CORROSION BEHAVIOR OF GH3535 SUPERALLOY IN FLiNaK MOLTEN SALT

doi:10.11900/0412.1961.2015.00132

Acta Metall Sin

2015, Vol. 51

Issue (9): 1059-1066 DOI: 10.11900/0412.1961.2015.00132

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CORROSION BEHAVIOR OF GH3535 SUPERALLOY IN FLiNaK MOLTEN SALT

Tao LIU^1,²,Jiasheng DONG²(

),Guang XIE²,Yisheng WANG³,Hui LI²,Zhijun LI⁴,Xingtai ZHOU⁴,Langhong LOU²

1 School of Materials Science and Engineering, Dalian University of Technology, Dalian 116024
2 Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016
3 Power Branch, AVIC China National South Aviation Industry Co., Ltd., Zhuzhou 412002
4 Shanghai Institute of Applied Physics, Chinese Academy of Sciences, Shanghai 201800

Cite this article:

Tao LIU,Jiasheng DONG,Guang XIE,Yisheng WANG,Hui LI,Zhijun LI,Xingtai ZHOU,Langhong LOU. CORROSION BEHAVIOR OF GH3535 SUPERALLOY IN FLiNaK MOLTEN SALT. Acta Metall Sin, 2015, 51(9): 1059-1066.

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Abstract

As one of the most promising next generation reactors, the molten salt breeder reactor (MSBR) with excellent inherence security has attracted more and more attentions in recent years due to energy shortage and the security problem of traditional nuclear reactor. The most significant service characteristic of the structural material used in MSBR is the existence of FLiNaK molten salt compared with other nuclear reactors. FLiNaK molten salt is very corrosive to the structural material in the reactor, and affects the safety operation of nuclear power plants. A polycrystalline Ni-Mo-Cr-Fe superalloy was developed and used as an important structural material in MSBR at Oak Ridge National Laboratory (ORNL), but the corrosion mechanism of the alloy in FLiNaK molten salt has not been determined since the study terminated in 1970's as some politic reasons. Alloy served in harsh environments, often using protective coating to improve the corrosion properties. While few works about the coating corrosion resistance in FLiNaK molten salt were reported at present. Al₂O₃ and Cr₂O₃ coatings usually have excellent corrosion resistance in molten salt, such as sulphate, nitrate and halide molten salt. But, whether the oxide film has corrosion resistance in FLiNaK molten salt has not been determined. In this work, the corrosion mechanism of alloy in FLiNaK molten salt was studied by using immersion corrosion experiment through the method of SEM, EDS and XRD. The influence of Al₂O₃ coating on corrosion resistance in FLiNaK molten salt was also investigated. The results show that the Al₂O₃ coating does not affect the exsolution corrosion characteristics of Cr and Mo elements in FLiNaK molten salt at 700 ℃ for 400 h. The different is that naked alloy exhibits intergranular corrosion characteristic, and the alloy with Al₂O₃ coating exhibits spot corrosion characteristic. The Al₂O₃ coating cannot improve the corrosion resistance of the alloy in FLiNaK molten salt. The Al₂O₃ film dissolved in molten salt and resulted in the exposure of the alloy surface. The corrosion rate was increased since the formation of corrosion cell between oxide film and the exposed alloy surface.

Key words: GH3535 alloy FLiNaK molten salt Al₂O₃ coating corrosion

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	Articles by authors
	Tao LIU
	Jiasheng DONG
	Guang XIE
	Yisheng WANG
	Hui LI
	Zhijun LI
	Xingtai ZHOU
	Langhong LOU

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https://www.ams.org.cn/EN/10.11900/0412.1961.2015.00132 OR https://www.ams.org.cn/EN/Y2015/V51/I9/1059

Fig.1 SEM images of the GH3535 specimens immersed in FLiNaK molten salt at 700 ℃ for 400 h without (a, c, e) and with (b, d, f) Al₂O₃ film

Fig.2 XRD spectra of the GH3535 specimens immersed in FLiNaK molten salt without (a) and with (b) Al₂O₃ film at 700 ℃ for 400 h

Fig.3 Cross-sectional SE-SEM (a) and BSE-SEM (b) images of the GH3535 specimens without Al₂O₃ film in FLiNaK molten salt at 700 ℃ for 400 h

Fig.4 Element distributions of the GH3535 specimen without Al₂O₃ film immersed in FLiNaK molten salt at 700 ℃ for 400 h

(a) Cr (b) Mo (c) Fe (d) O (e) Al (f) Ni

Fig.5 Cross-sectional SE-SEM (a) and BSE-SEM (b) images of the GH3535 specimens with Al₂O₃ film immersed in FLiNaK molten salt at 700 ℃ for 400 h

Fig.6 Element distributions of the GH3535 specimens with Al₂O₃ film immersed in FLiNaK molten salt at 700 ℃ for 400 h

Fig.7 Corrosion schematic of the corrosion reaction of the GH3535 specimen without Al₂O₃ film during long term thermal exposure in FLiNaK molten salt at 700 ℃ for 400 h

Fig.8 Corrosion schematic of the corrosion reaction of the Al₂O₃ film during long term thermal exposure in FLiNaK molten salt at 700℃ for 400 h

Fig.9 Corrosion schematic of the corrosion reaction of the Al₂O₃ film during long term thermal exposure before (a) and after (b) Al₂O₃ film peeled off in FLiNaK molten salt at 700 ℃ for 400 h

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