DOCTORA L T H E S I S

Sajid Ali A

lvi Refractory H

igh-entropy Alloys and Film

s for High Tem

perature Applications

Department of Engineering Sciences and MathematicsDivision of Materials Science

ISSN 1402-1544ISBN 978-91-7790-641-4 (print)ISBN 978-91-7790-642-1 (pdf)

Luleå University of Technology 2020

Refractory High-entropy Alloys and Films for High Temperature Applications

Sajid Ali Alvi

Engineering Materials

Refractory High-entropy Alloys and Films for High Temperature Applications

Sajid Ali Alvi

Engineering Materials

130263-LTU_Avh-Alvi.indd Alla sidor130263-LTU_Avh-Alvi.indd Alla sidor 2020-09-24 09:482020-09-24 09:48

Refractory High-Entropy Alloys and Films for High Temperature Applications

Sajid Ali Alvi

Luleå University of Technology

Department of Engineering Sciences and Mathematics

Division of Materials Science

Kertem safar skem k̃hũ nasib hayronem wuz Manzĩl g̃hẽtaker zh̃ũ qarib hayronem wuz

(Riaz Ahmed Riaz, Gulmit)

To the loved ones I lost

And to the loved ones I found;

To my lovely parents and brother

And to the lovely people of my village Passu.

i

ABSTRACT High-entropy alloy (HEA) is a multi-component alloy constituting five or more principal elements in equi- or near equi-atomic percentages. The high configurational entropy in a HEA composition, in contrast to conventional alloys, leads to the stabilisation of the alloying elements in stable solid solutions of face-centred-cubic (FCC), body-centred-cubic (BCC) and/or amorphous structures. The characteristic properties of HEAs are mainly governed by lattice distortion, sluggish diffusion and entropy- and cocktail-effects. Refractory high-entropy alloys (RHEAs), consisting of refractory elements, are considered as a paradigm shift in developing materials for high temperature applications. The current PhD project investigates four different aspects of RHEAs. First, it involves developing CuMoTaWV RHEA by spark plasma sintering (SPS) and utilising the cocktail effect of HEAs for high temperature tribological application. The use of the cocktail effect, defined as selecting favourable compositions for particular applications, is utilised for RHEA compositions in order to yield adaptive tribological behaviour at changing temperatures or environments. The sintered CuMoTaWV showed formation of BCC solid solution and a composite microstructure. The high temperature tribological investigations showed an adaptive behaviour at different temperatures. At lower temperatures Cu lowered the wear rate through formation of CuO, and at higher temperatures V enhanced the tribological resistance through formation of lubricating V2O5 phases. The second aspect involves studying the effect of lattice distortion on mechanical properties of magnetron sputtered thin film after adding Cu to the refractory elements of Mo, Ta, W and V. A target of CuMoTaWV was developed through partial sintering and used to deposit thin film on different substrates. The deposited film showed formation of BCC solid solution, which was verified through DFT calculations. The lattice distortion in CuMoTaWV film showed high hardness and nano-pillar compressive strength. Furthermore, the tribological properties were enhanced at temperatures up to 400oC due to the addition of Cu. The third aspect involves studying the effect of configurational entropy on the formation and high temperature stability of refractory high-entropy thin film metallic glass and its nitrides, by increasing the number of principal elements. A partially

ii

sintered target of TiVZrNbMoHfTaW was used to deposit thin films of metallic glass and nitrides through magnetron sputtering. The metallic glass thin films and its nitrides were found to have high hardness of 7.3 GPa and 19–43 GPa, respectively. Furthermore, the metallic glass thin films showed a high nano-pillar compressive strength of up to 3 GPa, almost twice as high as conventional metallic glass films. The phase stability of metallic glass and its nitride thin films were found to be stable at temperatures up to 750oC and 950oC, respectively. The exceptionally superior mechanical properties and high temperature stability has been attributed to the presence of high configurational entropy. The last part of this PhD thesis consists of studying high-entropy-based W-rich alloys for high temperature applications. A W-based alloy of composition W0.5(TaTiVCr)0.5 was consolidated using SPS. The resulting alloy revealed a BCC solid solution structure. The microstructure of W-rich alloys consist of a combination of W-rich, high-entropy and TiC phases. The BCC solid solution structure in W-rich alloys was found to be stable with exceptionally high compressional strength up to 1,400oC. A high compressive yield strength of 1136 ± 40 MPa, 830 ± 60 MPa and 425 ± 15 MPa was found at test temperatures of 1,000oC, 1,200oC and 1,400oC, respectively. The resulting high strength has been related to the formation of high-entropy phases, which in return induces sluggish diffusion at higher temperatures. The high temperature tribology at 400oC showed an average COF and low wear rate of 0.5 and 1.37 x 10-5 mm3/Nm, respectively. The high temperature wear resistance at 400oC was enhanced due to the presence of HEA and TiC phases. The studies carried out in this thesis suggest the possibility of utilising the full potential of the cocktail effect, lattice distortion and configurational entropy in designing new high-entropy compositions for applications requiring adaptive tribological behaviour, superior mechanical properties and high temperature phase stability.

iii

ACKNOWLEDGEMENTS

This doctoral thesis is part of the Thermo-Mechanical and Tribology Infrastructure

(TMTEST) project which focusses on the development of new metal and ceramic

materials for high temperature applications and is funded by the Swedish Foundation

for Strategic Research (SSF). I am extremely thankful for being part of this project.

I would like to extend by deepest gratitude to my supervisor Farid Akhtar for giving

me the opportunity to work on this project and for being a source of motivation for

innovative research work. I would also like to thank my co-supervisor Marta-Lena

Antti for her valuable feedback during the last four years.

My sincere gratitude to Lars Frisk, Johnny Grahn and Erik Nilsson for their tireless

effort in helping out in different labs, and for always bringing laughter and a positive

work atmosphere to the department.

To all my colleagues at the Division of Materials Science, I am extremely grateful

for a very productive and positive working environment. I would specially like to

thank Alberto Vomiero for collaborating with me on thin film synthesis and providing

valuable feedback on my work. Many thanks to Dariusz Jarzabek at IPPT, Warsaw,

Poland, for his valuable collaboration on nano-mechanical testing of thin films, and

I am glad that I sat next to you during dinner at a conference in Ghent, as our chat

resulted in a very valuable collaboration. I would also like to thank Owais Waseem

at Plasma Division in MIT, United States, for his collaboration and for providing

valuable feedback on my manuscript. My sincere gratitude goes to Mojtaba Gilzad

Kohan for his great friendship, and for helping me develope new coatings. Many

thanks to Magnus Neiktar, Daniel Hedman, Kamran Saeidi, Pedram Ghamgosar,

Piotr Jenczyk and Michal Milczarek and Federica Rigoni for their collaboration in

different research and their feedback. I am also grateful for great times at Engineering

iv

Materials with Hanzhu Zhang, Kritika Narang, Zhejian Cao, Ana Feltrin, Marina

Oset and Viktor Sandell. Also, thanks to Johan and Pernilla for teaching me coffee

roasting and appreciating all the value chains of specialty coffee at Gringo Nordic

Roastery.

I am grateful to my dear friends Sohaib, Fahad, Sydney, Jamil, Shahab, Marko, Lasse,

Joakim, Nadia, Emma, Bryan, Felicia and Chrystel for being there for me when I

needed them during the past decade.

Lastly, I would like to thank my loving parents and brother for their continuous

support throughout my life and for their unconditional love.

v

List of Papers

Appended papers of this thesis: Paper I

High temperature tribology of CuMoTaWV high-entropy alloy Sajid Alvi and Farid Akhtar Wear 426 (2019): 412–419

Paper II Synthesis and mechanical characterization of CuMoTaWV high-entropy film by magnetron sputtering Sajid Alvi, Dariusz Jarzabek, Mojtaba Gilzad Kohan, Daniel Hedman, Piotr Jenczyk, Marta Maria Natile, Alberto Vomiero and Farid Akhtar ACS Applied Materials & Interfaces 12 (18) (2020): 21070–21079

Paper III Enhanced mechanical and thermal stability of high-entropy TiNbMoZrHfWVTa thin film metallic glass and its nitrides Sajid Alvi, Dariusz Jarzabek, Michal Milczarek, Daniel Hedman and Farid Akhtar (To be submitted) Paper IV High temperature performance of W0.5(TaTiVCr)0.5 refractory alloy Sajid Alvi, Owais Ahmed Waseem and Farid Akhtar (Submitted to Metals) Published book chapter

High-entropy Ceramics Sajid Alvi, Hanzhu Zhang and Farid Akhtar In High-entropy Alloys, IntechOpen, 2019

vi

List of papers not included in this thesis:

Paper I High temperature tribology of polymer derived ceramic composite coatings Sajid Alvi and Farid Akhtar Scientific Reports 8 (2018): 15105

Paper II Advanced Mechanical Strength in Post Heat Treated SLM 2507 at Room and High Temperature Promoted by Hard/Ductile Sigma Precipitates Kamran Saeidi, Sajid Alvi, Frantisek Lofaj, Valeri Ivanov Petkov and Farid Akhtar Metals 9 (2019) 199.

