscopy, allowed understanding how alloying effects the material properties and deformation mechanisms. Ten undergraduate projects under my supervision enhanced my four-year PhD not only scientifically but also personally. The

behaviour. In particular, I develop electrochemical techniques that enable to obtain corrosion-related information by applying minimal or no electrical perturbation to the corroding surface and are therefore intrinsically representative of the real-life behaviour. This involves the development of software and hardware for measurement and analysis of electrochemical noise generated during corrosion and real-time imaging of corroding surfaces.

The LATEST2 programme grant was particularly beneficial to my scientific career thanks to the exciting and challenging objectives that the team has developed during the years. This combined with the critical mass of researchers and expertise, and the strong interactions with industry in a wide range of sectors, gave me the opportunity to focus on the fundamental science required to solve the new technological challenges appearing in the future but also on increasing the technology readiness level of concepts developed during the early stages of my scientific career.

LATEST2 team encouraged me to communicate material science in general to the public and my project in particular to the scientific as well as industrial community.

Most importantly for my career, were conferences I was able to attend, which brought me into contact with industry, including Constellium and BCAST (Brunel Centre for Advanced Solidification Technology). Furthermore, Constellium offered an interesting and challenging job as a research fellow with excellent future perspectives. Together with Constelliums R&D team, at AMCC (Advanced Metal Casting Centre, Brunel University) we develop crash management systems from casting new alloy compositions over specific thermo-mechanical treatments in lab scale, to improving designs of the final product. I am looking forward to a good start at the AMCC, and working as the first part of the metal research park in Brunel, which will upscale the laboratory breakthroughs of BCAST.

Dr Aneta Němcová Post-doctoral research Associate corrosion and Protection centre School of materials The university of manchester

Dr. Alex Cassell Post-doctoral research Associate Environmentally Assisted degradation, School of materials, The university of manchester

I joined the EPSRC LATEST2 Programme Grant at The University of Manchester as part of an Erasmus programme “Student Mobility for Training”, during my PhD in 2012. My research centred on developing plasma electrolytic oxidation coatings on magnesium alloys and studying their microstructure, corrosion behaviour and fatigue performance. The opportunity to use a wide range of modern experimental facilities in cooperation with highly experienced researchers helped me to obtain valuable results for my PhD thesis and successfully complete my doctorate degree at Brno University of Technology in the Czech Republic. It also helped inform my decision to continue working in an academic environment.

After completing my PhD in 2013, I was appointed as a Post-Doctoral Research Associate within LATEST2, where I furthered my knowledge of surface engineering.

Collaboration with international partners gave me, amongst other things, an opportunity to regularly use the Van de Graaff accelerator at the University of Namur in Belgium. I used a range of ion beam analytical techniques to study the mechanism of anodizing of light alloys.

The opportunity to discuss results at regular meetings also helped to develop my presentation and communication skills in the English language.

I joined the EPSRC LATEST2 Programme Grant during my PhD within the Advanced Metallic Systems Centre for Doctoral Training (CDT). Upon completion of my PhD I continued work within LATEST2, as a PostDoctoral Research Associate. The Advanced Metallic Systems CDT provided me with the tools I needed to further my career as an experienced mechanical engineer, and materials science in advanced light alloys was the ideal stepping stone into scientific research at a world-leading university.

aluminium alloys for the transport industry.

I gained skill sets at the forefront of aluminium surface science, corrosion science and aluminium alloy processing, including the ability to solve complicated technical issues encountered in sheet aluminium production. Equally important for my research was the opportunity to attend monthly seminars, group meetings and conferences to showcase student contributions. The EPSRC LATEST2 Programme Grant enabled and encouraged the sharing of information and scientific communication with other research groups and industry. In addition, outreach programmes organised by the LATEST2 team were particularly interesting for students and researchers alike, enabling practical demonstrations of materials science to the community.

My PhD project with the LATEST 2 team, at The University of Manchester, was enhanced by a broad academic support network and the right tools needed to carry out outstanding research in the field of light alloy research. My research was enabled by free access to a vast range of characterisation techniques at the fore-front of materials research including classical metallography, 3D X-ray tomography and advanced electron microscopy techniques.

My PhD project was sponsored by Constellium, who provided development material for a novel application. My research was based around the investigation of the corrosion behaviour of development

Being part of the EPSRC LATEST2 Programme Grant, with close cooperation and supervision by experts in the field, has had a strong positive effect on my personal development. I believe that gaining transferable multidisciplinary skills in material science, electrochemistry and nuclear physics will help me successfully progress in my scientific career.

In August 2015 I began as a Post-Doctoral Research Associate for LATEST 2 as part of a joint venture between Otto-Fuchs and Airbus. The many skills gained from my experiences with LATEST 2 have helped me to interact with industry as a metallurgist, and an environmental degradation and surface Scientist.

