核用耐铅铋腐蚀涂层的研究进展

doi:10.15541/jim20250372

无机材料学报 ›› 2026, Vol. 41 ›› Issue (6): 775-786.DOI: 10.15541/jim20250372

核用耐铅铋腐蚀涂层的研究进展

刘春帆¹^,³(), 陈科¹^,², 葛芳芳¹^,²(), 黄庆¹^,²

¹ 中国科学院宁波材料技术与工程研究所, 浙江省数据驱动高安全性能源材料与应用重点实验室, 宁波市特种能源材料与化学重点实验室, 宁波 315201
² 宁波杭州湾新材料研究院, 宁波 315336
³ 中国科学院大学, 北京 100049

收稿日期:2025-09-24 修回日期:2025-12-04 出版日期:2026-06-20 网络出版日期:2026-01-21
通讯作者: 葛芳芳, 研究员. E-mail: gefangfang@nimte.ac.cn
作者简介:刘春帆(2001-), 男, 硕士研究生. E-mail: liuchunfan@nimte.ac.cn
基金资助:
中国科学院战略性先导专项(XDA041030301)

Research Progress on Lead-bismuth Eutectic Corrosion Resistant Coatings

LIU Chunfan¹^,³(), CHEN Ke¹^,², GE Fangfang¹^,²(), HUANG Qing¹^,²

¹ Ningbo Key Laboratory of Special Energy Materials and Chemistry, Zhejiang Key Laboratory of Data-Driven High-Safety Energy Materials and Applications, Ningbo Institute of Materials Technology and Engineering, Chinese Academy of Sciences, Ningbo 315201, China
² Qianwan Institute of CNITECH, Ningbo 315336, China
³ University of Chinese Academy of Sciences, Beijing 100049, China

Received:2025-09-24 Revised:2025-12-04 Published:2026-06-20 Online:2026-01-21
Contact: GE Fangfang, professor. E-mail: gefangfang@nimte.ac.cn
About author:LIU Chunfan (2001-), male, Master candidate. E-mail: liuchunfan@nimte.ac.cn
Supported by:
Strategic Priority Research Program of the Chinese Academy of Sciences(XDA041030301)

摘要/Abstract

摘要：

铅铋共晶(LBE)凭借其高沸点、高导热性及优良安全性能, 已成为加速器驱动先进核能系统(ADANES)和铅冷快堆(LFR)的核心冷却剂, 但其在高温环境下引发的氧化腐蚀、溶解腐蚀及冲刷腐蚀耦合问题, 严重威胁结构材料的服役寿命, 制约了先进核能技术的工程化应用。表面涂层技术可在保留基体固有性能的基础上提升耐蚀性, 是缓解LBE腐蚀的关键技术途径之一。本文系统综述了核用耐LBE腐蚀涂层的研究进展, 首先从腐蚀机理入手, 阐明了溶解氧、温度、流速与辐照等多因素协同作用对材料腐蚀的影响规律; 进而按金属、陶瓷及复合三大体系, 分析了FeCrAl(Y)、高熵合金、Al₂O₃、MAX相及梯度复合涂层的耐蚀机制、性能优势与失效行为。研究表明: FeCrAl(Y)涂层通过“基体-氧化膜”协同作用形成连续Al₂O₃隔离层, 其耐蚀性和力学性能与Cr、Al含量相关; 高熵合金涂层利用晶格畸变与多组元协同氧化抑制腐蚀介质的内扩散, 但面临高温相分解与辐照脆化等问题; Al₂O₃等陶瓷涂层热力学稳定, 可为基底提供有效防护, 但在高温环境中容易因非晶化、界面匹配及自修复缺失等失效。复合结构涂层通过“金属过渡层+陶瓷功能层”梯度设计, 有望实现高结合、高韧性、高阻隔等功能一体化。未来研究需聚焦环境-成分-工艺的耦合调控、多因素服役评价与寿命预测模型, 为先进核能系统提供长时可靠防护解决方案。

关键词: 铅冷快堆, 铅铋共晶, 涂层, 耐腐蚀性, 综述

Abstract:

