Opportunity and Challenge of Refractory High-Entropy Alloys in the Field of Reactor Structural Materials

doi:10.11900/0412.1961.2020.00293

Acta Metall Sin

2021, Vol. 57

Issue (1): 42-54 DOI: 10.11900/0412.1961.2020.00293

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Opportunity and Challenge of Refractory High-Entropy Alloys in the Field of Reactor Structural Materials

LI Tianxin¹, LU Yiping¹^,²(

), CAO Zhiqiang¹, WANG Tongmin¹, LI Tingju¹

^1.Key Laboratory of Solidification Control and Digital Preparation Technology (Liaoning Province), School of Materials Science and Engineering, Dalian University of Technology, Dalian 116024, China
^2.Science and Technology on Reactor Fuel and Materials Laboratory, Nuclear Power Institute of China, Chengdu 610014, China

Cite this article:

LI Tianxin, LU Yiping, CAO Zhiqiang, WANG Tongmin, LI Tingju. Opportunity and Challenge of Refractory High-Entropy Alloys in the Field of Reactor Structural Materials. Acta Metall Sin, 2021, 57(1): 42-54.

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Abstract

Exploitation of traditional reactor structural materials tends to limits; thus, the development of novel materials is urgent. Alloying has long been used to obtain materials with desirable properties. In recent decades, a new alloying technique that combines multiple principal elements in high concentrations to fabricate new materials, termed high-entropy alloys (HEAs), has gained popularity. Refractory HEAs (RHEAs) consist of several principle refractory elements and are an important subset of HEAs. RHEAs have attracted immense attention owing to their unique mechanical, physical, and chemical properties, particularly their excellent high-temperature mechanical properties and radiation resistance. RHEAs are expected to be utilized in cladding materials for fourth-generation fission reactors and plasma-facing materials for fusion reactors. Combined with representative literature, this paper focuses on mechanical, radiation resistance, and oxidation resistance properties of RHEAs. Further, strengthening and radiation resistance mechanisms of RHEAs are explored, and the development evolution and prospects of RHEAs are proposed.

Key words: refractory high-entropy alloy mechanical property radiation resistance oxidation resistance

Received: 06 August 2020

ZTFLH:

TG132.3

Fund: National Magnetic Confinement Fusion Energy Research and Development Program(2018YFE-0312400);National Natural Science Foundation of China(51822402);National Key Research and Development Program of China(2019YFA0209901);Liao Ning Revitalization Talents Program(XLYC1807047);Fund of Science and Technology on Reactor Fuel and Materials Laboratory(6142A06190304);Fund of the State Key Laboratory of Solidification Processing in NWPU(SKLSP201902)

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	Tianxin LI
	Yiping LU
	Zhiqiang CAO
	Tongmin WANG
	Tingju LI

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https://www.ams.org.cn/EN/10.11900/0412.1961.2020.00293 OR https://www.ams.org.cn/EN/Y2021/V57/I1/42

Fig.1 Difference between the design of conventional alloys and high-entropy alloys on a ternary plot

Fig.2 Yield strengths of model refractory high-entropy alloys and nickel-based superalloys, molybdenum-based alloys, tantalum-based alloys, niobium-based alloys at different temperatures (The strength of Mo-20W-0.1Zr-0.1Ti alloy is tensile strength, and the strengths of other alloys are yield strengths)^[36-39]

Table 1 Brief summaries of yield strength (σ_0.2), plastic strain (ε), temperature (T), phase structure, alloys composition (mole fraction) and equilibrium condition^{[14,36,40-50]}

Fig.3 Yield strength at 1200^oC ( $σ 0.2 1200 ℃$ ) of single-phase (S) and multi-phase (M) refractory high-entropy alloys as a function of the melting temperature (T_m)^[11]

Fig.4 Separation of ductile and brittle refractory high-entropy alloys by the valence electron concentration^[59]

Fig.5 Yield strength, prediction by Labusch model vs experiment, for a range of refractory high-entropy alloys^[64]

Fig.6 Yield strength, prediction by Maresca et al. model and experiments, vs temperature^[68]

Fig.7 STEM-HAADF images and the fast Fourier transforms of AlMo_0.5NbTa_0.5TiZr showing cuboidal precipitates of a disordered bcc phase are separated by ordered B2 phase for the dark channels^[39]

Fig.8 Average nanoindentation hardness vs the indentation depth (a) and variation of lattice parameter vs irradiation dose (b) for irradiated Ti₂ZrHfV_0.5Mo_0.2 alloys at different ion doses^[23]

Table 2 Density functional theory calculated defect migration energy in different alloys^[90-92]

Fig.9 Trajectories of an interstitial cluster in various alloys^[75]

Fig.10 Generalized oxidation kinetics scheme of alloys with different oxides^[99]

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