Dr Ganesh Kumar Tirumalasetty material Scientist Tata Steel Europe, rotherham, uK

After completing my PhD at Delft University in the Netherlands, I sought to further my expertise in physical metallurgy and have a greater understanding of the mechanical behaviour of materials. Hence, I joined the EPSRC LATEST2 Programme Grant as a Post-Doctoral Research Associate at the

Dr Gabor Timar Post-doctoral research Associate gnET â&#x20AC;&#x201C; complex networks department of Physics university of Aveiro Portugal

University of Manchester. Here, my work focused on devising novel in-situ characterization techniques (using both Electron Backscattered diffraction and digital image correlation) to understand the links between microstructure and its development during deformation and the formability of Mg alloys. Thanks to the availability of a range of equipment, I gained invaluable hands on experience in electron microscopy, digital image correlation and sheet metal testing.

Thanks to the expertise of my supervisor Dr. Joao Quinta da Fonseca and very helpful colleagues within the LATEST2 team, I gained not only hands on experience but also attained important transferable skills.

My supervisorâ&#x20AC;&#x2122;s additional freedom in permitting me to publish my PhD work resulted in me publishing an article in Acta Materialia. This combined experience gave confidence to my career as a successful materials scientist, and as such helped me secure a position within Tata Steel Research and Development.

The Tata Steel Group is among the top-ten global steel companies with an annual crude steel capacity of nearly 30 million tonnes per annum. It is the world's secondmost geographically-diversified steel manufacturer and second largest steel producer in Europe. I work in the Materials Design department where I manage several projects involving new product development of steels for automobile, oil and gas, construction applications and high strength steels for heavy transportation and lifting equipment. My job responsibilities include designing and developing novel steel alloys, steel composites and perform experiments with various microscopy and analytical techniques. In addition, I collaborate with Universities in the UK and overseas by working as an interface between scientific and industrial research.

I arrived at the University of Manchester in 2012 having finished my PhD in physics at the University of Debrecen, Hungary. I joined the EPSRC LATEST2 Programme Grant as a Research Associate focusing on the plastic deformation of hexagonal metal alloys. My primary aim was to understand the limits of formability of industrial alloys by means of crystal plasticity finite element models, building on my experience in statistical mechanics. I was aided in my work by constant discussions with wellestablished researchers within the LATEST2 group and also international collaborations.

I had at my disposal a wide range of stateof-the-art experimental characterisation techniques. I had the chance to co-supervise MSc and PhD students and benefited greatly from working in a diverse multidisciplinary group. I found LATEST2 and the University of Manchester as a whole, to be a very supportive, straight-forward and friendly environment that has helped me gain valuable professional experience and has made my time there most enjoyable and memorable.

In October 2015, I took a position as research associate at the University of Aveiro, Portugal, in one of the leading research groups in the statistical physics of complex networks. I am studying the structure and evolution of multiplex networks as part of the project MULTIPLEX financed by the European Commission.

Although my research interests have changed, I gained a lot of experience in academic research in general during my time at LATEST2. The three years I spent at the University of Manchester has been invaluable in helping me form my decision to pursue an academic career.

Irina Gordovskaya Advanced technologist nSg group Pilkington Technical centre Lathom, uK

I joined the EPSRC LATEST2 Programme Grant at the University of Manchester in 2011 as a PhD student supervised by Professor George Thompson, Professor Peter Skeldon and Dr. Michele Curioni. The aim of my project was to enhance the corrosion resistance of aluminium alloys for aerospace industry using rare earth metals.

While working within LATEST2 I became a specialist in materials science and electrochemistry, with particular emphasis on corrosion protection and analysis of materials. I gained substantial skills in surface analysis and characterization of materials using electron microscopy, XPS, XRD and other methods. The LATEST2 programme provided a stimulating and friendly environment to work within.

Furthermore, The University of Manchester and the School of Materials were extremely family friendly, providing help and advice before and during my maternity leave and supporting me when I returned to continue my project. At the moment I am writing up my thesis and will submit in the coming months.

Upon finishing my research project at the University of Manchester, I have been employed by the Pilkington Technical, which is a part of the international NSG Group and one of the worldâ&#x20AC;&#x2122;s leading specialist glass manufacturers. My role is Advanced Technologist within the Research and Development group. I provide technical support to manufacturing lines and develop new products, improving properties of automotive, architectural and technical glass. The knowledge and experience I obtained while working within LATEST2 is invaluable. Many, if not most, of the methods and instruments I use for my current work I learned during my PhD project. Even more important are the problem-solving and analytical skills which I also gained, as these have provided me with a sound basis for my future career.

ImPAcT ScIEncE communIcATIon

LATEST2 ScIEncE communIcATIon ProgrAmmE The LATEST2 team have successfully developed and executed an effective science communication programme to engage with a wide range of target audiences. The key goals were to raise awareness of the research being undertaken and its value, to develop collaborations both academic and industrial, to facilitate effective knowledge transfer and help address the skills gap by attracting high quality students and researchers into the engineering and physical sciences.

The outreach activities were coordinated by a dedicated Science Communication Officer, supported by the LATEST2 academic champion, academic staff, students and external industrial collaborators. The activities were specifically developed to effectively reach a wide range of target audiences.

