Interaction Mechanism of Dislocation and Hydrogen in Austenitic 316 Stainless Steel

doi:10.11900/0412.1961.2020.00332

Acta Metall Sin

2021, Vol. 57

Issue (7): 913-920 DOI: 10.11900/0412.1961.2020.00332

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Interaction Mechanism of Dislocation and Hydrogen in Austenitic 316 Stainless Steel

AN Xudong¹^,², ZHU Te¹, WANG Qianqian¹^,², SONG Yamin¹, LIU Jinyang¹, ZHANG Peng¹, ZHANG Zhaokuan¹, WAN Mingpan²(

), CAO Xingzhong¹(

)

^1.Institute of High Energy Physics, Chinese Academy of Sciences, Beijing 100049, China
^2.College of Materials and Metallurgy, Guizhou University, Guiyang 550025, China

Cite this article:

AN Xudong, ZHU Te, WANG Qianqian, SONG Yamin, LIU Jinyang, ZHANG Peng, ZHANG Zhaokuan, WAN Mingpan, CAO Xingzhong. Interaction Mechanism of Dislocation and Hydrogen in Austenitic 316 Stainless Steel. Acta Metall Sin, 2021, 57(7): 913-920.

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Abstract

The formation of hydrogen-induced defects in 316 stainless steel and the interaction between hydrogen and defects are crucial aspects to understand the failure law of the hydrogen-induced mechanical properties. Introducing various types of hydrogen sinks, such as interfaces and dislocations, is a popular method for reducing the concentration of residual hydrogen and curbing the mobility of hydrogen atoms in materials. In this work, positron annihilation spectroscopy and thermal desorption spectroscopy (TDS) were used to measure the distribution of hydrogen-induced defects and hydrogen content in deformed 316 stainless steel with hydrogen charging. In particular, the influence of dislocations on the formation of hydrogen-induced defects and the hydrogen retention behavior in the specimens were experimentally investigated. The results show that the S-parameter increases upon hydrogen charging, and the W-parameter is negatively correlated with the S-parameter. The S-parameter value of the deformed sample was found to be larger than that of the annealed sample, indicating that the introduction of hydrogen results in the formation of vacancy defects in the sample. Additionally, hydrogen atoms may gather together to form a large number of volume defects near dislocations. The S-W curves show that the (S, W) point for the sample containing dislocations aggregates towards the surface after hydrogen charging, due to the hindered dislocation motion. In the deformed samples with low hydrogen charge current density, the vacancy formation rate was found to be slow, and the combination of excess hydrogen and vacancies was observed to give rise to hydrogen-vacancy clusters (H_mV_n), where n > m. The TDS results show that both the activation energy for hydrogen desorption and the amount of hydrogen retention increase due to the presence of dislocations.

Key words: austenitic 316 stainless steel dislocation hydrogen damage positron annihilation spectroscopy

Received: 28 August 2020

ZTFLH:

TG142.25

Fund: National Key Research and Development Program of China(2019YFA0210002);Natural Science Foundation of China(11775235、U1732265)

About author: WAN Mingpan, associate professor, Tel: 18984135926, E-mail: mpwan@gzu.edu.cn.
CAO Xingzhong, professor, Tel: (010)88233393, E-mail: caoxzh@ihep.ac.cn.

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	Xudong AN
	Te ZHU
	Qianqian WANG
	Yamin SONG
	Jinyang LIU
	Peng ZHANG
	Zhaokuan ZHANG
	Mingpan WAN
	Xingzhong CAO

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https://www.ams.org.cn/EN/10.11900/0412.1961.2020.00332 OR https://www.ams.org.cn/EN/Y2021/V57/I7/913

Table 1 Annealing conditions and electrochemical hydrogen charging parameters of austenitic 316 stainless steel

Fig.1 S-E (a) and ΔS-E (b) curves of 316 stainless steel samples after hydrogen charging under different annealing conditions and hydrogen charging conditions of electrochemical cathode (S—the positron and free electron annihilation information, E—the positron incident energy, ΔS—the increment of S, ΔS₂—the difference of S parameters between No.1 and No.2, ΔS₄—the difference of S parameters between No.3 and No.4)

Fig.2 S-W curves of hydrogen charging of austenitic 316 stainless steel at different annealing conditions (W—the annihilation information between positrons and high-momentum electrons)

Fig.3 S-E (a) and ΔS-E (b) curves of austenitic 316 stainless steel under different hydrogen charging conditions after annealing at 500^oC for 1 h (ΔS₅— the difference of S parameters between No.3 and No.5, ΔS₆—the difference of S parameters between No.3 and No.6)

Fig.4 W-E (a) and ΔW-E (b) curves of austenitic 316 stainless steel under different hydrogen charging conditions after annealing at 500^oC for 1 h (ΔW—the increment of W, ΔW₄—the difference of W parameters between No.3 and No.4, ΔW₅—the difference of W parameters between No.3 and No.5, ΔW₆—the difference of W parameters between No.3 and No.6)

Fig.5 XRD spectra of austenitic 316 stainless steel under different hydrogen charging conditions after annealing at 500^oC for 1 h

Fig.6 S-W curves of austenite 316 stainless steel under different hydrogen charging conditions after annealing at 500^oC for 1 h

Fig.7 Thermal hydrogen desorption spectra of hydrogen charged austenitic 316 stainless steel

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