充氢时间对QP980钢拉伸性能和断裂行为的影响

doi:10.12068/j.issn.1005-3026.2026.20240129

摘要/Abstract

摘要：

采用电化学充氢与慢应变速率拉伸（SSRT）实验研究充氢时间对QP980钢复相组织氢脆特性的影响.应力-应变曲线结果表明，随充氢时间延长，抗拉强度与延伸率显著下降，但氢的存在不影响断裂前的加工硬化速率.断口形貌分析表明，在无氢情况下，试样中部为韧窝与准解理混合断裂，边缘部分为韧窝断裂；充氢后试样的混合断裂区增大，且随充氢时间的延长，准解理单元刻面尺寸增大.通过二次裂纹和组织观察发现，当氢浓度较低时，铁素体与马氏体的相界面成为裂纹源主要位置，裂纹沿马氏体与铁素体相界面扩展并被铁素体钝化，形成微孔缩聚式裂纹，表明此时氢致局部塑性理论(HELP)为氢脆主导机制；当氢浓度较高时，裂纹转变为发丝状裂纹并穿过基体铁素体组织内部，表明氢致弱键理论(HEDE)为主导机制.

关键词: QP980钢, 充氢, 氢致裂纹, 慢应变速率拉伸, 氢脆机制

Abstract:

The effect of hydrogen charging time on the hydrogen embrittlement （HE） of the multiphase microstructure of QP980 steel was studied by electrochemical hydrogen charging and slow strain rate tensile （SSRT） tests. The stress-strain curve shows that the tensile strength and elongation decrease significantly with the increase of hydrogen charging time， but the presence of hydrogen does not affect the work hardening rate before fracture. The fracture morphology analysis shows that in the absence of hydrogen， the fracture mode at the center of the specimen is a mixed dimple and quasi-cleavage， and the edge region exhibits a dimple fracture morphology. After hydrogen charging， the mixed fracture zone of the specimen expands， and the unit facet size of quasi-cleavage increases with prolonged hydrogen charging time. Observations of secondary cracks and microstructure revealed that at lower hydrogen concentrations， the phase interfaces between ferrite and martensite served as the primary sites for crack initiation. These cracks propagated along the ferrite-martensite interfaces but were blunted by the ferrite phase， resulting in microvoid-coalescence type cracks. This indicates that the hydrogen-enhanced localized plasticity （HELP） mechanism was the dominant hydrogen embrittlement mechanism under these conditions. When hydrogen concentration is high， the cracks transform into hairline cracks and pass through the matrix ferrite structure， indicating that the hydrogen-enhanced decohesion （HEDE） is the dominant mechanism.

Key words: QP980 steel, hydrogen charging, hydrogen-induced crack, slow strain rate tensile, hydrogen embrittlement mechanism

中图分类号:

TG 142.1

阮昕懿, 尹晶晶, 常智渊, 兰亮云. 充氢时间对QP980钢拉伸性能和断裂行为的影响[J]. 东北大学学报（自然科学版）, 2026, 47(1): 115-122.

Xin-yi RUAN, Jing-jing YIN, Zhi-yuan CHANG, Liang-yun LAN. Effect of Hydrogen Charging Time on Tensile Properties and Fracture Behavior of QP980 Steel[J]. Journal of Northeastern University(Natural Science), 2026, 47(1): 115-122.

图/表 8

图1 QP980钢的SEM显微组织F—铁素体，M—马氏体，RA—残余奥氏体.

Fig.1 SEM microstructure of QP980 steel

图2 二次裂纹的观察位置

Fig.2 Observation location of secondary cracks

图3 QP980钢的慢应变速率拉伸实验结果（a）—应力-应变曲线；（b）—加工硬化速率-真应变曲线.

Fig.3 SSRT test results of QP980 steel

表1 试样抗拉强度和延伸率损失率 (elongation loss rate %)

Table 1 Specimen’s tensile strength and

变量	损失率
变量	HC-2h	HC-12h	HC-24h	HC-24h/24h
抗拉强度	13.1	27.6	31.4	4.9
延伸率	52.5	75.3	76.2	0.0

图4 不同充氢时间下试样表面断口形貌（a）—HF断口；（b）—HF断口A区域；（c）—HF断口B区域；（d）—HC-2h断口；（e）—HC-2h断口A区域；（f）—HC-2h断口B区域；（g）—HC-24h断口；（h）—HC-24h断口A区域；（i）—HC-24h断口B区域；（j）—HC-24h/24h断口；（k）—HC-24h/24h断口A区域；（l）—HC-24h/24h断口B区域.

Fig.4 Surface fracture morphology of specimens under different hydrogen charging time

图5 断口附近中心截面的二次裂纹与组织形态（a）—HF宏观图；（b）—HF中心组织；（c）—HF组织C区域放大视图；（d）—HC-2h宏观图；（e）—HC-2h中心组织；（f）—HC-2h组织C区域放大视图；（g）—HC-24h宏观图；（h）—HC-24h中心组织；（i）—HC-24h组织C区域放大视图；（j）—HC-24h/24h宏观图；（k）—HC-24h/24h中心组织；（l）—HC-24h/24h组织C区域放大视图.

Fig.5 Secondary cracks and microstructure of central section near fracture surface

图6 不同充氢时间下基体裂纹形貌（a）—HC-2h；（b）—HC-24h.

Fig.6 Crack morphology of matrix under different hydrogen charging time

图7 不同充氢时间下QP980钢氢致断裂过程及氢脆机制（a）—短时间充氢；（b）—长时间充氢.

Fig.7 Hydrogen-induced fracture process and HE mechanism of QP980 steel under different hydrogen charging time

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