OuR "IMPACT" STRATEGy SuCCESSFuLLy REAChED ThE FOLLOWING AuDIENCES:

InduSTry MATErIAL ScIEnTISTS PuPILS AcAdEmIA CommunITy TEAchErS And cArEEr AdVISorS

Events for Schools and Colleges During the lifetime of the award LATEST2 ran a wide variety of events aimed at school and college students and their teachers. The key aims of the activities were to engage students with Materials Science and raise awareness of the subject, the EPSRC, and to introduce them to some of the research taking place in this area, as well as highlight the range of careers and courses available.

We engaged with students in a lot of different ways; our researchers visited schools to deliver lectures and workshops, we hosted work experience students and we also ran practical activities at The University of Manchester for students including full Residential Engineering Summer Schools and a regional “LATEST2 Ultimate Car Challenge” competition.

The programme of activities for schools and colleges went from strength to strength during the lifetime of the award, achieving year on year growth. In year 1 the team achieved 1500 contact points and that figure was more than doubled in the most recent period. Over the lifetime of the award we achieved over 12,500 contact points with students from schools and colleges.

Activities have included participating in Physics at Work Events, LATEST2 Residential Engineering Summer Schools, University of Manchester Science Spectacular Fairs, Headstart Summer Schools, Dragon Fly Days, IOM3 Open Days, Discover Engineering Days, Aim Higher Summer Schools, The Institution of Engineering and Technology Christmas Lectures and more recently Manchester Teen Tech and the LATEST2 Ultimate Car Challenge.

A couple of the key events held during the lifetime of the award are highlighted here.

LATEST2 Engineering Materials Residential Summer Schools

LATEST2 ultimate Car Challenge

The Residential Summer Schools have proven to be a phenomenal success and have been run every year since 2010. A total of 350 students aged 14 – 16 years old, from across the country attended the 5 Day Residential Summer Schools over the lifetime. It is also important to note that with the support of the Widening Participation team we were able to offer a number of bursary places to enable students from difficult economic backgrounds to attend.

The Ultimate Car Challenge was developed as a regional competition to enable secondary school pupils from across Greater Manchester to compete in teams to try to design and build the ultimate model scalextric slot car based on realistic design criteria including, weight, cost, CO2 footprint, safety and asthetics. Pupils were mentored by postgraduate students from across the Faculty of Engineering and Physical Sciences.

The aim of the competition was to give pupils an insight into the world of engineering and the careers and courses available, to engage them with materials science and to provide the postgraduate students with experience of outreach activities.

The aims of the LATEST2 Engineering Residential Summer Schools were for school students to: • Engage with the University and help them find out more about the exciting world of materials science and potential university study and careers, • Learn about the EPSRC, the Engineering and Physical Sciences in general and more specifically the important research being undertaken by the ESPRC LATEST2 Programme Grant, • Find out what life is like for a student at The University of Manchester, • Take part in lectures, practical lab based activities and team challenges, and work with current engineering students and world-class scientists, • Learn more about the fascinating field of materials science, and see how we design materials for automotive and aerospace, • Experience a site visit to a major manufacturer in the automotive or aerospace sector; e.g. Airbus, Jaguar LandRover.

The Engineering Residential Summer Schools have been such a great success that they will continue to be run by The School of Materials.

Students attending the EPSRC LATEST2 Engineering Residential Summer School 2014

Pupils were supplied with a wide range of materials to choose from when building their car including aluminium, steel and carbon fibre, and we encouraged students to think about the advantages and disadvantages of each material. The pupils also had to take a number of factors into account when designing their car including the cost and environmental impact of the materials used, make sure their design was aerodynamic and think about how their car will survive a corrosion test!

Each Postgraduate student was paired with a school, and they ran weekly workshops with the students, supporting them to design and build their car. The competition culminated in a two-day finals event at the University of Manchester, where the winning team from each school came to compete, and their cars were put through various tests including a drag race, circuit time trials, and crash and crush tests! The cars were judged by a panel of experts including representatives from Jaguar Land Rover, The LATEST2 advisory panel and the School of Materials at The University of Manchester.

LATEST2 Ultimate Car Challenge Winning Team

The Ultimate Car Challenge was developed and run for the first time in 2014, with funding provided by the Royal Academy of Engineering through their Ingenious Public Engagement Grants Scheme and supported by the EPSRC LATEST2 Programme Grant.

Over the course of the project we worked with 272 pupils aged 13 – 16 years old, and ran 159 school or university based workshops. The challenge was a huge success, and the positive impact of the project was quantified via student surveys in which 71% answered ‘yes’ or maybe’ to the question – ‘Would you be interested in studying engineering?’ compared to 54% at the start of the project.

Comments made by some of the pupils involved in the project include; “I have learnt that there are many things engineers can do and that it is fun!” and “I have learnt how challenging and exciting engineering can be.” One of the elements most enjoyed by the students was the practical experience of getting hands-on and actually building the car. All of the postgraduate students involved said that they would like to take part in similar activities in the future, and felt that they were now either confident, or very confident, of carrying out public engagement activities – showing the project had developed their skills in this area.