Paper III Adaptive nanolaminate coating by atomic layer deposition Sajid Alvi, Pedram Ghamgosar, Federica Rigoni, Alberto Vomiero and Farid Akhtar Thin Solid Films 692 (2019): 137631

Paper IV High temperature tribology of selective laser melted 316L stainless steel Sajid Alvi, Kamran Saeidi and Farid Akhtar Wear 448 (2020): 203228 Paper V Tribological performance of Ti6Al4V at elevated temperatures fabricated by electron beam powder bed fusion Sajid Alvi, Magnus Neikter, Marta-Lena Antti and Farid Akhtar Tribology International 153 (2021): 106658

vii

CONFERENCE CONTRIBUTIONS

International Materials Research Meeting in The Greater Region

Saarbrücken, 6–7 April, 2017

Oral Presentation

High temperature tribology of poymer derived ceramic composite coatings

Sajid Alvi and Farid Akhtar 7th International Conference on Fracture Fatigue and Wear

Ghent University, 9–10 July, 2018

Oral Presentation

Adaptive nanolaminate coating by atomic layer deposition

Sajid Alvi, Pedram Ghangosar, Federica Rigoni, Alberto Vomiero and Farid Akhtar Tribology Days 2018

Sandvik Coromant, Sandviken, 27–28 November, 2018

Oral Presentation

High Temperature tribology of CuMoTaWV high-entropy alloy

Sajid Alvi and Farid Akhtar

22nd International Conference on Wear of Materials

Miami, 14–18 April, 2019

Oral Presentation

High temperature tribology of CuMoTaWV high-entropy alloy

Sajid Alvi and Farid Akhtar

viii

Tribology Days 2019

Swerim, Stockholm, 12–13 Nov, 2019

Oral Presentation

Synthesis and characterization of CuMoTaWV high-entropy film

Sajid Alvi, Dariusz Jarzabek, Mojtaba Gilzad Kohan, Daniel Hedman, Piotr Jenczyk, Marta Maria Natile, Alberto Vomiero and Farid Akhtar

ix

Abbreviations

HEA High-entropy alloys RHEF Refractory high-entropy films FCC Face-centred cubic BCC Body-centred cubic HCP Hexagonal close-packed SEM Scanning electron microscopy EDS Energy-dispersive x-ray spectroscopy TEM Transmission electron microscopy XRD X-ray diffraction SPS Spark plasma sintering RT Room temperature HT High temperature PM Powder metallurgy TFMG Thin film metallic glass COF Coefficient of friction RBS Rutherford backscattered spectroscopy XPS X-ray photoelectron spectroscopy DFT Density function theory

x

xi

TABLE OF CONTENTS Abstract ...................................................................................................................... i

Acknowledgements .................................................................................................. iii

1. High-entropy alloys ............................................................................................... 1

The inception of high-entropy alloys..................................................................... 1

2. Refractory High-entropy alloys ............................................................................. 5

Processing of refractory HEAs .............................................................................. 5

Bulk refractory HEAs ........................................................................................ 5

Refractory HEA thin films and their nitrides .................................................... 8

Properties of refractory HEAs ............................................................................... 8

Mechanical behaviour of bulk refractory HEAs ................................................ 8

Mechanical behaviour of refractory high-entropy films and their nitrides ...... 10

Wear properties of bulk refractory HEAs ........................................................ 11

3. Research Objectives ............................................................................................ 13

4. Methodology........................................................................................................ 17

5. Summary of published work................................................................................ 23

Paper I .................................................................................................................. 23

Paper II ................................................................................................................ 25

Paper III ............................................................................................................... 27

Paper IV ............................................................................................................... 31

6. Future Directions ................................................................................................. 33

References ............................................................................................................... 37

Appended Papers ..................................................................................................... 47

xii

1

1. HIGH-ENTROPY ALLOYS

The inception of high-entropy alloys The widespread strategy for the synthesis of alloys of engineering importance has been based on mixing one principal element, like Fe, Ti or Al, with smaller amounts of other elements. The concept of alloy development has been instrumental to the technological advancement of civilisation and daily life. Conventional alloy development limits the degree of freedom in the selection of composition for alloys with special microstructure and properties for future advanced applications. Karl Franz Achard first proposed the idea of multi-component alloys in the late eighteenth century, in his book “Recherches sur les Proprites des Alliages Metallique,” which included a compilation of experimental work of 900 alloy compositions from 11 different metals, with up to seven metals in equal proportions in weight in each of the compositions. This knowledge was lost as the book was written in French and ignored by metallurgists everywhere, until it was brought to light in 1963 by Professor Cyril Stanley Smilth [1].

The first systematic work exploring the concept of multi-principal-element alloys (high-entropy alloys) was independently reported by Brian Cantor, Jien-Wei Yeh and S Ranganathan in 2003–2004 [2–6]. The early publications captured the interest of material scientists around the world towards the development of high-entropy alloys and related materials. Since then, research into these new alloys started to increase exponentially after researchers working with different aspects of materials science started to apply the concepts in their own fields.

2

High-entropy alloys (HEA) can be simply defined as a multicomponent alloy system that consists of five or more principal elements with equi- or near equi-atomic composition with atomic fractions between 5% to 35% [7]. The use of the term high-entropy alloy comes from the entropy-driven stabilisation of multicomponent alloys, especially at high temperatures. In general, total mixing entropy has four contributions, namely configurational, vibrational, magnetic dipole and electronic randomness, where configurational entropy dominates the other three [8,9]. The configurational entropy of a system can be represented using Boltzmann’s equation [9,10]:

∆𝑆𝑆𝑐𝑐𝑐𝑐𝑐𝑐𝑐𝑐 = −𝑘𝑘 ln𝑤𝑤 Equation 1

Thus, the configurational entropy per mole towards solid solution formation with n element and Xi mole fraction can be represented by:

∆𝑆𝑆𝑐𝑐𝑐𝑐𝑐𝑐𝑐𝑐 = −𝑅𝑅∑ 𝑋𝑋𝑖𝑖 𝑙𝑙𝑙𝑙𝑋𝑋𝑖𝑖𝑐𝑐𝑖𝑖=1 Equation 2

For equi-atomic solid solution composition, Equation 2 can be simplified as [7,11]:

∆𝑆𝑆𝑐𝑐𝑐𝑐𝑐𝑐𝑐𝑐 = 𝑅𝑅 ln𝑙𝑙 Equation 3

where 𝑘𝑘 is Boltzmann’s constant, 𝑤𝑤 is the number of ways in which the available energy can be mixed or shared among the particles of the system, 𝑅𝑅 is the gas constant (8.314 J/K mol), 𝑋𝑋𝑖𝑖 is the mole fraction of each ith component and 𝑙𝑙 is the number of components in the system. The configurational entropy for a system of five elements will be 1.61R, which restricts the definition of HEA to an alloy system consisting of equi- or near equi-molar composition with a configurational entropy larger than 1.5R �∆𝑆𝑆𝑐𝑐𝑐𝑐𝑐𝑐𝑐𝑐 > 1.5𝑅𝑅� [7]. Subsequently, following the configuration entropy classification, conventional alloys (steel, Ti-alloy or Al-alloy) are termed as low-entropy alloys with configuration entropy lower than 1R (∆𝑆𝑆𝑐𝑐𝑐𝑐𝑐𝑐𝑐𝑐 ≤ 1𝑅𝑅) , and superalloys (Ni-based or Co-based) and bulk metallic glasses are termed medium-entropy alloys with configurational entropy at the borderline of high-entropy and low-entropy alloys (1𝑅𝑅 ≤ ∆𝑆𝑆𝑐𝑐𝑐𝑐𝑐𝑐𝑐𝑐 ≤ 1.5𝑅𝑅) [12]. Based on these classifications, the field of entropy stabilised alloys is divided into three sections, as shown in Figure 1.

3

Figure 1. Alloy design based on configurational entropy. Adopted with permission. Copyright 2013, Springer Nature [12].

The microstructure and properties of HEAs are governed by different mechanisms. However, four basic core effects that give HEAs superior properties over conventional alloys have been identified [12]. The high-entropy effect plays a major role in stabilising the formation of solid solution in HEAs, resulting in a simpler microstructure than the expected heterogeneous structure which has a brittle nature. Based on thermodynamics, Gibbs free energy of mixing ∆𝐺𝐺𝑚𝑚𝑖𝑖𝑚𝑚 can be calculated by:

∆𝐺𝐺𝑚𝑚𝑖𝑖𝑚𝑚 = ∆𝐻𝐻𝑚𝑚𝑖𝑖𝑚𝑚 − 𝑇𝑇∆𝑆𝑆𝑚𝑚𝑖𝑖𝑚𝑚 Equation 4

where ∆𝐻𝐻𝑚𝑚𝑖𝑖𝑚𝑚 is the enthalpy of mixing, 𝑇𝑇 is the temperature and ∆𝑆𝑆𝑚𝑚𝑖𝑖𝑚𝑚 is the entropy of mixing. From Equation 4, a larger number of elements and high temperature can lower the free energy of mixing by increasing the 𝑇𝑇∆𝑆𝑆𝑚𝑚𝑖𝑖𝑚𝑚 term to form a stable solid solution phase over intermetallic phases with lower configurational entropy [12].

The multicomponent matrix of each solid solution phase in HEAs is a whole solute matrix where each atom is surrounded by a different atom in a lattice structure, and the high atomic size differences lead to severe lattice strain and stress. Furthermore, the bonding energies and crystal structure among constituent atoms induce high amounts of lattice distortion in HEAs, resulting in high strength and hardness.

The formation of a random solid solution or ordered solid solution in HEAs hinders substitutional diffusion, since a vacancy is competed for by many atoms surrounding it, where the matrices in HEAs are regarded as whole-solute matrices. The sluggish

High-entropy Alloys

Medium-entropy Alloys

Low-Entropy Alloy

•∆𝑆𝑆𝑐𝑐𝑐𝑐𝑐𝑐𝑐𝑐 ≥ 1.5𝑅𝑅

•1.5 ≥ ∆𝑆𝑆𝑐𝑐𝑐𝑐𝑐𝑐𝑐𝑐 ≥ 1𝑅𝑅

•∆𝑆𝑆𝑐𝑐𝑐𝑐𝑐𝑐𝑐𝑐 ≤ 𝑅𝑅

4

diffusion in HEAs contributes to slow grain growth, increased recrystallisation temperature, reduced particle coarsening, the formation of a supersaturated state and fine precipitates, and increased creep resistance [13–15].

Ranganathan first presented the concept of the cocktail effect in his article “Alloyed pleasures: Multimetallic cocktails” [6]. As HEAs consist of five or more principal elements, the resulting solid solution can have a single, dual or more phase and the resulting properties are the combined effect of each element as well as lattice distortion. Therefore, each phase in HEA solid solution can be regarded as an atomic composite. This core effect can be utilised by selecting elements for properties needed in alloys for specific applications [16–24].

The inception of HEAs has opened up a new alloy development in materials science due to their special microstructure and superior mechanical properties. Different processing routes can be applied in developing HEAs for specific applications. Particularly, HEAs have shown promise regarding applications such as cutting tools, hydrogen storage-, aerospace-, plasma facing- and thermoelectric-materials, which require materials with enhanced high temperature mechanical and wear properties, corrosion and creep resistance, hard hardness and fatigue properties [21,25–27].

5

2. REFRACTORY HIGH-ENTROPY ALLOYS

The initial research on HEAs was based on 3d-transition metal alloy compositions of Fe, Co, Cr, Mn and Ni, also known as Cantor alloys [28]. These alloys were found to have enhanced mechanical properties up to 800oC. However, these alloys were not superior to Ni-based superalloys. To overcome the limitation of Cantor alloys and to exceed the properties offered by Ni-based superalloys for high temperature applications, recent research progress has been made in developing new refractory HEAs. Refractory HEAs consist of group IV to VI elements in the periodic table and form a BCC structure. Senkov et al., at the American Air Force Research Laboratory, were the first to report quaternary MoNbTaW and quinary MoNbTaWV refractory HEAs, and studied the room temperature (RT) and high temperature (HT) compressive properties [29,30]. Both alloys were developed using arc melting and formed a BCC solid solution. The refractory HEAs showed high compressive strengths from RT to 1,600oC as compared to conventional superalloys.

