Electrochemistry and In Situ Scratch Behavior of 690 Alloy in Simulated Nuclear Power High Temperature High Pressure Water

doi:10.11900/0412.1961.2020.00091

Acta Metall Sin

2020, Vol. 56

Issue (11): 1474-1484 DOI: 10.11900/0412.1961.2020.00091

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Electrochemistry and In Situ Scratch Behavior of 690 Alloy in Simulated Nuclear Power High Temperature High Pressure Water

LI Xiaohui¹, WANG Jianqiu²(

), HAN En-Hou², GUO Yanjun¹, ZHENG Hui³, YANG Shuangliang³

1 Huadian Electric Power Research Institute Co. , Ltd. , Hangzhou 310030, China
2 Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
3 State Nuclear Power Plant Service Company, Shanghai 200233, China

Cite this article:

LI Xiaohui, WANG Jianqiu, HAN En-Hou, GUO Yanjun, ZHENG Hui, YANG Shuangliang. Electrochemistry and In Situ Scratch Behavior of 690 Alloy in Simulated Nuclear Power High Temperature High Pressure Water. Acta Metall Sin, 2020, 56(11): 1474-1484.

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Abstract

The abnormal shutdown of the pressurized water reactor (PWR) nuclear power plants can be primarily attributed to the rupturing of the heat transfer tube of the steam generator. Regardless, stress corrosion cracking is the most important ageing mechanism associated with the primary water of the PWR. In this work, the damage behavior of alloy 690 was systematically investigated using high-temperature and high-pressure in situ scratching and electrochemical techniques to understand its corrosion behavior and failure mode and provide a reference for controlling the manufacturing, processing, and installation of the alloy 690 tubing. Further, the polarization behavior of alloy 690 at different temperatures was investigated using the self-built high-temperature and high-pressure water circulation circuit system and the high-temperature and high-pressure in situ scratching device. Subsequently, the single-pass scratch in air and in situ reciprocating scratch of alloy 690 obtained using high-temperature and high-pressure water for 11 and 100 h, respectively, were studied. The samples after scratching were observed and analyzed via SEM and EDS. The results revealed the occurrence of microcracks at the bottom of the scratch during the single-pass scratch of alloy 690. The TiN inclusions with large particles were prone to fragmentation, whereas those with smaller particles were susceptible to cracking at the joint of the matrix. During the reciprocating scratch process in high-temperature and high-pressure water, a portion of the metal substrate debris at the bottom of the scratch groove was peeled off along with oxide particles, microcracks, and chipped debris. Further, the TiN inclusions with large particles were fragmented, whereas those with smaller particles easily cracked at the bonding interface of the substrate. The electrochemical signals of alloy 690 during the reciprocating scratch processes were measured using the high-temperature and high-pressure in situ electrochemical technology. The instantaneous peak current density at the scratch during the scratch process is 149~326 times of that associated with the substrate.

Key words: alloy 690 high temperature high pressure water corrosion in situ scratch

Received: 20 March 2020

ZTFLH:

TG172.82

Fund: National Science and Technology Major Project(2015ZX06002005)

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	Xiaohui LI
	Jianqiu WANG
	En-Hou HAN
	Yanjun GUO
	Hui ZHENG
	Shuangliang YANG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2020.00091 OR https://www.ams.org.cn/EN/Y2020/V56/I11/1474

Fig.1 Schematics of high temperature and high pressure water in situ scratching device (a) and internal structure (b) (RE—reference electrode, CE—counter electrode, WE—working electrode, PTFE —polytetrafluoroethylene)

Fig.2 Polarization curves of alloy 690 at different temperatures (SHE—standard hydrogen electrode, E—potential, i—current density)

Fig.3 Relationship between passive current density (i_p) and temperature (T) of alloy 690 in high temperature and high pressure water (E_a—apparent activation energy)

Fig.4 Macro surface (a) and section (b) images, and micro morphology inside the scratch groove (c) after single scratching of alloy 690 in air

Fig.5 SEM images (a, c) and EDS result (b) of single scratch bottom around TiN inclusion on alloy 690 in air
(a) cracking at the interface between TiN inclu- ^{sion and substrate
(b) EDS result of point in Fig.5a(c) TiN inclusion fragmented}

Fig.6 SEM image of hard alloy YG8 scratching head (a) and surface morphology of the tip (b)

Fig.7 Morphologies of the bottom of the scratch (a) and local inclusions (b), and EDS result (c) of alloy 690 after 11 h of reciprocating scratches

Fig.8 Bottom morphologies of alloy 690 after 100 h reciprocating scratches(a) fish scale (b) micro cracks (c) granular oxides

Fig.9 Morphologies (a, c) and EDS results (b, d) of local inclusions at the bottom of the scratch after alloy 690 is scratched back and forth for 100 h
(a) TiN inclusion fragmented
(b) EDS result of the TiN inclusion in Fig.9a
(c) cracking at the interface between TiN inclusion and substrate
(d) EDS result of the TiN inclusion in Fig.9c

Fig.10 Current density changes with elapsed time during high temperature high pressure in situ reciprocating scratches

Table 1 Comparison of peak current density at the moment of scratches

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