Due to the enormous success of the LATEST2 Ultimate Car Challenge, it ran again in 2015, this time fully funded by the EPSRC LATEST2 Programme Grant.

More information about the Ultimate Car Challenge can be found at: www.ultimatecarchallenge.co.uk

Events for the Community LATEST2 was committed to delivering a programme of activities aimed at the community, including for both family and adult audiences. Each year we were involved in a variety of different events, including taking part in large science festivals such as the Manchester Science Spectacular.

Our community events focused on running hands-on activities aimed at raising awareness of materials science and to showcase some of the research taking place within the LATEST2 programme. These activities were designed to be suitable for a variety of audiences, and encouraged people to engage with the science in a fun and practical way. Our community events have been a huge success, and each year we looked to develop the programme further and reach new audiences.

During the lifetime of the award we have reached over 35,000 contact points with the general community. Activities have

included participating in Cheltenham Science Festivals, Airbus Family Days, Jodrell Bank Summer Science Festivals , Big Bang Science Spectaculars, Meet the Scientist Days at Manchester Museum of Science and Technology and Low Carbon Vehicle CENEX Events. A major event that we have been involved with successfully since June 2013 is the Cheltenham Science Festival.

Cheltenham Science Festival Cheltenham is one of the largest science festivals of its kind, and each year attracts scientists from across industry and academia who come to share their latest research with the public through lectures and interactive activities. In June 2013 we had a stand in the Discover Zone, running hands-on materials science activities aimed at a family audience. The Discover Zone is a hugely popular part of the festival, and over the course of the week is attended by over 7,000 people.

Following the success of this, we took part in the Festival again in 2014, but on this occasion we asked to develop activities for the adults-only zone. In 2015 we returned to the Discover Zone, and were linked in to the Back to the Future theme of the Festival.

We have a run a variety of hands-on activities at the Festival, including using chocolate to explore impact testing, by

LATEST2 Ultimate Car Challenge Crush Test

School visit

LATEST2 Ultimate Car Challenge Track Test

LATEST2 general outreach event for the community

investigating how tough different chocolate bars are using a model impact tester and comparing their structure to engineering materials; e.g. thinking about what an Aero bar can tell us about a metal foam! Other activities have included demonstrating the principle of electro-plating, a recycling challenge dance mat, getting people to try to match every-day objects with images taken of them using electron microscopes!

The events were attended by members of the public, ranging from young children up to adults, and have been a great way to engage with a broad audience.

Events for Industry and Academia The LATEST2 team have delivered a comprehensive programme of events for industry and academia, in order to help to establish and build long-term strategic partnerships with leading industrial and other research institutions and, facilitate networking and knowledge transfer.

As well as organising one or two day academia-industry targeted workshops, the LATEST2 team have had a presence at a number of trade and industry focused fairs.

For example, LATEST2 has given invited presentations at the Advanced Engineering Conference held at the NEC Arena ,the UK’s largest free-to-attend engineering conference programme, where the supply chain meet with visiting engineering and procurement decision makers from OEMs and top tier organisations spanning: Aerospace; Automotive; Motorsport; Marine; Civil Engineering, and more.

Attendance over the 2 days was 13,000 delegates. The team also participated in the EPSRC Conference, Manufacturing the Future. The programme of events for

LATEST2 Conference

Industry and Academia developed each year and one of the key events held is highlighted below. The LATEST2 team organised and hosted the LATEST2 Guest Seminar Series featuring a wide range of guest speakers from both Academia and Industry. The team have also helped organise a number of major conferences including; the Aluminium Surface Science and Technology 2012 and 2015; the Light Metals Symposium at EUROMAT 2015 as well as hosting a number of workshops for example; Challenges for Joining Light Weight Dissimilar Materials for Automotive Applications; Advanced Tools for Characterisation; and a Titanium Information Group Meeting. The team hosted a key road mapping event held in 2014 in collaboration with the Institute of Materials Mining and Minerals (IOM3) light metals Board as highlighted below.

Light Alloys Road Mapping Workshop Fundamental challenges in light alloys research supporting innovation in advanced manufacturing for environmentally sustainable transport

experts from the aerospace and automotive industries and across the materials supply chain in titanium, magnesium and aluminium.

The aim of the meeting was to help to define future research challenges, addressing questions such as: • What developments are needed to help facilitate and support innovative manufacturing in lightweight metallic materials?

• What fundamental enabling research is critical to deliver the light alloy technologies required by the transport sector?

• What are the key technology areas and research challenges for maximum impact?

• What fundamental research synergies exist between different sectors?

The outcomes of the road mapping workshop were widely circulated to academia and industry.

LATEST2 dissemination activities have been further supported by the website, newsletters and published reports. In addition the LATEST2 team have encouraged visits to and from industry and to and from other academic institutions.