Processing of refractory HEAs Bulk refractory HEAs Refractory elements with high melting points (>1,800oC) make the processing of refractory HEAs more challenging. Arc melting is one of the main development methods for refractory HEAs, which involves liquid state melting of elements in high vacuum or inert atmosphere. The large differences in melting temperature of the elemental mixture in arc melting leads to different defects, such as micro- and macro- segregation in the form of dendritic microstructure, residual stresses and pores [31].

6

The resulting defects in refractory HEAs are affected by the solidification rate. Higher solidification rates result in grain refinement and reduced micro-segregation [32]. The post-processing of arc melted refractory HEAs through cold rolling and/or annealing (1,200–1,800oC) has been found to be useful to produce a homogenous composition with good mechanical properties [33–35].

Figure 2. Temperature dependence of (a) yield stress and (b) specific yield stress for refractor HEAs and two Ni-based superalloys (Inconel 718 and Mar-M247). RT: room temperature; SPS: spark plasma sintering; TRIP: transformation-induced plasticity. Copyright 2018, Cambridge University Press [31].

Powder metallurgy (PM) is another important processing route to counter the micro- and macro-segregation problems in refractory HEAs during solidification. The PM of refractory HEAs involves the use of elemental or mechanically alloyed powder mixtures, followed by consolidation in vacuum using spark plasma sintering (SPS), also known as pulsed current processing (PCP) [36]. The PM route results in fine-grained microstructures with homogenous composition due to its high solidification rate. The fine-grained microstructure contributes to the enhanced mechanical properties, as compared to refractory HEAs developed through conventional techniques. The initial studies on developing HEAs with SPS was focussed on transitional metal-based HEAs. Owais et al. reported the first refectory HEA with a composition of WxTiTaVCr (x=0.3-0.9), developed with SPS using elemental powder mixture [20]. The resulting refractory HEA and W-rich alloy composite

7

showed high hardness and RT yield strength of 800 HV and ~2.3 GPa, respectively, which decreased with increasing W content. Furthermore, the fast heating and cooling rates in SPS have been found to be beneficial towards developing new HEA composites for functional applications, such as high temperature tribology for aerospace and steam turbine applications [37]. Liu et al. developed a MoNbTaTiV refractory HEA using mechanical alloying followed by SPS, which showed high compressive yield strength in the range of 1.8–2.2 GPa [38]. The superior mechanical properties were attributed to the grain boundary strengthening arising from ultra-fine grain microstructure and interstitial solid solution strengthening.

Recently, additive manufacturing (AM), such as laser-melt deposition (LMD), direct metal deposition (DMD), Laser Powder Bed Fusion (LPBF) and laser engineered net shaping (LENS), has been employed for developing refractory HEAs [39]. A starting powder without any defects, such as pores, cracks, inclusion and suboptimal surface roughness, is essential for governing the properties of the resulting AM alloy. The starting powders for AM of HEAs are developed mainly through gas atomisation, water atomisation and mechanical alloying [40–42]. The use of LMD to develop TiZrNbHfTa refractory HEA from an elemental powder mixture shows a homogenous equi-atomic composition with a hardness value significantly higher than arc-melted samples [43]. Furthermore, the fast solidification rate in LMD hinders micro- or macro-segregation. However, formation of pores was observed due to release of a gas from the substrate or from powders. In another work, MoTaNbW refractory HEA was developed using DMD with a pulsed Nd:YAG laser, where the equi-molar composition was found to be sensitive to laser powder due to different melting points of the principal elements [44]. LPBF has also been employed to develop MoTaNbW refractory HEA using blended elemental powder feedstock that showed bulk samples deviating from initial powder feedstock chemistry due to vaporisation of elements with lower melting points [45,46]. The resulting refractory HEA showed a microhardness range of 475–830 MPa. The proposed LPBF was designed to develop flank blades for aviation applications.

8

Refractory HEA thin films and their nitrides HEA films and coatings are an efficient strategy for performing high-throughput experiments for developing new HEA compositions, as compared to time consuming and costly traditional alloy development processes [47]. In recent years, different coating deposition technologies have been deployed in developing new HEA films and coatings, such as magnetron sputtering, laser cladding, thermal spraying, electrodeposition and plasma-transferred arc cladding [48]. Of all the technologies, magnetron sputtering is the most widely used technique for HEA film deposition, due to its versatility in controlling film composition and properties through changing deposition parameters, such as substrate bias, substrate temperature, sputtering power and atmosphere (Ar, N2, CH4 and/or O2) [49–52]. Furthermore, high quenching rates of up to 106 K/s combined with low surface mobility makes it possible to synthesise amorphous HEAs using magnetron sputtering, which is not achievable through conventional bulk alloy synthesis techniques.

Properties of refractory HEAs Mechanical behaviour of bulk refractory HEAs Refractory HEAs are found to be brittle at RT [31]. The addition of group IV elements, such as Ti, Hf and Zr, increases the ductility refractory HEAs, while the addition of subgroup V and VI elements and/or Al increases the strength at the cost of reduced ductility. Recently, the addition of Ti in HfNbTaTiZr was found to increase the RT ductility with a compressive strain of 50% without fracture [53]. Similarly, MoNbTaTiW and MoNbTaTiVW showed higher RT ductility as compared to MoNbTaW and MoNbTaVW, respectively [30,54]. This brittle-to-ductile transition, based on composition variation, is related to the electronic structure changes inducing Jahn-Teller distortion and the transition of elastic instability modes from tensile to shear failure. The brittle behaviour of most of the refractory HEAs has been explained by the segregation of interstitial elements’ impurities and grain boundary segregation during solidification and/or annealing. Zou et al. studied micropillar compression with diameters ranging from 2 µm to 200 nm in single crystalline MoTaNbW films and reported high strengths of up to ~4–4.5 GPa, which has a strength three times higher than bulk samples and showed significantly

9

improved ductility [55]. Similarly, in another work, Zou et al. studied the fracture toughness of bicrystalline MoTaNbW and found it to be lower than single crystalline samples, which was attributed to the presence of carbon and nitrogen segregated at grain-boundaries of bicrystalline samples [56]. The RT temperature mechanical behaviour has also been improved by the addition of carbides and silicides reinforcements. The addition of small amounts of carbon (0.1-0.3 at%) to refractory HEAs has been found to increase the RT ductility, peak strength and strain hardening ability due to solution strengthening and second-phase strengthening, by forming MC carbides (M = Hf, Nb, Ti or Zr) [57]. Similarly, small amounts of silicon increase the RT ductility and compressional strength by refining the grain size [58,59]. Other strategies, such as severe plastic deformation followed by annealing at 300-1,200oC, leading to grain refinement and formation of new phases, has been found to enhance the mechanical properties at RT [55,60,61]. Refractory HEAs developed by SPS have been found to show enhanced mechanical properties compared to the same alloys developed through arc melting. Pan et al. developed NbMoTaW and TiNbMoTaW refractory HEA using mechanical alloying and SPS [62]. The resulting refractory HEA showed high hardness and a compressional yield strength of ~7 GPa and ~2.4 GPa, respectively. The resulting high hardness and compressional strength has been related to the fine grain sizes and formation of precipitates using SPS processing.

Refractory HEAs show brittle-to-ductile transition with increasing temperatures and show good ductility and ductile fracture at temperatures above 600–800oC. The refractory HEAs MoNbTaW and MoNbTaVW were found to have high compressive strength of 421–506 MPa and 656–735 MPa at temperatures up to 1,400–1,600oC range, respectively [29,30]. The replacement of Nb with Mo has been found to increase the compressive strength of HfMoNbTaTiZr and HfMoTaTiZr at 1,000oC and 1,200oC [63]. The reported refractory HEAs have been found to have less correlation between RT and high temperature compressive strength values, for example 2–3 phase refractory HEAs will have a high compressive strength at RT and low compressive strength at high temperatures [31]. Similarly, a single phase refractory HEAs will have a low RT compressive strength while a high compressive yield strength at high temperatures. These findings suggest that refractory HEAs with good mechanical properties at RT do not necessitate good mechanical properties at

10

high temperatures. Thus, studying high temperature mechanical properties is also essential for refractory HEA selection for high temperature applications. Owais et al. developed WxTaTiVCr (x = 0.3–0.9) refractory HEA using SPS for radiation resistance applications [64]. The developed refractory HEA and its derivative alloys showed superior RT hardness and compression yield strength of 800 HV and ~2.3 GPa, respectively, which decreased with increasing W-content. To carry this work forward, we studied the HT mechanical properties of W0.5TaTiVCr alloy from 1,000oC to 1,400oC and HT wear behaviour at 400oC, which showed superior compression yield strength from ~400–1100 MPa, and low wear rate of 1.37 x 10-5

mm3/Nm at 400oC, as discussed in Paper III.

Mechanical behaviour of refractory high-entropy films and their nitrides Few works have reported on the development and mechanical properties of refractory high-entropy films (RHEF). Zou et al. developed NbMoTaW RHEF film using direct current (DC)-magnetron co-sputtering of elemental targets [49,65]. The resulting nanocrystalline film showed high micro-pillar compressional strength from ~8–10 GPa to 5 GPa from RT to 600oC, respectively. Similarly, Feng et al. studied the effect of grain size and film thickness on the mechanical properties and reported that NbMoTaW RHEF with grain size of ~10 nm and film thickness of 250 nm showed the highest hardness of ~16 GPa [66]. To carry this concept forward, we developed a single partially sintered CuMoTaWV target through SPS and deposited CuMoTaWV RHEF using DC-magnetron sputtering (Paper II). The resulting film showed low grain size of 18 nm, which in combination with lattice distortion resulted in very high hardness and micro-pillar compressional strength of 19 GPa and 10 GPa, respectively, as demonstrated in Paper II. Fritze et al. studied the effect of deposition temperature on the phase evolution and mechanical properties of HfNbTiVZr RHEF [67]. The deposited film changed from an amorphous phase at RT to a BCC phase at 275oC and then to a BCC + Laves phase at 450oC deposition temperature. The hardness values also increased from 6.5 GPa to 9.2 GPa with increasing temperature. In a recent work, El-Atwani studied the irradiation resistance of nanocrystalline WTaVCr RHEF developed using co-sputtering of elemental targets [21]. The

11

resulting film, after irradiation at RT and 800oC, showed negligible irradiation hardening and no sign of radiation-induced dislocation loops.