Lead-bismuth eutectic (LBE), with its high boiling point, excellent thermal conductivity, and favorable safety properties, has become the core coolant for accelerator-driven advanced nuclear energy systems (ADANES) and lead-cooled fast reactors (LFRs). However, the coupled issues of oxidation corrosion, dissolution corrosion, and erosion corrosion induced by its high-temperature environment severely threaten the service life of structural materials, and hinder the engineering implementation of advanced nuclear technology. Surface coating technology, which enhances corrosion resistance while preserving the inherent properties of the substrate, has emerged as a key strategy to mitigate LBE corrosion. This paper provides a systematic review of research progress on corrosion-resistant coatings for nuclear applications against LBE corrosion. Starting from corrosion mechanisms, the influences of synergistic factors, including dissolved oxygen, temperature, flow velocity, and irradiation, on corrosion behavior are elucidated. Coatings are classified into three major systems, i.e. metallic, ceramic, and composite, and the corrosion resistance mechanisms, performance advantages, and failure behaviors of FeCrAl(Y), high-entropy alloys, Al₂O₃, MAX phases, and gradient composite coatings are analyzed. Research indicates that FeCrAl(Y) coatings form a continuous Al₂O₃ barrier layer through “matrix-oxide film” synergistic effect, with corrosion resistance and mechanical properties correlated to Cr and Al content. High-entropy alloy coatings suppress inward diffusion of corrosion species through lattice distortion and multi-component synergistic oxidation, yet they are susceptible to like high-temperature phase decomposition and irradiation embrittlement. Thermodynamically stable ceramic coatings like Al₂O₃ provide effective substrate protection, yet tend to fail in high-temperature environments due to amorphous crystallization, interface mismatch, and lack of self-healing. Composite-structured coatings with a gradient architecture of “metal transition layers + ceramic functional layers” present a promising approach for integrating high adhesion, high toughness, and high barrier properties. Future efforts should focus on coupled regulation of environment-composition-process, multi-factor service evaluation, and lifetime prediction models to deliver long-term reliable protection solutions for advanced nuclear energy systems.

Key words: lead-cooled fast reactor, lead-bismuth eutectic, coating, corrosion resistance, review

中图分类号:

TL34

刘春帆, 陈科, 葛芳芳, 黄庆. 核用耐铅铋腐蚀涂层的研究进展[J]. 无机材料学报, 2026, 41(6): 775-786.

LIU Chunfan, CHEN Ke, GE Fangfang, HUANG Qing. Research Progress on Lead-bismuth Eutectic Corrosion Resistant Coatings[J]. Journal of Inorganic Materials, 2026, 41(6): 775-786.

图/表 10

图1 AISI 316L钢经动态LBE腐蚀后(420/550/600 ℃, 2000 h, 2 m/s)的截面腐蚀形貌[8]

Fig. 1 Cross-sectional morphologies of AISI 316L after dynamic LBE corrosion (420/550/600 ℃, 2000 h, 2 m/s)[8]

表1

Table 1 Lead-bismuth corrosion resistance of various alloy coatings[9,18 -32]

Coating	Base material	Deposition method	Thickness/ μm	LBE corrosion test			Ref.
Coating	Base material	Deposition method	Thickness/ μm	O₂ concentration (mass fraction)	Temperature/℃	Duration/h	Ref.
FeCrAl	T91	GESA	30	10^-6%	480−600	2000	[9]
	T91	GESA	30	Saturated	400	900	[18]
	T91	LPPS/GESA	30	10^-6%/10^-8%	400−550	900	[19]
	F/M steel	MS	1.7−7.1	6.6×10⁻³%	500−650	1000	[20]
FeCrAlSi	F/M steel	MS	2.6−3.9	8.1×10⁻⁴%/1.8×10⁻³%/ 4.0×10⁻³%	500/550/600	1000	[21]
FeCrAlW_x	F/M steel	SLM	5.1	1.37×10⁻⁴%	550	500/1000/2000	[22]
FeCrAlY	F/M steel	MS	6	1.7×10⁻³%	550	40	[23]
FeCrMoWCBY	F/M steel	Arc melting	40	2.1×10^-3%	500	1000	[24]
AlCrFeMoTi	F/M steel	MS	3.6	Saturated	450-650	1000	[25]
AlCrFeMoTi	F/M steel	MS	4.1	6.04×10^-3%	650	1000	[26]
AlCrFeMoTiSi_x	F/M steel	MS	10	6.04×10^-3%	650	1000	[27]
FeCrAlTiNb	F/M steel	MS	3	1.8×10⁻³%/6.8×10⁻³%	550/650	500−1500	[28]
	F/M steel	MS	5−15	8×10^-4%	500	500	[29]
	F/M steel	MS	4.5	10⁻⁴%/10⁻⁷%	500	1000	[30]
TiNbZrMoV	F/M steel	MS	3.9	6.8×10^-3%	650	100−1000	[31]
FeAl	316L	Slurry aluminizing	48.8	10^-7%/1.8×10⁻³%	550	1500	[32]

