Effect of Surface State on Corrosion and Stress Corrosion for Nuclear Materials
HAN En-Hou1,2,3(), WANG Jianqiu1
1CAS Key Laboratory of Nuclear Materials and Safety Assessment, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China 2Institute of Corrosion Science and Technology, Guangzhou 510535, China 3School of Materials Science and Engineering, South China University of Technology, Guangzhou 511442, China
Cite this article:
HAN En-Hou, WANG Jianqiu. Effect of Surface State on Corrosion and Stress Corrosion for Nuclear Materials. Acta Metall Sin, 2023, 59(4): 513-522.
Global nuclear power events are often caused by local corrosion, which starts at the surface. The effect of the surface state on corrosion and the interaction among corrosion, irradiation, and stress are important technical problems affecting the safety, reliability, and economy of nuclear power plants. In this paper, supported by a series of national projects in the last 10 years, the various surface state effects, for key structural materials used in nuclear power plants after surface finishing, grinding, machining, or scratching, on corrosion and stress corrosion behaviors in the simulated primary water of nuclear power plants are reviewed. The results show that surface grinding, scratching, or cutting can cause the formation of microstructures of different gradients near the surface and also cause large differences in surface deformation. For example, the residual compressive stress is greater than the yield stress in the superficial surface of the scratch; the different cutting parameters can cause the various gradient structures of the nanocrystalline and grain distortion zones to form along the depth of the cutting surface with similar surface roughness. Such microstructures and local stress-strain conditions lead to significant differences in corrosion resistance. For example, the number of stress corrosion cracks is positively correlated with scratch depth. Under the combined action of irradiation, corrosion, and stress, irradiation-assisted stress corrosion is further enhanced. Finally, the future research trend on the topic is forecast.
Fund: National Basic Research Program of China(2011CB610500);National Basic Research Program of China(2006CB610500);National Science and Technology Major Project of China(2011ZX06004-009);National Key Research and Development Program of China(2016YFE0105200);Key Programs of Chinese Academy of Sciences(ZDRW-CN-2017-1);Key Research Program of Frontier Sciences, Chinese Academy of Sciences(QYZDY-SSW-JSC012)
Corresponding Authors:
HAN En-Hou, professor, Tel: (020)22309460, E-mail: ehhan@scut.edu.cn
Fig.1 Cross-section TEM images and SAED patters (insets) of alloy 690TT samples with different surface states (a) ground to 400 grit (b) ground to 1500 grit (c) mechanically polished (d) electropolished
Fig.2 Cross-section of the scratch in alloy 690TT[16] (a) SEM observation (b) TEM observation of the nano-grains at the bottom of the scratch (c) TEM observation of the mechanical twins at the bank of the scratch
Fig.3 EBSD analyses of cross-sectional deformation of the machined samples (Samples from #1 to #7 are arranged in order from left to right)[18] (a) band contrast (BC) map (b) inverse pole figure (IPF) (c) kernel average misorientation (KAM) map
Fig.4 TEM observations and analyses of the oxide scale formed on electropolished surface (EPS) (a, c) and colloidal silica slurry polished surface (CPS) (b, d) on 316L following the 500 h exposure in high temperature water[20] (a, b) TEM images and corresponding SAED patterns (insets) showing the cross-section of the oxide scale and the area analyzed (c, d) EDS mappings for O, Ni, Cr, and Fe, respectively
Fig.5 TEM bright-field corrosion morphology at the deformed zone of sample #5, with the inserted SAED pattern (a); high-angle annular dark field (HAADF) image of the deformation twin corrosion area (b); EDS mapping analyses of Cr, Fe, Ni, and O elements (c); EDS line scan analyses across the corroded deformation twin (d) (Under scanning transmission mode, the electron beam spot size is 1.5 nm, and the scanning step size is 2 nm)[18]
Fig.6 Stress corrosion carcking (SCC) cracks growth[35] (a) transgranular stress corrosion carcking (TGSCC) underneath a scratch (b) intergranular stress corrosion carcking (IGSCC) at scratch bank
Fig.7 Depth of intergranular oxide in strain-free and 3% strained specimens as a function of irradiation dose (PWR—pressurized water reactor, DH—dissolved hydrogen) (a), irradiation-assisted stress corrosion cracking (IASCC) susceptibility as measured by crack number and crack length per unit area as a function of irradiation dose (b)[46]
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