Conventional super hard coatings for functional applications, such as nitride coatings for cutting tools, often involve the use of binary, ternary or quaternary compositions [68,69]. To develop nitride films with more enhanced properties, research on HEA nitride films has shown that the use of suitable multi-component elements can increase the hardness and oxidation and wear resistance [48]. Chen et al. were the first to develop FeCoNiCrCuAlMn and FeCoNiCrCuAl0.5 HEA nitride film using reactive sputtering in N2 atmosphere, which showed moderate hardness and electrical resistivity [70]. Following this work, researchers tried to develop HEA nitride films with compositions that are strong nitride formers to obtain nitride films with superior mechanical properties. Huang et al. developed AlCrNbSiTiV HEA nitride film using reactive sputtering to obtain super hard nitride films with hardness values higher than 40 GPa and negligible grain coarsening up to 1,000oC [71]. Following these strategies, we have developed octonary TiVZrNbMoHfTaW RHEF consisting of strong nitride forming elements using reactive magnetron sputtering, which changed from an amorphous phase in metallic film to an FCC phase with increasing N2 content, as discussed in Paper III. We have studied the micro-compression of high-entropy-based thin film metallic glass (TFMG) and its nitride for the first time. The resulting TFMG showed exceptionally high ductility with strains up to ~60% without any fracture and compressional strength of up to ~3 GPa. Similarly, its nitride film showed a high amount of work hardening up to ~30% strain and high compressive strength of up to 10.2 ± 0.4 GPa, and even showed mechanical stability after annealing at 1,000oC. The high-entropy nitride film with 30% RN also showed superior mechanical properties of hardness up to 43.8 ± 3.7 GPa, placing it in the super hard films category [68].

Wear properties of bulk refractory HEAs Friction and wear resistance in different environments, such as high temperature and/or corrosive environments, are essential components of alloy design for functional applications. Most of the research reporting on tribological behaviour of HEAs has been based on transition metal-based HEAs [5,72–75] and its composites

12

[37,76,77]. Fewer works have reported on wear properties of refractory HEAs. Poulia et al. and Mathiou et al. studied the wear behaviour of arc melted MoTaWNbV refractory HEA against steel and alumina couter-balls at RT, and compared the wear rate with Inconel 718 superalloy [78,79]. The resulting wear behaviour showed a wear rate in refractory HEAs two times lower than Inconel 718 alloy. However, high COF in the range of 0.7–0.8 was observed, which can be related to the absence of a lubricating phase or the formation of lubricating oxides in the wear track. Following this work, Mathiou et al. studied the dry sliding behaviour of MoTaNbZrTi refractory HEA against steel and alumina couter-balls, and found the wear resistance to be even higher than MoTaWNbV [80]. Such an enhancement of wear resistance in MoTaNbZrTi has been related to the presence of the dual structure of BCC and HCP, where the BCC phase deforms whilst the HCP phase remains bare during sliding. To carry these concepts forward, we designed a composition of CuMoTaWV with a mixture of FCC and BCC phases using ThermoCalc software, and developed CuMoTaWV refractory HEA using SPS at 1,200oC, followed by studying the tribological behaviour of refractory HEA for the first time from RT to 600oC, as discussed in Paper I. The resulting refractory HEA showed a composite structure with a BCC phase and formation of V-rich zones, where Cu and V showed adaptive wear behaviour at elevated temperatures with the formation of CuO and V2O5, respectively, influenced by the cocktail effect of HEAs.

13

3. RESEARCH OBJECTIVES

The use of HEA’s core effects, as discussed in Chapter 1, towards developing alloys for functional applications are necessary for the advancement of new materials. In this thesis, one of the major objectives was to develop different HEAs that can take advantage of the core effects to enhance the mechanical and tribological properties. A. Studying the cocktail effect for adaptive tribological properties.

In our first work (Paper I), we developed CuMoTaWV refractory HEA with a composite microstructure to give adaptive wear behaviour at different temperatures from RT to 600oC, to utilise the cocktail effect of HEAs. We chose Cu to provide wear resistance at moderate temperatures by forming CuO, Ta, W and V to give high temperature wear resistance through the formation of lubricating TaO, WO3 and V2O5, respectively. The work in Paper I can serve as a good starting point for designing HEA compositions to design alloys that form in-situ composite phases with adaptive tribological properties in different environments for various applications.

14

B. How does the use of single partially sintered target and lattice distortion effect the mechanical properties of thin films?

The HEA film deposition usually involves the use of targets that are either arc melted HEAs or co-sputtered from elemental targets. The use of a single refractory HEA target can be economically unfeasible due to the cost and time related to arc melting. The objective of our work in Paper II and Paper III was to use a partially sintered target to develop RHEF and study the film homogeneity and nanocrystallinity and its effect on mechanical and thermal stability. Through these works, we showed that partially sintered targets could be an economically feasible option to develop HEA films for industrial applications. Furthermore, to utilise the lattice distortion effect of HEA, we studied RHEF films that combine Cu with refractory elements to enhance the mechanical and tribological properties. We observed that the hardness and micro-pillar compressional strength increased to a greater extend as compared to previously reported works on RHEF. Similarly, the configurational entropy and lattice distortion was utilised in octonary refractory film and its nitrides to obtain TFMG, and its nitride film with superior mechanical properties and thermal stability, as discussed in Paper III.

C. Could increasing configurational high-entropy enhance the mechanical properties and thermal stability of high-entropy based TFMG and its nitride films?

Metallic glasses, considered as amorphous metal, are based on the principle of using one principal element to form metallic glass films or bulk metallic glasses (BMGs). The use of multi-principal elements, based on compositions consisting of transition metal and refractory elements, to form high-entropy metallic glasses has been reported earlier [81,82]. High-entropy-based TFMG with high thermal stability has also been reported [83]. However, the micro-compression and the effect of annealing on the mechanical properties of high-entropy TFMG have not to date been reported. In Paper III, we used octonary refractory elements to achieve the high-entropy-based TiNbMoZrHfWVTa TFMG using magnetron

15

sputtering and studied its high temperature stability up to 800oC using in-situ high temperature XRD analysis. Another objective was to study how the increase of configuration entropy and strong bonding between like-elements can impart high mechanical stability to TFMG. To take this concept even further, we studied the thermal stability and mechanical properties of nitride films of the same composition in reactive sputtering with two different RN (10% and 30%). Furthermore, the micro-compression analysis of high-entropy nitride film has been carried out for the first time in this work.

D. High temperature thermal stability of refractory HEAs towards application.

Refractory HEAs are considered to be one possible alloy for irradiation resistance material in fusion energy applications. In Paper IV, we studied the high temperature mechanical and wear properties of W0.5TiTaVCr alloy, which is an HEA derivative of WTiTaVCr refractory HEA. To study the suitability of this alloy in high temperature applications, we carried out high temperature compression tests at 1,000oC, 1,200oC and 1,400oC to study the effect of phases and microstructure on compressional strength. Furthermore, the high temperature tribology of this alloy was carried out at 400oC and the effect of microstructure on wear properties was correlated.

16

17

4. METHODOLOGY

Figure 3. Schematic of alloy and thin film development from powder mixture to sintering using SPS, followed by a tribological and micro-compression test. Adapted from Paper II.

18

Spark plasma sintering (SPS)

The bulk refractory HEAs in this thesis were developed using the powder metallurgy route. The elemental powders were packed in a vinyl box in argon atmosphere, followed by ball milling using zirconia ceramic balls for one hour. The resulting mixed powders were fed into a graphite die and consolidated using spark plasma sintering (SPS, SPS530ET, Dr. Sinter Spark Plasma Sintering System, Fuji Electronic Industrial Co., Ltd., Japan). The detailed sintering profile including heating rates, sintering temperatures and holding times is discussed in the appended papers.

Magnetron sputtering

The partially sintered targets for sputtering deposition with a diameter of 76 mm and a thickness of 3 mm was developed using SPS 530ET (Dr. Sinter Spark Plasma Sintering System, Fuji Electronic Industrial Co., Ltd., Japan), as shown in Figure 4. The details of the target preparation method and sintering temperatures are discussed in the appended papers.

Figure 4, Target prepared at 1,000oC using SPS [84].

19

The RHEF were deposited on silicon substrate for cross-section analysis, nano-indentation hardness measurement, nano-pillar compression testing, Rutherford backscattering analysis (RBS) and X-ray photoelectron spectra (XPS) analysis; and on 304 stainless steel substrate for XRD analysis and tribological testing. Sheet metal substrate of 304 stainless steel with a thickness of 5 mm was cut into 20 x 20 mm sections and diamond polished up to 0.4 µm, followed by cleaning with ethanol in an ultrasonicator for 30 minutes and dried in an oven at 80oC for 30 minutes. Silicon substrate with a thickness of 2 mm and dimensions of 5 x 5 mm were used after rinsing with ethanol and distilled water, followed by drying in an oven at 70oC. The parameters for film deposition are discussed in the appended papers. Microhardness measurement

Microhardness measurements were performed using Vickers microhardness (Matsuzawa, MXT-CX) equipped with a diamond indenter at 200 g load. The samples were diamond polished up to 0.4 µm to get a smooth surface for hardness measurement. At least eight indentations were performed at different locations of interest. Nano-indentation

In Paper II and Paper III, hardness measurements were performed using nano-indenter (Micro Materials, UK) at 3-10 mN load. The nano-indentation tests were performed at loading, unloading and duel time of 25 seconds, 20 seconds and 10 seconds, respectively. Nano-indentation measurements were performed to obtain force-displacement curves at 12 different locations and the average hardness and Young’s modulus were reported in the paper. Nano-pillar compression tests

In Paper II and Paper III, nano-pillars were developed using focused-ion beam (FIB) for compression tests. For each pillar, firstly, a ring was etched using high current (1 nA) with the outer and inner diameter set to 30 µm and 8 µm, respectively. Secondly, fine etching of a pillar with current lower than 320 pA was used to mill 440–800 nm

20

diameter pillars. The pillars were then compressed using an Anton Paar ultra-nano-indentation tester in the load control mode with a maximum force set to 3 mN, using a flat punch with a diameter of 20 µm. The loading and unloading rates were set to 1 mN/min and 3 mN/min, respectively. The data acquisition rate was set to 50 Hz. The value of the compression strength was determined as the engineering strain at which 0.2% plastic deformation occurs. Young’s modulus was determined from the linear fit to the data for which engineering stress was lower than 0.6 compression strength. Engineering stress was determined by dividing the force measured by nano-indentation tester over the pillars’ cross-section area. Hence, we measured the pillars’ diameters before and after the compression test with the use of SEM. Furthermore, in order to determine engineering strain, the ratio of displacement obtained from nano-indentation to the initial height of a pillar measured by an atomic force microscope (AFM) was obtained. Tribological studies

Tribological tests in Paper I, Paper II and Paper III were carried out using a universal tribometer (Rtec Instruments, San Jose, USA) equipped with a normal load (FN) sensor in the range of 1–100 N and a frictional force (Fx) sensor in the range of 1–50 N.

