High-Entropy Alloys in Extreme Environments: A Perspective on Advantages, Challenges, and Breakthroughs

doi:10.11900/0412.1961.2025.00322

Acta Metall Sin

2026, Vol. 62

Issue (5): 743-755 DOI: 10.11900/0412.1961.2025.00322

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High-Entropy Alloys in Extreme Environments: A Perspective on Advantages, Challenges, and Breakthroughs

LU Zhaoping(

), SHEN Yaozu, WANG Xianzhen, CHEN Qiang, TANG Jianguo, ZHANG Xiaobin, YU Yong, JIANG Suihe, LIU Xiongjun, WANG Hui, WU Yuan

State Key Laboratory for Advanced Metals and Materials, University of Science and Technology Beijing, Beijing 100083, China

Cite this article:

LU Zhaoping, SHEN Yaozu, WANG Xianzhen, CHEN Qiang, TANG Jianguo, ZHANG Xiaobin, YU Yong, JIANG Suihe, LIU Xiongjun, WANG Hui, WU Yuan. High-Entropy Alloys in Extreme Environments: A Perspective on Advantages, Challenges, and Breakthroughs. Acta Metall Sin, 2026, 62(5): 743-755.

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Abstract

Extreme environments, such as ultra-high temperatures, extremely low temperatures, and intense irradiation, impose growing demands on structural materials for next-generation engineering applications. Conventional single-principal-element alloys are approaching their performance limits because of insufficient phase stability, low-temperature ductile-to-brittle transitions, and uncontrolled defect evolution. Conversely, high-entropy alloys (HEAs), characterized by multi-principal elements, exhibit high configurational entropy, severe lattice distortion, and chemical short-range order. These intrinsic characteristics enable exceptional thermal-mechanical stability, cryogenic toughness, and irradiation resistance, rendering them promising candidates for applications in extreme environments. Focusing on three representative conditions, this work summarizes the potentials and challenges of HEAs as structural materials, clarifies the underlying high-entropy-driven mechanisms, and identifies key technological barriers. Furthermore, we report perspectives on future research directions and propose pathways to accelerate the transition of HEAs from laboratory-scale research to practical engineering applications.

Key words: high-entropy alloy extreme environment structural material mechanical property

Received: 15 October 2025

ZTFLH:

TG139

Fund: National Natural Science Foundation of China(52201171);National Natural Science Foundation of China(52225103);National Natural Science Foundation of China(52322102);National Natural Science Foundation of China(U2441262);National Natural Science Foundation of China(W2412068);National Key Research and Development Program of China(2022-YFB4602101);Fundamental Research Funds for the Central Universities(FRF-IDRY-23-020);State Key Laboratory for Advanced Metals and Materials(2025-S11)

Corresponding Authors: LU Zhaoping, professor, Tel: (010)82375387, E-mail: luzp@ustb.edu.cn

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	Articles by authors
	LU Zhaoping
	SHEN Yaozu
	WANG Xianzhen
	CHEN Qiang
	TANG Jianguo
	ZHANG Xiaobin
	YU Yong
	JIANG Suihe
	LIU Xiongjun
	WANG Hui
	WU Yuan

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https://www.ams.org.cn/EN/10.11900/0412.1961.2025.00322 OR https://www.ams.org.cn/EN/Y2026/V62/I5/743

Fig.1 Summary diagrams showing yield strength vs temperature^[24] (HEA—high-entropy alloy)

Fig.2 Synergistic improvement of room-temperature plasticity and ultra-high-temperature strength of refractory HEA (RHEA) through grain boundary (GB) engineering strategies^[31]
(a) microstructure, solute element distribution, and the mechanical properties of the MoNbTaW alloy
(b) microstructure, solute element distribution, and the mechanical properties of the MoNbTaW alloy doped with B

Fig.3 Synergistic improvement of the room temperature (RT) and high-temperature mechanical properties of ultra-high-temperature RHEA through the introduction of eutectic carbides^[42]
(a) dual-phase microstructure and corresponding SAED pattern of the a1 region (inset)
(b) atomic-level bcc/hcp phase interface
(c) solute element distribution(d) room-temperature mechanical properties (In W₃₀Ta₃₀(MoNb)_{40 -}_x C _x alloy, where x represents the molar ratio of C, x = 0, 4, 10, and 16, hereafter referred to as C0, C4, C10, and C16, respectively)
(e) high-temperature mechanical properties

Fig.4 Low-temperature fracture toughness and deformation microstructure of CrCoNi alloy^[47]
(a) J-integral versus crack growth resistance curves and fracture toughness values for the CrCoNi alloy (K_JIc—crack-initiation fracture toughness, K_SS—crack-growth toughness, σ_n—strength, Δa_max—maximum value of the crack extension)
(b) Ashby map in terms of the fracture toughness versus the yield strength for a broad class of materials (PC—polycarbonate, PE—polyethylene, PET—polyethylene terephthalate, PP—polypropylene, PS—polystyrene, PTFE—polytetrafluoroe-thylene)
(c) deformed microstructures of the CrCoNi alloy at 20 K (DF—dark-field, SF—stacking fault, SAD—selected area diffraction)

Fig.5 Room-temperature and low-temperature stress-strain curves (a) and the schematic of the deformation mechanism (b) of HfNbTaTiZr HEA^[56]

Fig.6 Cross-sectional TEM images of Ni, NiFe, NiCoFe, and NiCoFeCrMn irradiated with 3 MeV Ni⁺ to 5 × 10¹⁶ cm^-2 at 773 K showing the influence of the number of principal elements on irradiation defects in alloys^[65]

Fig.7 More pronounced chemical short-range order (CSRO) (a) and chemical fluctuation (b) in NiCoCrFeMn-CN compared to NiCoCrFeMn suppress void swelling (c, d) showing the influence of local chemical ordered structures and compositional fluctuations on irradiation defects in HEAs^[74] (D, D_vac, and D_inter represent the diffusion coefficient, diffusion coefficient of self-interstitial atoms, and diffusion coefficient of vacancies, respectively)

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