High-Temperature Microstructural Stability of High-Si Austenitic Steels for Lead-Cooled Fast Reactor Fasteners

doi:10.11900/0412.1961.2026.00079

Acta Metall Sin

2026, Vol. 62

Issue (8): 1347-1356 DOI: 10.11900/0412.1961.2026.00079

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High-Temperature Microstructural Stability of High-Si Austenitic Steels for Lead-Cooled Fast Reactor Fasteners

SHI Xianbo¹, ZHANG Shuzhan¹, SU Yuanfei¹, JIAO Shengxuan¹^,², YAN Wei¹(

), RONG Lijian¹(

)

1 Shenyang National Laboratory for Materials Science, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
2 School of Materials Science and Engineering, University of Science and Technology of China, Shenyang 110016, China

Cite this article:

SHI Xianbo, ZHANG Shuzhan, SU Yuanfei, JIAO Shengxuan, YAN Wei, RONG Lijian. High-Temperature Microstructural Stability of High-Si Austenitic Steels for Lead-Cooled Fast Reactor Fasteners. Acta Metall Sin, 2026, 62(8): 1347-1356.

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Abstract

Currently, there is rapid development of lead-cooled fast reactors (LFRs) as a main type of Generation IV nuclear reactor in China. High-Si austenitic stainless steel is a candidate structural material for important LFR components, such as fasteners, due to its excellent high-temperature mechanical properties and corrosion resistance to liquid Pb-Bi. However, high-Si steel accelerates the precipitation of secondary phases, such as M₂₃C₆, M₆C, χ phase, G phase, and ferrite, during long-term high-temperature aging, thereby reducing microstructural stability and degrading mechanical properties. Therefore, while high-Si steel enables better corrosion resistance, the problem of high-temperature microstructural stability remains a critical issue to resolve. This review focuses on the use of high-Si austenitic stainless steel for LFR fasteners, with the introduction of the Si alloying design principle and a summary of the evolution characteristics of secondary phases induced by Si addition in austenitic steels. Furthermore, an alloying strategy to improve microstructural stability based on experimental findings is proposed along with an outlook toward future developments.

Key words: lead-cooled fast reactor fastener high-Si austenitic steel microstructural stability liquid Pb-Bi corrosion

Received: 17 March 2026

ZTFLH:

TG142.25

Fund: Natural Science Foundation of Liaoning Province(2023-MS-019);LingChuang Research Project of China National Nuclear Corporation

Corresponding Authors: YAN Wei, professor, Tel: (024)23978990, E-mail: weiyan@imr.ac.cn; RONG Lijian, professor, Tel: (024)23971979, E-mail: ljrong@imr.ac.cn

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	SHI Xianbo
	ZHANG Shuzhan
	SU Yuanfei
	JIAO Shengxuan
	YAN Wei
	RONG Lijian

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https://www.ams.org.cn/EN/10.11900/0412.1961.2026.00079 OR https://www.ams.org.cn/EN/Y2026/V62/I8/1347

Fig.1 Standard Gibbs free energy of formation (Δ_mG⁰) as a function of temperature for various oxides relevant to oxygen-containing liquid Pb and liquid Pb-Bi eutectic (LBE) alloy^[38] (R—gas constant, T—temperature (K), p $O 2$ —oxygen partial pressure (bar), s—solid, L—liquid)

Fig.2 Cross-sectional SEM images showing oxide layer morphologies of Fe-15Cr-11Ni austenitic steel with different Si contents (mass fraction, %, the same below) after exposure to static oxygen-saturated LBE at 550 ^oC for 3000 h

Fig.3 Cross-sectional low (a) and high (b) magnified SEM images and EDS elemental distribution maps (c) of Fe-15Cr-11Ni-2.5Si austenitic steel after exposure to LBE at 550 ^oC for 3000 h with a flow velocity of 2 m/s and an oxygen content of 10^-6%

Fig.4 SEM image (a) and bright field (BF) TEM image (b) of G phase and ferrite formed in Fe-15Cr-10Ni-2.5Si austenitic steel after aging at 510 ^oC for 1000 h^[50] (Inset in Fig.4a is the high magnified view, insets in Fig.4b are EDS elemental distribution maps of the rectangle area. GB—grain boundary)

Fig.5 SEM images of two high-Si austenitic steels after aging at 510 ^oC for 3000 h

Table 1 Key chemical compositions, Ni_eq, Cr_eq, and Ni_eq / Cr_eq of eight high-Si austenitic steels

Fig.6 Locations of eight Fe-Cr-Ni-Si-Mo austenitic steels in Schaeffler diagram (w_i —mass fraction of element i. Blue and red four-pointed stars denote the absence and presence of G-phase and ferrite precipitation during aging at 510 ^oC for 3000 h under the specified Cr_eq / Ni_eq equivalent ratio, respectively)

Fig.7 Variation curves of diffusion coefficients of Ni, Cr (a) and Mo, Si (b) with N content in high-Si austenitic steel^[64]

Fig.8 Stress relaxation resistances of N-free, N-containing, and γ′-strengthened high-Si austenitic steels at 510 ^oC

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