The road mapping workshop was held to focus the future direction of UK light alloy research. The aim of the meeting was to identify the research challenges that will need to be addressed, to support future industrial innovation in advanced manufacturing with light alloys in the transport sector. The workshop was by invitation only. Forty-two technical experts participated in the event, including technical

LATEST2 Light Alloys Road Mapping Workshop

coLLABorATorS

Academic Collaborators Advanced Metallic Systems Centre for Doctoral Training (CDT), UK Brno University of Technology, Czech Republic Brunel Centre for Advance Solidification Technology (BCAST), UK Brunel University London, UK Cranfield University, UK Deakin University, Australia Diamond Light Source, UK Engineering and Physical Science Research Council (EPSRC), UK EPSRC Centre for Innovative Manufacturing in Liquid Metal Engineering (LiME), UK Hokkaido University, Japan Imperial College London, UK

Institut Laue-Langevin (ILL), France Iowa State University, USA ISIS, UK Materials Performance Centre (MPC), UK Monash University, Australia The National Center for Metallurgical Research (CENIM), Spain National Centre of Scientific Research (DEMOKRITOS), Greece Ohio State University, USA Politecnico di Milan, Italy RWTH Aachen University, Germany Universidad Complutense de Madrid, Spain Universidad de Santiago de Chile (USACH), Chile UniversitiĂŠ Pierre et Marie Curie, France University of Antioquia, Colombia

University of Birmingham, UK University of Cambridge, UK University of Kaiserslautern, Germany The University of Manchester Aerospace Research Institute (UMARI), UK The University of Manchester, Manchester X-Ray Imaging Facility, UK University of Milan, Italy University of Naples Federico II, Italy University of Nottingham, UK University of Sheffield, UK University of Strathclyde, UK Warwick Manufacturing Group (WMG), UK Xiâ&#x20AC;&#x2122;an Technology University, China

Industrial and RO Collaborators Airbus, an EADS Company, UK Akzo Nobel N. V., the Netherlands Alcoa Inc., UK Aston Martin Lagonda Ltd, UK Australian Government Department of Defence, Australia BAE Systems plc, UK Beijing Aeronautical Manufacturing Technology Research Institute (BAMTRI), China Baosteel Group, China Beijing Institute of Aeronautical Materials (AVIC), China BMW, UK BP, UK Bridgnorth Aluminium Limited, UK Constellium, France Commonwealth Scientific and Industrial Research Organisation (CSIRO), Australia EADS Innovation Works, UK European Synchrotron Radiation Facility (ESRF), France

Engineered Capabilities Ltd, UK FEI Company, UK Ford, USA Goodrich, UK Heat Trace Ltd, UK Helmholtz-Zentrum Geesthacht Centre for Materials and Coastal Research, Germany Innoval Technology Ltd, UK Institute of Materials, Minerals and Mining (IOM3), UK Jaguar Land Rover (JLR), UK Magnesium Elektron, UK Michell Instruments, UK Novelis Inc., USA Northwest Aerospace Alliance (NWAA), UK Northwest Automotive Alliance (NAA), UK Otto Fuchs KG, Germany Poeton Industries Ltd, UK POSCO Engineering & Construction Ltd, South Korea Rio Tinto Group, UK Rolls-Royce plc, UK

Sapa AS Group, Sweden Siemens VAI â&#x20AC;&#x201C; Metals Technologies Ltd, UK Tata Steel Europe Limited, UK Technology Strategy Board (TSB), UK The Welding Institute (TWI), UK Titanium Metals Corporation (Timet), UK Outreach Collaborators Engineering Development Trust (Headstart), UK Institute of Materials, Minerals and Mining (IOM3), UK Jodrell Bank Centre for Astrophysics, UK Museum of Science and Industry (MOSI), UK Nuffield Foundation, UK Royal Academy of Engineering, UK Science, Technology, Engineering and Mathematics Network (STEMNET), UK Smallpeice Trust, UK The University of Manchester Widening Participation, UK Womenâ&#x20AC;&#x2122;s Engineering Society (Dragonfly), UK

mAnAgEmEnT TEAm Professor Philip B. Prangnell LATEST2 Programme director, Theme Leader and Principal Investigator chair in materials Engineering, The university of manchester co-director of the metallic Systems doctoral Training centre of metallurgy Philip Prangnell joined the Manchester Materials Science Centre in 1992 after completing his PhD in Metal Matrix Composites at Cambridge University. He was promoted to Chair in Materials Engineering in 2005 and is Co-director of the Metallic Systems Centre of Doctoral Training Centre in Metallurgy with Sheffield University. He officially took over the Directorship of the LATEST2 in June 2015 after a lengthy period as acting Programme Director. His research activities are largely focused on studying material interactions in advanced thermomechanical processing and joining techniques for light alloys (mainly aluminium and titanium). This work has recently expanded to include the metallurgical optimisation of additive manufacturing. He has on going collaborations with major aerospace companies, including EADS, Airbus, and Rolls-Royce, as well as companies within the supply chain (e.g. Constellium, Siemens, GKN). He is also working with DSTL and BAE Land systems on aluminium intensive fighting vehicles.

