耐Pb-Bi腐蚀Si增强型铁素体/马氏体钢和奥氏体不锈钢的研究进展

doi:10.11900/0412.1961.2022.00531

金属学报

2023, Vol. 59

Issue (4): 502-512 DOI: 10.11900/0412.1961.2022.00531

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本期目录 | 过刊浏览

耐Pb-Bi腐蚀Si增强型铁素体/马氏体钢和奥氏体不锈钢的研究进展

吴欣强, 戎利建(

), 谭季波, 陈胜虎, 胡小锋, 张洋鹏, 张兹瑜

中国科学院金属研究所中国科学院核用材料与安全评价重点实验室沈阳 110016

Research Advance on Liquid Lead-Bismuth Eutectic Corrosion Resistant Si Enhanced Ferritic/Martensitic and Austenitic Stainless Steels

WU Xinqiang, RONG Lijian(

), TAN Jibo, CHEN Shenghu, HU Xiaofeng, ZHANG Yangpeng, ZHANG Ziyu

CAS Key Laboratory of Nuclear Materials and Safety Assessment, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

引用本文:

吴欣强, 戎利建, 谭季波, 陈胜虎, 胡小锋, 张洋鹏, 张兹瑜. 耐Pb-Bi腐蚀Si增强型铁素体/马氏体钢和奥氏体不锈钢的研究进展[J]. 金属学报, 2023, 59(4): 502-512.
Xinqiang WU, Lijian RONG, Jibo TAN, Shenghu CHEN, Xiaofeng HU, Yangpeng ZHANG, Ziyu ZHANG. Research Advance on Liquid Lead-Bismuth Eutectic Corrosion Resistant Si Enhanced Ferritic/Martensitic and Austenitic Stainless Steels[J]. Acta Metall Sin, 2023, 59(4): 502-512.

全文: PDF(4501 KB) HTML

摘要:

结构材料是制约铅冷快堆建设的关键因素之一，原因是其组成元素在液态Pb-Bi共晶(LBE)中会发生不同程度的溶解，影响结构安全。候选结构材料铁素体/马氏体钢T91与不锈钢316在550℃饱和氧LBE环境中发生快速氧化腐蚀；溶解氧浓度降至1.26 × 10^-6% (质量分数)可减轻T91的液态LBE腐蚀，但低于1 × 10^-6%时，T91与316钢发生溶解腐蚀；T91液态LBE脆化敏感性高，导致其在350℃液态LBE中腐蚀疲劳寿命显著降低。与商用的(9%~12%)Cr铁素体/马氏体钢和316型奥氏体不锈钢相比，经微合金化的Si增强型铁素体/马氏体钢(9Cr-Si和12Cr-Si)和奥氏体不锈钢(ASS-Si)，具有较好的组织稳定性和综合力学性能，且在液态LBE中形成的富Si氧化物提高了氧化膜的致密性，改善了其耐腐蚀性能，在550℃下静态饱和氧和动态控氧LBE环境中的溶解腐蚀受到抑制，有望满足铅冷快堆的设计需求。

关键词 ：铁素体/马氏体钢, 奥氏体不锈钢, 液态金属腐蚀, 液态金属脆化, 力学性能, 组织稳定性

Abstract：

Structural materials are one of the major factors that restrict the lead-cooled fast reactor construction due to metallic elements that can dissolve in the liquid lead-bismuth eutectic (LBE), which may affect the structure's safety. T91 steel and 316 stainless steel are the leading structural materials for critical equipment such as fuel cladding, reactor vessels, and reactor core internals. The environmental compatibility of those steels with the liquid LBE needs to be systematically evaluated. However, T91 steel and 316 stainless steel suffer from rapid oxidation corrosion in oxygen-saturated LBE at 550^oC. T91 steel's corrosion resistance in liquid LBE can be improved by decreasing the oxygen concentration (1.26 × 10^-6%, mass fraction), but dissolved corrosion occurred at dissolved oxygen concentration below 1 × 10^-6% for T91 steel and 316 stainless steel. T91 steel is sensitive to liquid metal embrittlement, significantly reducing its corrosion fatigue life in the liquid LBE. Compared to the standard (9%-12%)Cr ferritic/martensitic steel and 316 stainless steel, the microalloyed Si enhanced (9%-12%)Cr ferritic/martensitic steel (9Cr-Si and 12Cr-Si) and 316 stainless steel (ASS-Si) have good microstructural stability and comprehensive mechanical properties. The Si-rich oxide formation in liquid LBE improves the oxide film compactness and corrosion resistance. The dissolution corrosion was inhibited in static oxygen-saturation and oxygen-controlled (10^-6%-10^-7%) flowing liquid LBE (0.3 m/s) at 550^oC for 9Cr-Si, 12Cr-Si, and ASS-Si. These alloys are expected to meet the design requirements for a lead-cooled fast reactor.

Key words： ferritic/martensitic steel austenitic stainless steel liquid metal corrosion liquid metal embrittlement mechanical property microstructure stability

收稿日期: 2022-10-20

ZTFLH:

TL341

基金资助:国家自然科学基金项目(52271077);国家自然科学基金项目(51871218);中核集团领创科研项目及中国科学院青年创新促进会项目(2021189)

通讯作者: 戎利建，ljrong@imr.ac.cn，主要从事核用材料研究

Corresponding author: RONG Lijian, professor, Tel: (024)23971979, E-mail: ljrong@imr.ac.cn

作者简介: 吴欣强，男，1971年生，研究员，博士

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图1 液态Pb-Bi共晶(LBE)腐蚀损伤测试装置实物图

图2 铁素体/马氏体钢T91在550℃液态LBE中浸泡1000 h后的截面形貌[4]

图3 不锈钢316在550℃液态LBE中浸泡1000 h后的截面形貌

图4 T91和316钢在高温空气与液态LBE环境中疲劳寿命对比

图5 T91和316钢在液态LBE环境中疲劳裂纹扩展区特征

图6 9Cr-Si在550℃静态饱和氧LBE环境下腐蚀1000 h后的氧化层形貌及元素分布

图7 12Cr-Si系铁素体/马氏体钢LBE腐蚀实验结果

图8 9Cr-Si铁素体/马氏体钢的铸态组织和均质化处理后的组织

图9 回火态9Cr-Si铁素体/马氏体钢的SEM像

图10 9Cr-Si铁素体/马氏体钢和T91的室温、高温强度曲线及韧脆转变温度(DBTT)曲线

图11 9Cr-Si铁素体/马氏体钢550℃时效后DBTT曲线及时效3000 h后的TEM像与元素分布图

图12 650℃下12Cr-Si和HT9持久性能的对比

图13 ASS-Si和316钢经550℃饱和氧LBE腐蚀5000 h后氧化层厚度随时间的变化曲线

图14 ASS-Si经550℃饱和氧LBE腐蚀1000 h后氧化膜的截面形貌和元素分布

图15 ASS-Si和316钢经550℃流动控氧LBE腐蚀1500 h后的截面形貌

图16 含Si奥氏体钢经550℃时效处理1000 h后晶界附近的微观组织及元素分布

表1 ASS-Si奥氏体钢和Type 304奥氏体钢在550℃下的拉伸强度和持久强度 (MPa)

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