High temperature tribology

For Paper I, Paper II and Paper IV, a high temperature furnace with asbestos lining was used to perform high temperature tribological tests. A ball-on-disc sliding test was performed, with dimensions of 12 mm diameter and 5 mm thickness. The tribological tests were performed at RT to 600oC, 300 oC and 400oC in Paper I, Paper II and Paper IV, respectively. The details of the type of counter-balls, normal loads and sliding distance can be found in the appended papers. The counter-balls and specimens were brought in contact after the desired test temperature was reached. For repeatability of the tribotests, three tests/conditions were conducted and the average COF and wear rate were reported. The average depth of the resulting wear track was measured using optical profilometry (Wyko) to calculate the specific wear rate at each temperature. At least eight wear track depths were measured for each tribotest.

21

The wear rate, expressed as mm3/Nm, was measured by dividing wear volume by normal load and sliding distance.

Room temperature tribotest

For Paper II, a RT tribotest of CuMoTaWV RHEF was performed in the ball-on-disc setup at 1 N normal load and a sliding speed of 0.1 m/s. A counter-ball of E52100 alloy steel (Grade 25, 700-880 HV) with a diameter of 6.3 mm was used after cleaning with ethanol in a ultrasonicator machine for 10 minutes, followed by drying in an oven at 80oC for 30 minutes. The average depth of wear was measured using optical profilometry (Wyko) to calculate the wear rate, expressed in mm3/Nm. Scanning electron microscopy (SEM)

SEM analysis was performed using a JSM-IT300 (JEOL, Tokyo, Japan) and Magellan 400 XHR-SEM (FEI Company, Eindhoven, Netherlands), based on the requirement of magnification. In Paper I, Paper II and IV, a JSM-IT300 was used to characterise the microstructure of the alloys and the resulting wear tracks after high temperature tribotests. The accelerating voltage for microstructural analysis and wear track analysis from the tribotests was set to 15 kV and 10 kV, respectively. In Paper II and Paper III, a Magellon 400 was used to characterise the coating surface and cross-section morphology of the films. XPS measurements

X-ray photoelectron spectra (XPS) were recorded using a PerkinElmer PHI 5600 ci spectrometer with a standard Al−Kα source (1486.6 eV) working at 250 W. The working pressure was set to 5 × 10−8 Pa. The spectrometer was calibrated by assuming the binding energy (BE) of the Au 4f7/2 line to be 84.0 eV with respect to the Fermi level. Extended spectra (surveys) were collected in the range 0−1300 eV (187.85 eV pass energy, 0.5 eV step, 0.025 s·step−1). Detailed spectra were recorded for the following regions: V 2p, Mo 3d, Ta 4f, W 4f, Cu 2p and O1s (23.5 eV pass energy, 0.1 eV step, 0.2 s·step−1). The atomic percentage, after a Shirley type background subtraction, was evaluated by using the PHI sensitivity factors. The sample was

22

analysed before and after 2 minutes of Ar+ sputtering at 3.5 keV with an argon partial pressure of 5 x 10-8 mbar and a rastered area of 2.5 x 2.5 mm.

Rutherford backscattering spectrometry

In Paper II, Rutherford Backscattering Spectrometry (RBS) with a 1.8 or 2.0 MeV 4He+ beam in IBM geometry was used to measure the composition homogeneity in the CuMoTaWV RHEF. Atomic force microscopy (AFM)

In Paper II, the AFM analysis was used to study the surface morphology and surface roughness of CuMoTaWV RHEF. The AFM measurements were performed using ambient conditions with an NTEGRA AFM (NT-MDT) in semi-contact mode using a polysilicon lever, monocrystal silicon probe (HA_NC series) with a tip height of 10 μm, nominal tip radius less than 10 nm, and a measured resonance frequency of 240.3 Hz. DFT calculations

In Paper II and Paper III, density-functional theory (DFT) was applied to predict the lattice structure and mechanical properties of CuMoTaWV RHEF and 30% RN TiNbMoZrHfWVTa high entropy nitride film. Based on experimental XRD analysis, a DFT calculation was used to compare the theoretical and experimental peak positions (2θ) of different planes.

23

5. SUMMARY OF PUBLISHED WORK

Paper I High temperature tribology of CuMoTaWV high-entropy alloy S. Alvi and F. Akhtar Wear (2019) In this work, an equi-atomic CuMoTaWV refractory HEA was developed using spark plasma sintering (SPS) from an elemental powder mixture at 1,400oC. The objective of this paper was to use the cocktail effect of HEAs to design an alloy for adaptive tribological behaviour. Furthermore, how the microstructural changes at different temperature effects the tribological properties was studied. The resulting sintered alloy showed a composite structure with the formation of a BCC solid solution (Figure 5a) along with V-rich phases with an average hardness of 600 HV and 900 HV, respectively. Room temperature (RT) ball-on-disc sliding wear against alloy steel at 5 N load showed negligible wear rate. Thus, Si3N4 as a counter-ball was used against sintered CuMoTaWV refractory HEA in sliding motion to induce more wear and study the effect of microstructure and phases on wear properties. High temperature tribological studies of the sintered alloy showed wear properties specific to test temperatures, as shown in Figure 5b. The tribological tests from RT to 600oC showed an increasing average COF from RT to 400oC, which then decreased at 600oC. The wear rate was found to be lower at RT and 400oC, and slightly higher at 200oC and 600oC.

24

Figure 5. a) XRD analysis and b) tribological properties of CuMoTaWV HEA [85].

The wear surfaces were analysed to elucidate the wear mechanism at each test temperature. The wear of CuMoTaWV alloy was governed by adhesive wear at RT, adhesive with mild abrasion wear at 200oC and oxidative wear at 400oC and 600oC. CuMoTaWV alloy showed adaptive wear behaviour at test temperatures of 400oC and 600oC. At 400oC, the adaptive behaviour was found to be due to the formation of CuO, resulting in reducing the wear, while at 600oC the transformation of V-rich zones to elongated magneli phases of V2O5 reduced the COF to 0.54. The results suggest a promising utilisation of the cocktail effect to develop HEA compositions with in-situ composite phases that can be beneficial to adaptive tribological behaviour.

25

Paper II Synthesis and mechanical characterisation of CuMoTaWV refractory high-entropy film by magnetron sputtering S. Alvi, D. Jarzabek, M. Kohan, D. Hedman, P. Jenczyk, Marta. Natile, A. Vomiero ane F. Akhtar ACS Applied Materials & Interfaces 12.18 (2020): 21070–21079 This work involves the development of CuMoTaWV RHEF using DC-magnetron sputtering. The objective was to see the effect of a partially sintered single target on the nanocrystallinity and mechanical properties of RHEF. Furthermore, how lattice distortion can be utilised to develop HEA films with superior mechanical properties.

The deposited CuMoTaWV RHEF showed the formation of a BCC solid solution with a lattice parameter of 3.18 Å, which was similar to DFT optimised SQS (3.16 Å), as shown in Figure 6a. The deposited film showed a needle-like morphology with surface roughness of (Sa) of 2.5 nm, and a dense textured cross-sectional morphology, as shown in Figure 6b. The EDS area analysis of the film surface showed uniform distribution of elements, except for Cu which was present in a lower amount.

Figure 6.a) XRD analysis and b) surface, cross-section morphology, elemental EDS map and AFM analysis of surface of CuMoTaWV RHEF [84].

26

Nano-pillars from CuMoTaWV RHEF showed an average compressional strength and Young’s modulus of 10.7 ± 0.8 GPa and 196 ± 10 GPa, respectively, as shown in Figure 7a. The hardness measurements showed an average hardness and Young’s modulus of 19.5 ± 2.3 GPa and 259.3 ± 19.2 GPa, respectively (Figure 7b). The hardness and compressional strength values were found to be one of the highest reported thus far for RHEF. Such a high hardness and compressional strength is due to the nanocrystallinity and grain boundary strengthening of the films. Tribological performance of CuMoTaWV RHEF deposited on 304 stainless steel also showed low COF and wear rate. These results showed that the use of a partially sintered target could be a viable option for reducing the cost and time of single target development, and developing films with nanocrystallinity. Furthermore, the use of the lattice distortion effect and grain boundary strengthening can be utilised for developing films with improved mechanical properties.

Figure 7. Nano-mechanical studies of CuMoTaWV RHEF showing a) nano-pillar after compression, b) stress-strain curve after compression, c) comparison of micro-compressed pillars and d) comparison of hardness to that reported in literature [84].

27

Paper III Synthesis, nano-mechanical characterization and high temperature performance of amorphous TiNbMoZrHfWVTa and its nitride high-entropy film by magnetron sputtering S. Alvi, D. Jarzabek, M. Milczarek and F. Akhtar (To be submitted)

To explore the thermal and mechanical stability of high-entropy TFMG and its nitride films driven by the high-entropy effect, octonary TiNbMoZrHfWVTa high-entropy films and its nitride were synthesised through magnetron sputtering using a single partially sintered target. The resulting film showed an amorphous structure at 0% RN and 10% RN, followed by changing to an FCC solid solution at 30% RN, as shown in Figures 10 and 11.

Figure 10. XRD diffractograms of TiNbMoZrHfWVTa high-entropy films with 0% RN, 10% RN and 30% RN, and DFT optimised.

The octonary high-entropy TFMG showed high hardness and micro-compression strength of 7.8 GPa and 2.7 GPa, respectively, as shown in Figure 12. Furthermore, the TFMG showed extremely high ductile behaviour with no fracture even after compressing to ~60% strain. The in-situ high temperature XRD analysis showed thermal stability of high-entropy TFMG to be stable up to 750oC, after which it changed to a crystalline phase at 800oC. Such high thermal stability of TFMG has been attributed to the high-entropy effect and sluggish diffusion, where the presence

28

of highly concentrated refractory elements make the amorphous films resistant to diffusion controlled phase transformation. Furthermore, the mechanical properties of the high-entropy TFMG film after annealing was enhanced with a micro-compression strength and Young’s modulus of 4.3 ± 0.2 GPa and 77.9 ± 4.3 GPa, respectively.

Figure 11. SEM surface and cross-sectional morphology of TiNbMoZrHfWVTa films deposited at a) 0% RN, b) 10% RN, and c) 30% RN.

The mechanical properties of the nitride films were found to be directly related to the crystal structure, where amorphous nitride film showed a hardness and compressional strength of 21.5 GPa and 6.14 GPa, and increased to 47.7 GPa and 10.2 GPa, respectively, in FCC nitride film, as shown in Figure 12. The thermal stability of 10% RN high-entropy nitride films were found to be stable up to 750oC, after which it converts to an FCC solid solution along with minor phases of oxides and remains stable up to 1,000oC, whereas 30% RN nitride film with and FCC solid solution

29

structure was found to be stable up to 950oC, after which it delaminated from the substrate.