Professor Joseph D. Robson LATEST2 deputy Programme director and co-Investigator Professor of metallurgy Joe Robson graduated in Natural Sciences from the University of Cambridge in 1993, and obtained his PhD from the same institution in 1996. Since then he has worked at Cambridge, Swansea, and Manchester universities, and in 2003 was appointed to a Lectureship, becoming a Reader in 2012 and obtaining a personal chair in 2015. In June 2015, Joe took up the position of Deputy Programme Director and remains a Co-investigator on the EPSRC LATEST2 Programme Grant and a member of the Light Alloy Processing group with research interests that are focussed on microstructural evolution and control in industrial alloys, with an emphasis on modelling. Joe's work involves close collaboration with a range of industrial partners including Magnesium Elektron, Novelis, Constellium, Alcoa, and BP plus international research centres including Helmholtz Zentrum Geesthacht and Deakin University, Australia.

Professor Michael Preuss LATEST2 co-Investigator Professor of metallurgy, deputy director of the materials Performance centre and nuclear rolls-royce university Technology centre Michael Preuss is Deputy Director of the Materials Performance Centre and the Nuclear Rolls-Royce University Technology Centre in Manchester. He is a Co-investigator on the EPSRC LATEST2 Programme Grant and the Heterogeneous Mechanics in Hexagonal Alloys across length and time scale (HEXMAT) Programme Grant and recently became Director and Lead PI on the New Nuclear Manufacturing (NNUMAN) Programme Grant. In 2010, Michael was awarded an EPSRC Leadership Fellowship, which he commenced in April 2011. Michael's research focuses on microstructure, mechanical properties and residual stresses in high temperature materials for the aeroengine and nuclear applications.

Professor Peter Skeldon LATEST2 co-Investigator chair in materials Engineering Peter Skeldon graduated in Physics from the University of Manchester in 1974, and obtained a PhD from the same institution in 1977. He subsequently worked in industry in the area of electronic and composite materials, before joining the United Kingdom Atomic Energy Authority, where he was employed for ten years researching corrosion of reactor materials in high-temperature water and sodium environments. He was appointed to a Lectureship at The University Of Manchester Institute of Science Technology in 1992, progressing to Professor in Corrosion Science and Engineering in 2005. Peter is a Co-investigator on the EPSRC LATEST2 Programme Grant, with research interests that are focused on surface treatments of light alloys.

Professor Xiaorong Zhou LATEST2 Theme Leader and co-Investigator Professor of corrosion Science and Engineering Xiaorong Zhou graduated from the Department of Chemistry and Chemical Engineering of Hunan University, China in 1983. He obtained an MSc in materials science and engineering at Beijing University of Aeronautics and Astronautics, China in 1986. He was then appointed research engineer in Beijing Institute of Aeronautical Materials. Xiaorong received his PhD in corrosion science and engineering from UMIST in 1994. Subsequently, he joined the Corrosion and Protection Centre of The University of Manchester (then UMIST) in 1994 initially as Research Fellow, then Lecturer, then was promoted to a chair in 2015. Xiaorong is a Co-investigator on the EPSRC LATEST2 Programme Grant and recently took over as Theme leader on advanced surface engineering and a member of the Corrosion and Protection group. Xiaorong is a visiting professor to University of Santiago of Chile, Chile and Beijing Aeronautical Manufacturing Technology Research Institute, China. Xiaorongâ&#x20AC;&#x2122;s research interests lie in corrosion control of light alloys and developing novel surface engineering approaches.

Dr João Fonseca LATEST2 Theme Leader and co-Investigator Senior Lecturer João Fonseca completed his PhD on the mechanical behaviour of high volume fraction MMCs at the University of Leeds in 2001.

He then moved to the School of Materials at the University of Manchester, where he became a lecturer in 2005 and a senior lecturer in 2011. He is currently active in a number of different research groups, including the Engineering and Process Metallurgy group and the Materials Performance Centre. He is a Co-investigator on the EPSRC LATEST2 Programme Grant, where he is leader of the formability theme. Current projects in LATEST2 aim to understand the limits of formability of high strength aluminium alloys and hexagonal metals such as titanium and magnesium.

Dr Michele Curioni LATEST2 co-Investigator and acting Academic outreach champion Lecturer in corrosion Protection Michele obtained a BSc and MSc in Materials Science and Engineering from Politecnico di Milano (Italy), thereafter embarking on a PhD at the University of Manchester, working within the LATEST Portfolio Partnership. Michele’s PhD focussed on the development of new, chromate-free, anodizing treatment for the corrosion protection of aerospace alloys. After completing his PhD, Michele remained at the University of Manchester initially as a Research Associate, widening his research interests to a variety of issues related to the corrosion protection of Light Alloys. Then in 2011 he was awarded a Research Fellowship, and in 2014 appointed Lecturer in Corrosion Protection. His current work focuses on protective surface treatments for light alloys with particular attention to anodic oxidation and use of environmentally friendly inhibitors to provide long-term active protection.

