Effect of Annealing Process on Microstructure Evolution and Hydrogen Embrittlement Behavior of 304 Austenitic Stainless Steel

doi:10.11902/1005.4537.2024.078

Journal of Chinese Society for Corrosion and protection

2025, Vol. 45

Issue (2): 438-448 DOI: 10.11902/1005.4537.2024.078

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Effect of Annealing Process on Microstructure Evolution and Hydrogen Embrittlement Behavior of 304 Austenitic Stainless Steel

ZHANG Huiyun¹(

), ZHENG Liuwei², LIANG Wei²

^1.Department of Mecharical Marfacturing Engineering, Shanxi Engineering Vocational College, Taiyuan 030009, China
^2.School of Materials Science and Engineering, Taiyuan University of Technology, Taiyuan 030024, China

Cite this article:

ZHANG Huiyun, ZHENG Liuwei, LIANG Wei. Effect of Annealing Process on Microstructure Evolution and Hydrogen Embrittlement Behavior of 304 Austenitic Stainless Steel. Journal of Chinese Society for Corrosion and protection, 2025, 45(2): 438-448.

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Abstract

The effect of different annealing processes on microstructure evolution and hydrogen embrittlement sensitivity of 304 austenitic stainless steel was studied. The results show that after being subjected to annealing within the reverse phase of martensite transformation, the content of martensite as a rapid diffusion channel of hydrogen decreases continuously, correspondingly, the hydrogen content decreases, as a result, the hydrogen embrittlement sensitivity of the steel decreases. After annealing within the recovery and recrystallization stage, the dislocation density decreases, the fine equiaxed grains appear, the hydrogen content decreases, and thus the hydrogen embrittlement sensitivity of the steel also decreases. However, after annealing within the grain growth stage, the hydrogen content per unit area of grain boundaries increases, and the hydrogen embrittlement sensitivity of the steel increases. As a whole, after annealing treatment within the recovery and recrystallization stage, the 304 austenitic stainless steel present better comprehensive properties.

Key words: austenitic stainless steel anneal inverse martensite transformation recovery and recrystallization hydrogen embrittlement sensitivity

Received: 11 March 2024 32134.14.1005.4537.2024.078

TG337.5

Fund: Science and Technology Innovation Project of Colleges and Universities in Shanxi Province(2024L592);the Project of "Unveiling the List and Taking Charge" of Shanxi Engineering Vocational College in 2024(KY2024-1);the Research Project of Teaching Reform and Practice of Vocational Education in Shanxi Province(202303022)

Corresponding Authors: ZHANG Huiyun, E-mail: 245883278@qq.com

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https://www.jcscp.org/EN/10.11902/1005.4537.2024.078 OR https://www.jcscp.org/EN/Y2025/V45/I2/438

Fig.1 Schematic diagrams of electrochemical hydrogen charging device (a) and tensile specimen (b)

Fig.2 IPF maps (a, c, e) and phase distribution maps (b, d, f) of CR-20% (a, b), 700 ^oC-1 min (c, d) and 700 ^oC-3 min (e, f) samples

Fig.3 Stress-strain curves (a) and HE sensitivities (b) of CR-20%, 700 ^oC-1 min and 700 ^oC-3 min samples before and after hydrogen charging

Fig.4 Hydrogen desorption rates of CR-20%, 700 ^oC-1 min and 700 ^oC-3 min samples as a function of temperature

Fig.5 BC (a, c, e) and IPF (b, d, f) maps of 700 ^oC-5 min (a, b), 700 ^oC-10 min (c, d) and 800 ^oC-10 min (e, f) samples

Fig.6 KAM maps (a, c, e) and KAM values (b, d, f) of 700 ^oC-5 min (a, b), 700 ^oC-10 min (c, d) and 800 ^oC-10 min (e, f) samples

Fig.7 Recrystallization images (a, c, e) and corresponding fractions (b, d, f) of 700 ^oC-5 min (a, b), 700 ^oC-10 min (c, d) and 800 ^oC-10 min (e, f) samples

Fig.8 Stress-strain curves of 700 ^oC-5 min, 700 ^oC-10 min and 800 ^oC-10 min samples before and after hydrogen charging (a), and their HE sensitivities (b)

Fig.9 Hydrogen desorption rates of 700 ^oC-5 min, 700 ^oC-10 min and 800 ^oC-10 min samples as a function of temperature

Fig.10 BC maps (a, b), KAM maps (c, d), IPF maps (e, f), and grain sizes (g, h) of 900 ^oC-30 min (a, c, e, g) and 1000 ^oC-60 min (b, d, f, h) samples

Fig.11 Stress-strain curves of 900 ^oC-30 min and 1000 ^oC-60 min samples before and after hydrogen charg-ing (a), and their HE sensitivities (b)

Fig.12 Hydrogen desorption rates of 900 ^oC-30 min and 1000 ^oC-60 min samples as a function of temperature

Sample	d / μm	S_v / m²·m^-3	X_H / mg·kg^-1	X $H G B$ / g·m^-2
900 ^oC-30 min	20.01	1.0 × 10⁵	5.48	4.3 × 10^-4
1000 ^oC-60 min	30.35	6.59 × 10⁴	3.91	4.7 × 10^-4

Table 1 Summary of the grain size (d), grain boundary area per unit volume (S_v), content of diffusible hydrogen (X_H), and hydrogen content per unit grain boundary area (X

H G B

) obtained by calculation under an assumption that all hydrogen atoms locate at grain boundaries

Fig.13 Fracture morphologies of 900 ^oC-30 min sample (a, c) and 1000 ^oC-60 min sample (b, d) after hydrogen charging

Table 2 Comparisons of various performances of 304 austenitic stainless steel in different states

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