Figure 12. a) Micro-compression analysis and b) nano-indentation analysis of TiNbMoZrHfWVTa high-entropy TFMG and its nitride films.

This work demonstrates that the use of HEA compositions with increased configuration entropy and strong nitride forming elements can enhance the TFMG stability and yield nitride films with super hard mechanical properties.

30

31

Paper IV High temperature performance of W0.5(TaTiVCr)0.5 high-entropy based material S. Alvi, O. A. Waseem and F. Akhtar Submitted to Metals Refractory high-entropy alloys have been considered as a potential for plasma facing materials for future fusion energy applications. In this work, we studied the high temperature mechanical properties of HEA-based W0.5(TaTiVCr)0.5 alloy. The HEA-based alloy was developed using SPS at 1,600oC. The resulting consolidated alloy showed a formation of BCC and TiC phases. The microstructure consisted of composite phases of W, HEA and TiC phases. The high temperature phase stability and mechanical performance of W0.5(TaTiVCr)0.5 alloy was studied up to 1,400oC using in-situ high temperature XRD analysis and compression tests. Furthermore, high temperature wear tests were carried out at 400oC against alumina couter-balls. The BCC solid solution structure was found to be stable up to 1,400oC, as shown in Figure 13a–b. However, formation of TiO2 was observed after in-situ high temperature XRD analysis at 1,200oC, which was related to the low melting point of Ti, leading to its diffusion to the surface to form oxide, as shown in Figure 13c.

Figure 13. a) In-situ high temperature XRD analysis of W0.5(TaTiVCr)0.5 alloy, b) magnified image of XRD analysis plot after HT XRD analysis and c) SEM microstructure of surface after HT XRD analysis.

32

The high temperature compression tests showed high yield strength of 1136 ± 40 MPa, 830 ± 60 MPa and 425 ± 15 MPa at 1,000oC, 1,200oC and 1,400oC, respectively, as shown in Figure 14a. The resulting high yield strengths directly responds to the solid solution strengthening of the HEA phase and grain-boundary strengthening from the TiC phase. The formation of the in-situ TiC phase along with the HEA phase was found to be beneficial in sliding wear tests at 400oC, imparting a low wear rate of 1.37 x 10-5 mm3/Nm, as shown in Figure 14b.

Figure 14. a) High temperature compression stress-strain plots (left) and values (right) and b) SEM surface morphology after sliding wear at 400oC of W0.5(TaTiVCr)0.5 alloy.

33

6. FUTURE DIRECTIONS

34

35

The progress in research on HEAs has led to a paradigm shift towards pushing the boundaries of new alloy development for various applications. In this work, different core effects of HEAs have been utilised to enhance the thermal stability and mechanical properties of refractory HEAs. We have shown that the use of the cocktail effect can be beneficial towards the formation of in-situ composite phases for enhanced tribological properties at different temperatures in air environment. However, the formation of in-situ phases in HEA compositions focused on tribological properties in other environments, such as vacuum, dry air and corrosive environments, needs to be carried out. For example, the use of high-entropy sulfides can be beneficial for tribology in vacuum environment, the use of Ag, Au or Pb can be beneficial in air environment for high temperatures, and a system of composition that combines sulfides, Ag/Au and oxides can be beneficial for tribology in wide temperature ranges (RT–1,000oC).

Secondly, the reduction in cost and time for target preparation with the use of partially sintered single targets and its enhancement of nanocrystallinity in the RHEF have in this work been found to beneficial. Furthermore, we have reported that an increase in lattice distortion can enhance the mechanical properties of the RHEF as well. Future work can be directed towards studying the erosive wear resistance of CuMoTaWV RHEF, which was found to have enhanced mechanical properties. Furthermore, TEM analysis can be carried out for compressed pillars of CuMoTaWV RHEF to observe how the lattice structure evolves with micro-compression.

The increase of configurational entropy with octonary refractory elements has been found to provide high-entropy TFMG and its nitride films with enhanced mechanical properties. The octonary TFMG showed extremely high thermal stability, ductility and compressional strength. Future work can be focused towards studying the in-situ high temperature TEM analysis of the octonary TFMG to observe the amorphous phase evolution, interlayer diffusion barrier properties for Si/Cu contacts, electrical resistivity and magnetic properties at different temperatures. Furthermore, octonary TFMG can be combined with other films in nanolaminates to enhance its mechanical properties. Future work on the octonary nitride films with extremely enhanced thermal stability and mechanical properties can be studied for high temperature

36

applications, such as cutting tools, radiation resistance and thermoreflectance transducers. Furthermore, the structural characterisation of compressed pillars at different temperature can be studied using TEM to observe the mechanisms of deformation governing such high mechanical properties.

Lastly, refractory HEAs are a potential for plasma facing material in fusion energy applications. Our work on HEA-derivative W0.5(TaTiVCr)0.5 alloy has shown high thermal stability and mechanical properties at temperatures up to 1,400oC. Thus, future work can be carried out on radiation studies of this alloy composition, followed by studying the structural and mechanical property changes imparted by radiation.

37

REFERENCES

[1] C.S. Smith, Four Outstanding Researches in Metallurgical History, American Society for Testing and Materials, Baltimore MD, 1963. https://books.google.se/books?id=0eWaGQAACAAJ.

[2] B. Cantor, I.T.H. Chang, P. Knight, A.J.B. Vincent, Microstructural development in equiatomic multicomponent alloys, Mater. Sci. Eng. A. 375–377 (2004) 213–218. doi:10.1016/j.msea.2003.10.257.

[3] P. Huang, J. Yeh, T.-T. Shun, S.-K. Chen, Multi-Principal-Element Alloys with Improved Oxidation and Wear Resistance for Thermal Spray Coating, Adv. Eng. Mater. 6 (2004) 74–78. doi:10.1002/adem.200300507.

[4] J.W. Yeh, S.K. Chen, S.J. Lin, J.Y. Gan, T.S. Chin, T.T. Shun, C.H. Tsau, S.Y. Chang, Nanostructured high-entropy alloys with multiple principal elements: Novel alloy design concepts and outcomes, Adv. Eng. Mater. 6 (2004) 299-303+274. doi:10.1002/adem.200300567.

[5] C. Hsu, J. Yeh, S. Chen, T. Shun, Wear Resistance and High-Temperature Compression Strength of Fcc CuCoNiCrAl 0 . 5 Fe Alloy with Boron Addition, Metall. Mater. Trans. A. 35A (2004) 1465–1469.

[6] S. Ranganathan, Alloyed pleasures : Multimetallic cocktails, Curr. Sci. 85 (2003) 1404–1406.

[7] J.W. Yeh, S.K. Chen, S.J. Lin, J.Y. Gan, T.S. Chin, T.T. Shun, C.H. Tsau, S.Y. Chang, Nanostructured high-entropy alloys with multiple principal elements: Novel alloy design concepts and outcomes, Adv. Eng. Mater. 6 (2004) 299-303+274. doi:10.1002/adem.200300567.

[8] B. Fultz, Vibrational thermodynamics of materials, Prog. Mater. Sci. 55 (2010) 247–352. doi:10.1016/j.pmatsci.2009.05.002.

[9] R.A. Swalin, Thermodynamics of Solids, John Wiley, Toronto, ON, 1972.

[10] D.R. Gaskell, Introduction To The Thermodynamics Of Materials, Taylor and Francis, London, UK, 1995.

[11] J.W. Yeh, Recent progress in high-entropy alloys, Ann. Chim. Sci. Des Mater. 31 (2006) 633–648. doi:10.3166/acsm.31.633-648.

[12] J.W. Yeh, Alloy design strategies and future trends in high-entropy alloys, Jom. 65 (2013) 1759–1771. doi:10.1007/s11837-013-0761-6.

38

[13] K.Y. Tsai, M.H. Tsai, J.W. Yeh, Sluggish diffusion in Co-Cr-Fe-Mn-Ni high-entropy alloys, Acta Mater. 61 (2013) 4887–4897. doi:10.1016/j.actamat.2013.04.058.

[14] W.H. Liu, Y. Wu, J.Y. He, T.G. Nieh, Z.P. Lu, Grain growth and the Hall-Petch relationship in a high-entropy FeCrNiCoMn alloy, Scr. Mater. 68 (2013) 526–529. doi:10.1016/j.scriptamat.2012.12.002.

[15] T.K. Tsao, A.C. Yeh, C.M. Kuo, K. Kakehi, H. Murakami, J.W. Yeh, S.R. Jian, The High Temperature Tensile and Creep Behaviors of High Entropy Superalloy, Sci. Rep. 7 (2017) 1–9. doi:10.1038/s41598-017-13026-7.

[16] V.H. Hammond, M.A. Atwater, K.A. Darling, H.Q. Nguyen, L.J. Kecskes, Equal-Channel Angular Extrusion of a Low-Density High-Entropy Alloy Produced by High-Energy Cryogenic Mechanical Alloying, Jom. 66 (2014) 2021–2029. doi:10.1007/s11837-014-1113-x.

[17] O.N. Senkov, J.P. Couzinie, S.I. Rao, V. Soni, R. Banerjee, Temperature dependent deformation behavior and strengthening mechanisms in a low density refractory high entropy alloy Al10Nb15Ta5Ti30Zr40, Materialia. 9 (2020) 100627. doi:10.1016/j.mtla.2020.100627.

[18] O.A. Waseem, H.J. Ryu, Combinatorial development of the low-density high-entropy alloy Al10Cr20Mo20Nb20Ti20Zr10 having gigapascal strength at 1000 °C, J. Alloys Compd. 845 (2020) 155700. doi:10.1016/j.jallcom.2020.155700.

[19] C. Lu, L. Niu, N. Chen, K. Jin, T. Yang, P. Xiu, Y. Zhang, F. Gao, H. Bei, S. Shi, M.R. He, I.M. Robertson, W.J. Weber, L. Wang, Enhancing radiation tolerance by controlling defect mobility and migration pathways in multicomponent single-phase alloys, Nat. Commun. 7 (2016) 1–8. doi:10.1038/ncomms13564.

[20] O.A. Waseem, H.J. Ryu, Powder Metallurgy Processing of a Wx TaTiVCr High-Entropy Alloy and Its Derivative Alloys for Fusion Material Applications, Sci. Rep. 7 (2017). doi:10.1038/s41598-017-02168-3.

[21] O. El-Atwani, N. Li, M. Li, A. Devaraj, J.K.S. Baldwin, M.M. Schneider, D. Sobieraj, J.S. Wróbel, D. Nguyen-Manh, S.A. Maloy, E. Martinez, Outstanding radiation resistance of tungsten-based high-entropy alloys, Sci. Adv. 5 (2019) 1–10. doi:10.1126/sciadv.aav2002.