Professor George Thompson LATEST2 director 2010 - 2015, co-Investigator chair in materials Engineering George Thompson graduated in Metallurgy from the University of Nottingham in 1967 and was awarded his PhD from the same institution in 1970 for studies on the precipitation in Al-Cu and Al-Li alloys. After postdoctoral studies at Nottingham on the effects of heat and mass transfer on the corrosion behaviour of selected metals, he joined Howson Algraphy Ltd (now Agfa UK), lithograhic plate manufacturer, in Leeds in 1973. During the period in industry, he was seconded to UMIST (now known as The School of Materials in The University of Manchester) where promotions were gained from Section Leader to Principal Scientist. In 1978, he joined the academic staff at the Corrosion and Protection Centre in UMIST, and became Professor of Corrosion Science and Engineering in 1990. He has previously served as Head of the Corrosion and Protection Centre and Deputy Head of the School of Materials at The University of Manchester.

Professor Thompson became an Emeritus Professor in 2015 after previously leading the programme. His research interests are largely focused on the corrosion and protection of light alloys, with applications in the architecture, automotive, aerospace, lithography and packaging sectors, and electronic materials.

Ms Susan C. Davis LATEST2 Programme Project manager Sue led the Administrative Support Team, specific responsibilities included the overall project management of the LATEST2 Programme, staff and student recruitment, monitoring and reporting on the performance of the Programme and helping to ensure it was on track to deliver the vision and objectives on time and within budget. She helped to develop and manage existing and new external and internal collaborations with key stakeholders, and attracted new funding to the Programme.

Additionally she was responsible for developing the communication strategy, advertising and promotion including website development. Other aspects of her role included IP and risk management, information management including data collection, storage and dissemination.

Ms Lisa Beattie LATEST2 Programme Administrative Assistant Lisa provided a wide ranging administrative support role across the whole Programme, working particularly closely with the Programme Director, Project Manager, Science Communication Officer and Co-Investigators. She provided secretarial support, and was responsible for placing and receipting orders, booking accommodation and transport for the Team. She played a very active role in organising a wide range of meetings, workshops, symposia and conferences, including promotion of the events and booking of the appropriate venues. She also contributed to the development and implementation of the LATEST2 Management Information System, promotional materials and the website and regularly assisted and participated in outreach activities.

ProFILE Mr Rodney C. Jones Rjinntech Ltd, uK International Advisory Panel chairperson Rod Jones worked in the metals industry for almost 50 years and is now an independent consultant.

Having graduated in Metallurgy following a sandwich degree course at Aston University with industrial sponsorship from Henry Wiggin & Company Limited he did research initially into high temperature material for aircraft engine applications at British Non-Ferrous Metals Research Association.

Following the transition of the company into BNF Metals Technology Centre he specialised in the field of process development and control of fabrication processes in the copper- and aluminium alloy industries. He then moved to Alcan International to continue process developments primarily in the aluminium rolling industry.

After a period as Programme Director at the Banbury Laboratories he moved into operations having responsibilities for technology in the U.K. fabrication plants and subsequently across Europe as Technical Director. Whilst retaining a senior technology position in Europe he returned to Alcan International at Banbury as Laboratory Director.

Following Alcan’s merger with Alusuisse he moved to Switzerland to lead the application of aluminium in automotives followed by obtaining the position of VP Technology for Alcan’s Engineered Products division. This position expanded further following Alcan’s acquisition of Pechiney with global responsibility for the research laboratories and critical technology teams becoming based in Paris.

Key responsibilities of this position became the technology aspects of the spin-off of major rolled products businesses as Novelis and, following the purchase of Alcan by Rio Tinto, the sale of Engineered Products to private equity (now known as Constellium). Following completion of this sale he established RJInnTech Limited, an independent consultancy.

InTErnATIonAL AdVISory PAnEL The International Advisory Panel stood as international experts in the areas of the EPSRC LATEST2 Programme Grant. The Panel was made up of both national and international, academic and individual members with many years experience. The role of the Panel was to advise the Management Team on Strategic directions to benchmark the quality and progress of our research against our objectives and on the international stage.

Current Advisory Panel Members

Dr Jonathon Meyer Dr Ian Norris Additive manufacturing manager TwI Ltd, uK Airbus / EAdS, uK

Dr Helen Finch Jaguar Landrover, uK

Dr Hans Polak r&d manager Aerospace coatings Akzonobel, netherlands

John Ferguson JF consultancy Services, uK

Ms Carol Holden north west Automotive Alliance, uK

Professor Dorte Juul Jensen university of denmark

Professor Bevis Hutchinson Swerea KImAB, Sweden

Professor Warren Poole The university of British columbia, canada

Dr Neil Calder Engineered capabilities Ltd, uK

Previously Serving Advisory Panel Members

Professor Stefan ZaeďŹ&#x20AC;erer university of Aachen, germany

Dr Mark White Jaguar Landrover, uK

Mr Simon Gardiner Airbus, uK

Dr Floris Kooistra Akzonobel, netherlands

Principle Investigators Professor Philip Prangnell, June 2015 â&#x20AC;&#x201C; present Professor George Thompson, July 2010 â&#x20AC;&#x201C; June 2015 Co-Investigators Dr Michele Curioni Professor Michael Preuss Dr Joao Quinta Da Fonseca Professor Joseph Robson Professor Peter Skeldon Professor Xiaorong Zhou Emeritus Professor George Thompson Administrative Team Ms Lisa Beattie, Programme Administrative Assistant Ms Susan Davis, Programme Project Manager Ex Administrative Team Ms Karen Donnelly-Bale, Science Communication Officer Ms Cacia Percival, Programme Administrative Assistant Mr Max Rowe, Science Communication Officer Ms Laura Winters, Science Communication Officer