表2

Table 2 Lead-bismuth corrosion resistance of various ceramic coatings[33-45]

Coating	Base material	Deposition method	Thickness/ μm	LBE corrosion test			Ref.
Coating	Base material	Deposition method	Thickness/ μm	O₂ concentration (mass fraction)	Temperature/℃	Duration/h	Ref.
Al₂O₃	316L	PLD	1	10^-8%	550	1000/4000	[33]
	CrNiFe600	Sol-Gel	10	7.88×10^-4%	500	200	[34]
	Inconel 600	Sol-Gel	10	No mention	650	100	[35]
	T91	MS	1.5	10^-6%	550	1200	[36]
	F/M steel	MS	3.3	1.79×10^-3%	550	1000	[37]
	9Cr1Mo steel	PLD	2-8	No mention	550	500	[38]
ZrO₂	F/M steel	MS	0.5	3.25×10⁻⁴%	450−650	1000	[39]
AlTiN	316L	CAIP	4.35	1.61×10^-3% (550 ℃)/3.21×10^-3% (600 ℃)	550/600	500	[40]
TiAlN	T91	HIPIMS	2.2	10^-6%	550	1200	[36]
TiAlN	WNiFe alloy	CAIP	3.7	Saturated oxygen	450	3000	[41]
TiSiN	316L	CAIP	2-2.5	2.15×10^-2%	550	500	[42]
TiC	SIMP steel	CAIP	5.1	2.0×10^-3%	600	2000	[43]
Ti₃AlC₂	Al₂O₃	MS	3	1×10^-6%	600	3200	[44]
Ti₂AlC
V₂AlC
Cr₂AlC
(CrAlTiNbV)N_x	F/M steel	MS	0.8/0.9	7.0×10^-3%	550	1200	[45]

图2 550 ℃下暴露于液态LBE中的氧化物弥散强化型铁铬铝(ODS-FeCrAl)合金的金属氧化物吉布斯自由能-温度变化图[46]

Fig. 2 Gibbs free energy change-temperature diagram of metal oxides for ODS-FeCrAl exposed to liquid LBE at 550 ℃[46]

图3 试管在550 ℃下经1~1.2 m/s流速LBE腐蚀2000 h对比(上: 未涂覆涂层; 下: 涂覆涂层)[47]

Fig. 3 Original (above) and surface coated (below) test tubes after 2000 h LBE corrosion at 550 ℃ with a flow rate of 1-1.2 m/s[47]

图4 FeCrAl涂层成分的三元相图[19]

Fig. 4 Ternary phase diagram with the composition of FeCrAl coatings[19]

图5 经650 ℃ LBE腐蚀试验1000 h后, 不同辐照损伤剂量的AlCrFeMoTi高合金化钢涂层表面的扫描电子显微镜(SEM)形貌[26]

Fig. 5 Surface scanning electron microscope (SEM) images of the irradiated AlCrFeMoTi HEA coatings with different irradiation damage doses after static LBE corrosion tests at 650 ℃ for 1000 h[26] (a, d) 10 dpa; (b, e) 45 dpa; (c, f) 90 dpa

图6 (a, b)涂覆涂层的1515Ti圆柱体在腐蚀试验(550 ℃, 4000 h, 溶解氧质量分数10−8%)前(a)、后(b)的状态; (c)宏观和(d, e)微观尺度的基体形貌[33]

Fig. 6 (a, b) Coated 1515Ti cylinders before (a) and after (b) the corrosion tests (stagnant lead, 550 ℃, 4000 h, 10−8% (in mass) O); (c) Macroscopic and (d, e) microscopic scale of the matrix morphology[33]

图7 TiAlN横截面透射电子显微镜(TEM)形貌[41]

Fig. 7 Transmission electron microscope (TEM) images of TiAlN coating[41] (a) Original sample; (b-d) After corrosion for 3000 h of (b) samples unirradiated, (c) pre-irradiated with 4×1015 ions/cm2, and (d) irradiated with 2×1016 ions/cm2

图8 腐蚀试验后MAX相涂层(Cr2AlC、V2AlC、Ti2AlC和Ti3AlC2)的SEM照片[44]

Fig. 8 SEM images of MAX-phase coatings (Cr2AlC, V2AlC, Ti2AlC, and Ti3AlC2) after the corrosion test[44]

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核用耐铅铋腐蚀涂层的研究进展

Research Progress on Lead-bismuth Eutectic Corrosion Resistant Coatings

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