[22] H.P. Chou, Y.S. Chang, S.K. Chen, J.W. Yeh, Microstructure, thermophysical and electrical properties in AlxCoCrFeNi (0 ≤ x ≤2) high-entropy alloys, Mater. Sci. Eng. B Solid-State Mater. Adv. Technol. 163

39

(2009) 184–189. doi:10.1016/j.mseb.2009.05.024.

[23] Y. Zhang, T. Zuo, Y. Cheng, P.K. Liaw, High-entropy Alloys with High Saturation Magnetization, Electrical Resistivity and Malleability, Sci. Rep. 3 (2013) 1455. doi:10.1038/srep01455.

[24] W. Wang, B. Li, S. Zhai, J. Xu, Z. Niu, J. Xu, Y. Wang, Alloying Behavior and Properties of FeSiBAlNiCox High Entropy Alloys Fabricated by Mechanical Alloying and Spark Plasma Sintering, Met. Mater. Int. 24 (2018) 1112–1119. doi:10.1007/s12540-018-0047-1.

[25] E. Holmström, R. Lizárraga, D. Linder, A. Salmasi, W. Wang, B. Kaplan, H. Mao, H. Larsson, L. Vitos, High entropy alloys : Substituting for cobalt in cutting edge technology, Appl. Mater. Today. 12 (2018) 322–329. doi:10.1016/j.apmt.2018.07.001.

[26] R. Zhang, F. Gucci, H. Zhu, K. Chen, M.J. Reece, Data-Driven Design of Ecofriendly Thermoelectric High-Entropy Sulfides, 13033 (2018). doi:10.1021/acs.inorgchem.8b02379.

[27] M. Sahlberg, D. Karlsson, C. Zlotea, U. Jansson, Superior hydrogen storage in high entropy alloys, Sci. Rep. 6 (2016) 1–6. doi:10.1038/srep36770.

[28] Y.F. Ye, Q. Wang, J. Lu, C.T. Liu, Y. Yang, High-entropy alloy: challenges and prospects, Mater. Today. 19 (2016) 349–362. doi:10.1016/j.mattod.2015.11.026.

[29] O.N. Senkov, G.B. Wilks, D.B. Miracle, C.P. Chuang, P.K. Liaw, Refractory high-entropy alloys, Intermetallics. 18 (2010) 1758–1765. doi:10.1016/j.intermet.2010.05.014.

[30] O.N. Senkov, G.B. Wilks, J.M. Scott, D.B. Miracle, Mechanical properties of Nb25Mo25Ta25W25 and V20Nb20Mo20Ta20W20 refractory high entropy alloy, Intermetallics. 19 (2011) 698–706. doi:10.1016/j.intermet.2011.01.004.

[31] O.N. Senkov, D.B. Miracle, K.J. Chaput, J.P. Couzinie, Development and exploration of refractory high entropy alloys - A review, J. Mater. Res. 33 (2018) 3092–3128. doi:10.1557/jmr.2018.153.

[32] J.P. Couzinié, G. Dirras, L. Perrière, T. Chauveau, E. Leroy, Y. Champion, I. Guillot, Microstructure of a near-equimolar refractory high-entropy alloy, Mater. Lett. 126 (2014) 285–287. doi:10.1016/j.matlet.2014.04.062.

[33] O.N. Senkov, S. V. Senkova, C. Woodward, D.B. Miracle, Low-density, refractory multi-principal element alloys of the Cr-Nb-Ti-V-Zr system:

40

Microstructure and phase analysis, Acta Mater. 61 (2013) 1545–1557. doi:10.1016/j.actamat.2012.11.032.

[34] O.N. Senkov, S. V. Senkova, C. Woodward, Effect of aluminum on the microstructure and properties of two refractory high-entropy alloys, Acta Mater. 68 (2014) 214–228. doi:10.1016/j.actamat.2014.01.029.

[35] S. Maiti, W. Steurer, Structural-disorder and its effect on mechanical properties in single-phase TaNbHfZr high-entropy alloy, Acta Mater. 106 (2016) 87–97. doi:10.1016/j.actamat.2016.01.018.

[36] A.S. Sharma, S. Yadav, K. Biswas, B. Basu, High-entropy alloys and metallic nanocomposites: Processing challenges, microstructure development and property enhancement, Mater. Sci. Eng. R Reports. 131 (2018) 1–42. doi:10.1016/j.mser.2018.04.003.

[37] A. Zhang, J. Han, B. Su, J. Meng, A novel CoCrFeNi high entropy alloy matrix self-lubricating composite, J. Alloys Compd. 725 (2017) 700–710. doi:10.1016/j.jallcom.2017.07.197.

[38] Q. Liu, G. Wang, X. Sui, Y. Liu, X. Li, J. Yang, Microstructure and mechanical properties of ultra-fine grained MoNbTaTiV refractory high-entropy alloy fabricated by spark plasma sintering, J. Mater. Sci. Technol. 35 (2019) 2600–2607. doi:10.1016/j.jmst.2019.07.013.

[39] C. Han, Q. Fang, Y. Shi, S.B. Tor, C.K. Chua, K. Zhou, Recent Advances on High-Entropy Alloys for 3D Printing, Adv. Mater. 32 (2020) 1–41. doi:10.1002/adma.201903855.

[40] P. Ding, A. Mao, X. Zhang, X. Jin, B. Wang, M. Liu, X. Gu, Preparation, characterization and properties of multicomponent AlCoCrFeNi2.1 powder by gas atomization method, J. Alloys Compd. 721 (2017) 609–614. doi:10.1016/j.jallcom.2017.06.020.

[41] D. Yim, M.J. Jang, J.W. Bae, J. Moon, C.H. Lee, S.J. Hong, S.I. Hong, H.S. Kim, Compaction behavior of water-atomized CoCrFeMnNi high-entropy alloy powders, Mater. Chem. Phys. 210 (2018) 95–102. doi:10.1016/j.matchemphys.2017.06.013.

[42] R.F. Zhao, B. Ren, G.P. Zhang, Z.X. Liu, J. jian Zhang, Effect of Co content on the phase transition and magnetic properties of CoxCrCuFeMnNi high-entropy alloy powders, J. Magn. Magn. Mater. 468 (2018) 14–24. doi:10.1016/j.jmmm.2018.07.072.

[43] H. Dobbelstein, E.L. Gurevich, E.P. George, A. Ostendorf, G. Laplanche,

41

Laser metal deposition of a refractory TiZrNbHfTa high-entropy alloy, Addit. Manuf. 24 (2018) 386–390. doi:10.1016/j.addma.2018.10.008.

[44] H. Dobbelstein, M. Thiele, E.L. Gurevich, E.P. George, A. Ostendorf, Direct metal deposition of refractory high entropy alloy MoNbTaW, Phys. Procedia. 83 (2016) 624–633. doi:10.1016/j.phpro.2016.08.065.

[45] H. Zhang, W. Xu, Y. Xu, Z. Lu, D. Li, The thermal-mechanical behavior of WTaMoNb high-entropy alloy via selective laser melting (SLM): experiment and simulation, Int. J. Adv. Manuf. Technol. 96 (2018) 461–474. doi:10.1007/s00170-017-1331-9.

[46] H. Zhang, Y. Zhao, S. Huang, S. Zhu, F. Wang, D. Li, Manufacturing and analysis of high-performance refractory high-entropy alloy via selective laser melting (SLM), Materials (Basel). 12 (2019). doi:10.3390/ma12050720.

[47] Q. Xing, J. Ma, C. Wang, Y. Zhang, High-Throughput Screening Solar-Thermal Conversion Films in a Pseudobinary (Cr, Fe, V)–(Ta, W) System, ACS Comb. Sci. 20 (2018) 602–610. doi:10.1021/acscombsci.8b00055.

[48] W. Li, P. Liu, P.K. Liaw, Microstructures and properties of high-entropy alloy films and coatings: A review, Mater. Res. Lett. 6 (2018) 199–229. doi:10.1080/21663831.2018.1434248.

[49] Y. Zou, H. Ma, R. Spolenak, Ultrastrong ductile and stable high-entropy alloys at small scales, Nat. Commun. 6 (2015) 1–8. doi:10.1038/ncomms8748.

[50] T.K. Chen, M.S. Wong, T.T. Shun, J.W. Yeh, Nanostructured nitride films of multi-element high-entropy alloys by reactive DC sputtering, Surf. Coatings Technol. 200 (2005) 1361–1365. doi:10.1016/j.surfcoat.2005.08.081.

[51] V. Braic, A. Vladescu, M. Balaceanu, C.R. Luculescu, M. Braic, Nanostructured multi-element (TiZrNbHfTa)N and (TiZrNbHfTa)C hard coatings, Surf. Coatings Technol. 211 (2012) 117–121. doi:10.1016/j.surfcoat.2011.09.033.

[52] M.I. Lin, M.H. Tsai, W.J. Shen, J.W. Yeh, Evolution of structure and properties of multi-component (AlCrTaTiZr)Ox films, Thin Solid Films. 518 (2010) 2732–2737. doi:10.1016/j.tsf.2009.10.142.

[53] O.N. Senkov, J.M. Scott, S. V. Senkova, D.B. Miracle, C.F. Woodward, Microstructure and room temperature properties of a high-entropy

42

TaNbHfZrTi alloy, J. Alloys Compd. 509 (2011) 6043–6048. doi:10.1016/j.jallcom.2011.02.171.

[54] Z.D. Han, H.W. Luan, X. Liu, N. Chen, X.Y. Li, Y. Shao, K.F. Yao, Microstructures and mechanical properties of TixNbMoTaW refractory high-entropy alloys, Mater. Sci. Eng. A. 712 (2018) 380–385. doi:10.1016/j.msea.2017.12.004.

[55] Y. Zou, S. Maiti, W. Steurer, R. Spolenak, Size-dependent plasticity in an Nb25Mo25Ta 25W25 refractory high-entropy alloy, Acta Mater. 65 (2014) 85–97. doi:10.1016/j.actamat.2013.11.049.

[56] Y. Zou, P. Okle, H. Yu, T. Sumigawa, T. Kitamura, S. Maiti, W. Steurer, R. Spolenak, Fracture properties of a refractory high-entropy alloy: In situ micro-cantilever and atom probe tomography studies, Scr. Mater. 128 (2017) 95–99. doi:10.1016/j.scriptamat.2016.09.036.

[57] N.N. Guo, L. Wang, L.S. Luo, X.Z. Li, R.R. Chen, Y.Q. Su, J.J. Guo, H.Z. Fu, Microstructure and mechanical properties of in-situ MC-carbide particulates-reinforced refractory high-entropy Mo0.5NbHf0.5ZrTi matrix alloy composite, Intermetallics. 69 (2016) 74–77. doi:10.1016/j.intermet.2015.09.011.