LATEST2 TEAm mEmBErS Post-Doctoral Research Associates Dr Abdelhadi Abouarkoub Dr Aleksandra Baron-Wiechec Dr Alexander Cassell Dr Yingchun Chen Dr Daniel EsquĂŠ Dr Sergio Gonzalez Dr Paloma Hidalgo-Manrique Dr Naveed Iqbal Mr Dingle Jose Dr Alice Laferrere Dr Yanwen Liu Dr Aneta Nemcova Dr Alberto Orozoco-Cabellero Dr Surajkumar Pawar Dr Irina Shchedrina Dr Gaurav Singh Dr Kasra Sotoudeh Dr Yingtao Tian Dr Gabor Timar Dr Ganesh Tirumalasetty Dr Junjie Wang Dr Li Wang Dr Lei Yang Dr Yuan Feng Yang Dr Sergiu Albu PhD Researchers Dr Ramadan Abuaisha Ms Juliawati Alias Dr Sepideh Aliasghari Mr Basem Al-Zubaidy Dr Alphons Antonysamy Mr Michael Atkinson Dr Elkandari Bader Mr Andronikos Balaskas Mr Tomas Brownsmith Mr Lee Campbell Dr James Carr Dr Mark Chatterton Mr Alex Charlesworth Mr Alec Davis Dr Uyime Donatus Mr Jack Donoghue Mr Jefri Draup Dr Liam Dwyer Mr Dawod Elabar Mr Yingwei Fan Dr Arnas Fitzner Mr Joseph Fixter Mr Benjamin Gardener Mr Matthew Goodhall Ms Irina Gordovskaya

Dr David Griffiths Dr Farid Haddadi Ms Janette Harris Ms Rose Hartley Dr Tom Hill Mr Alistair Ho Dr Justyna Janiec-Anwar Dr Patryk Jedrasiak Mr Aaron Jordan Mr Zelong Jin Dr Kayoko Kawano Mr Michael Kenyon Dr Lawrence Ko Ms Heike Krebs Ms Virginie Landais Ms Bing Liu Mr Feng Li Dr Kai Li Dr Zuojia Liu Dr David Lunt Dr Chen Luo Dr Yanlong Ma Ms Faye McCarthy Dr Sonia Meco Dr Tatsiana Molchan Dr Francesca Muratore Ms Laura Nervo Dr Ross Nolan Dr Rotimi (Joseph) Oluleke Dr Chuleeporn Paa-Rai Dr Alexandra Panteli Dr Goncalo Pardal Mr Andrew Platts Mr Jiantao (Alexander) Qi Mr Reafat Elaish Dr Aiden Reilly Mr Ben Rodgers Mr Gunan Shang Dr Ahmad Shekhe Dr Albert Smith Dr Tahani Suliman Mr Tianzhu Sun Dr Sam Tammas-Williams Mr Andres Taylor Ms Jeanette Torrescano Alvarez Ms Jennifer Usiobo Ms Yin Wang Dr Hao Wu Dr Lei Xu Mr Hao Zhao Dr Chaoqun (Jason) Zhang Ms Xinxin Zhang Mr Wu Wei

EngD Researchers Dr Michelle Collins Dr David Mackie Dr Malgorzata Witkowska Dr Nick Wright MPhil Researchers Ms Milena Urban Visitors Dr Antonello Astarita Mr Manuel Azocar Professor Matthew Barnett Mr Jawed Kamran Mr Ziwen Cao Ms Anna Carangelo Mr Esteban Correa Dr Alaa El-Banna Dr Zuwei Feng Mr Pengtao Gai Mr Oscar Galvis Mr Juan Manuel Hernandez-Lopez Mr Bo-Young Jeong Mr Jawed Kamran Mr Mustafa Kocabas Dr Jianping Li Ms Lea Loaks Ms Alice Mazzarolo Ms Beatriz Mingo-Ramon Ms Lisa Munoz Mr Hayato Okumura Mr Jack Palmer Mr Ferdinando Quintiero Ms Guisi Rita La Monica Mr Albert Smith Mr Mahmood Tahir Ms Laura Tamayo Mr Daniel Trost Dr Etsushi Tsuji Mr Nelson Vejar Dr Shu Yang Dr Yicong Ye Mr Alejandro Zuleta Dr Xinnian Xia

D = Departed

LATEST2 Administration Team The University of Manchester School of Materials E1, The Mill Sackville Street Manchester M13 9PL United Kingdom tel +44 (0)161 306 5959 fax +44 (0)161 306 4865 email latest2@manchester.ac.uk www.manchester.ac.uk/latest2 Royal Charter Number RC000797 KD262 04.16