[58] N.N. Guo, L. Wang, L.S. Luo, X.Z. Li, R.R. Chen, Y.Q. Su, J.J. Guo, H.Z. Fu, Microstructure and mechanical properties of refractory high entropy (Mo0.5NbHf0.5ZrTi) BCC/M5Si3 in-situ compound, J. Alloys Compd. 660 (2016) 197–203. doi:10.1016/j.jallcom.2015.11.091.

[59] Y. Zhang, Y. Liu, Y. Li, X. Chen, H. Zhang, Microstructure and mechanical properties of a refractory HfNbTiVSi0.5 high-entropy alloy composite, Mater. Lett. 174 (2016) 82–85. doi:10.1016/j.matlet.2016.03.092.

[60] O.N. Senkov, S.L. Semiatin, Microstructure and properties of a refractory high-entropy alloy after cold working, J. Alloys Compd. 649 (2015) 1110–1123. doi:10.1016/j.jallcom.2015.07.209.

[61] B. Schuh, B. Völker, J. Todt, N. Schell, L. Perrière, J. Li, J.P. Couzinié, A. Hohenwarter, Thermodynamic instability of a nanocrystalline, single-phase TiZrNbHfTa alloy and its impact on the mechanical properties, Acta Mater. 142 (2018) 201–212. doi:10.1016/j.actamat.2017.09.035.

[62] J. Pan, T. Dai, T. Lu, X. Ni, J. Dai, M. Li, Microstructure and mechanical properties of Nb25Mo25Ta25W25 and Ti8Nb23Mo23Ta23W23 high entropy alloys prepared by mechanical alloying and spark plasma sintering, Mater. Sci. Eng. A. 738 (2018) 362–366. doi:10.1016/j.msea.2018.09.089.

43

[63] C.C. Juan, M.H. Tsai, C.W. Tsai, C.M. Lin, W.R. Wang, C.C. Yang, S.K. Chen, S.J. Lin, J.W. Yeh, Enhanced mechanical properties of HfMoTaTiZr and HfMoNbTaTiZr refractory high-entropy alloys, Intermetallics. 62 (2015) 76–83. doi:10.1016/j.intermet.2015.03.013.

[64] O.A. Waseem, H.J. Ryu, Powder Metallurgy Processing of a WxTaTiVCr High-Entropy Alloy and Its Derivative Alloys for Fusion Material Applications, Sci. Rep. 7 (2017) 1926. doi:10.1038/s41598-017-02168-3.

[65] Y. Zou, J.M. Wheeler, H. Ma, P. Okle, R. Spolenak, Nanocrystalline High-Entropy Alloys: A New Paradigm in High-Temperature Strength and Stability, Nano Lett. 17 (2017) 1569–1574. doi:10.1021/acs.nanolett.6b04716.

[66] X.B. Feng, J.Y. Zhang, Y.Q. Wang, Z.Q. Hou, K. Wu, G. Liu, J. Sun, Size effects on the mechanical properties of nanocrystalline NbMoTaW refractory high entropy alloy thin films, Int. J. Plast. 95 (2017) 264–277. doi:10.1016/j.ijplas.2017.04.013.

[67] S. Fritze, C.M. Koller, L. Von Fieandt, P. Malinovskis, K. Johansson, E. Lewin, P.H. Mayrhofer, U. Jansson, Influence of Deposition Temperature on the Phase Evolution of HfNbTiVZr High-Entropy Thin Films, (2019) 10–17. doi:10.3390/ma12040587.

[68] Y.-W. Chung, W.D. Sproul, Superhard Coating Materials, MRS Bull. 28 (2003) 164–168. doi:10.1557/mrs2003.56.

[69] K. V. Chauhan, S.K. Rawal, A Review Paper on Tribological and Mechanical Properties of Ternary Nitride based Coatings, Procedia Technol. 14 (2014) 430–437. doi:10.1016/j.protcy.2014.08.055.

[70] T.K. Chen, M.S. Wong, T.T. Shun, J.W. Yeh, Nanostructured nitride films of multi-element high-entropy alloys by reactive DC sputtering, Surf. Coatings Technol. 193 (2004) 193–200. doi:10.1016/j.surfcoat.2005.08.081.

[71] P.K. Huang, J.W. Yeh, Effects of substrate temperature and post-annealing on microstructure and properties of (AlCrNbSiTiV)N coatings, Thin Solid Films. 518 (2009) 180–184. doi:10.1016/j.tsf.2009.06.020.

[72] C.Y. Hsu, T.S. Sheu, J.W. Yeh, S.K. Chen, Effect of iron content on wear behavior of AlCoCrFexMo0.5Ni high-entropy alloys, Wear. 268 (2010) 653–659. doi:10.1016/j.wear.2009.10.013.

[73] B. Gwalani, A. V. Ayyagari, D. Choudhuri, T. Scharf, S. Mukherjee, M. Gibson, R. Banerjee, Microstructure and wear resistance of an intermetallic-

44

based Al0.25Ti0.75CoCrFeNi high entropy alloy, Mater. Chem. Phys. (2017) 1–10. doi:10.1016/j.matchemphys.2017.06.034.

[74] Y. Yu, F. He, Z. Qiao, Z. Wang, W. Liu, J. Yang, Effects of temperature and microstructure on the triblogical properties of CoCrFeNiNbx eutectic high entropy alloys, J. Alloys Compd. (2018). doi:10.1016/j.jallcom.2018.10.138.

[75] J. Joseph, N. Haghdadi, K. Shamlaye, P. Hodgson, M. Barnett, D. Fabijanic, The sliding wear behaviour of CoCrFeMnNi and AlxCoCrFeNi high entropy alloys at elevated temperatures, Wear. 428–429 (2019) 32–44. doi:10.1016/j.wear.2019.03.002.

[76] S. Yadav, A. Kumar, K. Biswas, Wear behavior of high entropy alloys containing soft dispersoids (Pb, Bi), Mater. Chem. Phys. 210 (2018) 222–232. doi:10.1016/j.matchemphys.2017.06.020.

[77] R. Zhou, G. Chen, B. Liu, J. Wang, L. Han, Y. Liu, Microstructures and wear behaviour of (FeCoCrNi)1-x(WC)x high entropy alloy composites, Int. J. Refract. Met. Hard Mater. 75 (2018) 56–62. doi:10.1016/j.ijrmhm.2018.03.019.

[78] A. Poulia, E. Georgatis, A. Lekatou, A.E. Karantzalis, Microstructure and wear behavior of a refractory high entropy alloy, Int. J. Refract. Met. Hard Mater. 57 (2016) 50–63. doi:10.1016/j.ijrmhm.2016.02.006.

[79] A. Poulia, E. Georgatis, A. Lekatou, A. Karantzalis, Dry-Sliding Wear Response of MoTaWNbV High Entropy Alloy, Adv. Eng. Mater. 19 (2017) 1–10. doi:10.1002/adem.201600535.

[80] C. Mathiou, A. Poulia, E. Georgatis, A.E. Karantzalis, Microstructural features and dry - Sliding wear response of MoTaNbZrTi high entropy alloy, Mater. Chem. Phys. 210 (2018) 126–135. doi:10.1016/j.matchemphys.2017.08.036.

[81] A. Cunliffe, J. Plummer, I. Figueroa, I. Todd, Glass formation in a high entropy alloy system by design, Intermetallics. 23 (2012) 204–207. doi:10.1016/j.intermet.2011.12.006.

[82] I.A. Figueroa, R. Ristić, A. Kuršumović, K. Biljaković, D. Starešinić, D. Pajić, G. Remenyi, E. Babić, Properties of (TiZrNbCu)1-xNix metallic glasses, J. Alloys Compd. 745 (2018) 455–459. doi:10.1016/j.jallcom.2018.02.169.

[83] C.Y. Cheng, J.W. Yeh, High thermal stability of the amorphous structure of GexNbTaTiZr (x=0.5, 1) high-entropy alloys, Mater. Lett. 181 (2016) 223–

45

226. doi:10.1016/j.matlet.2016.06.040.

[84] S. Alvi, D.M. Jarzabek, M.G. Kohan, D. Hedman, P. Jenczyk, M.M. Natile, A. Vomiero, F. Akhtar, Synthesis and Mechanical Characterization of a CuMoTaWV High-Entropy Film by Magnetron Sputtering, ACS Appl. Mater. Interfaces. 12 (2020) 21070–21079. doi:10.1021/acsami.0c02156.

[85] S. Alvi, F. Akhtar, High temperature tribology of CuMoTaWV high entropy alloy, Wear. 426–427 (2019) 412–419. doi:10.1016/j.wear.2018.12.085.

46

DOCTORA L T H E S I S

Sajid Ali A

lvi Refractory H

igh-entropy Alloys and Film

s for High Tem

perature Applications

Department of Engineering Sciences and MathematicsDivision of Materials Science

ISSN 1402-1544ISBN 978-91-7790-641-4 (print)ISBN 978-91-7790-642-1 (pdf)

Luleå University of Technology 2020

Refractory High-entropy Alloys and Films for High Temperature Applications

Sajid Ali Alvi

Engineering Materials

Refractory High-entropy Alloys and Films for High Temperature Applications

Sajid Ali Alvi

Engineering Materials

130263-LTU_Avh-Alvi.indd Alla sidor130263-LTU_Avh-Alvi.indd Alla sidor 2020-09-24 09:482020-09-24 09:48

130263_Sajid Ali Alvi_ PhD thesis.pdfAbstractAcknowledgements1. High-entropy alloysThe inception of high-entropy alloys

2. Refractory High-entropy alloysProcessing of refractory HEAsBulk refractory HEAsRefractory HEA thin films and their nitrides

Properties of refractory HEAsMechanical behaviour of bulk refractory HEAsMechanical behaviour of refractory high-entropy films and their nitridesWear properties of bulk refractory HEAs

3. Research Objectives4. MethodologyHigh temperature tribologyRoom temperature tribotest

5. Summary of published workPaper IPaper IIPaper IIIPaper IV

6. Future DirectionsReferencesAppended PapersPaper 1 for PHD dessertation.pdfHigh temperature tribology of CuMoTaWV high entropy alloyIntroductionMaterials and methodsThermocalc simulationSpark plasma sinteringStructural and chemical characterizationWear characterization

Results and discussionConclusionsAcknowledgmentsReferences

Paper 4 for PhD dessertation.pdf1. Introduction2. Materials and Methods3. Results and Discussion4. ConclusionsReferences

Tom sidaTom sidaTom sidaTom sidaTom sidaTom sida