基于原位<strong>TEM</strong>拉伸的稀土<strong>H13</strong>钢塑性形变行为和断裂机制

doi:10.11900/0412.1961.2020.00141

金属学报

2020, Vol. 56

Issue (12): 1592-1604 DOI: 10.11900/0412.1961.2020.00141

本期目录 | 过刊浏览

基于原位TEM拉伸的稀土H13钢塑性形变行为和断裂机制

朱健¹, 张志豪¹^,²(

), 谢建新¹^,²

1 北京科技大学新材料技术研究院北京 100083
2 北京科技大学材料先进制备技术教育部重点实验室北京 100083

Plastic Deformation Behavior and Fracture Mechanism of Rare Earth H13 Steel Based on In Situ TEM Tensile Study

ZHU Jian¹, ZHANG Zhihao¹^,²(

), XIE Jianxin¹^,²

1 Institute for Advanced Materials and Technology, University of Science and Technology Beijing, Beijing 100083, China
2 Key Laboratory for Advanced Materials Processing (MOE), University of Science and Technology Beijing, Beijing 100083, China

引用本文:

朱健, 张志豪, 谢建新. 基于原位TEM拉伸的稀土H13钢塑性形变行为和断裂机制[J]. 金属学报, 2020, 56(12): 1592-1604.
Jian ZHU, Zhihao ZHANG, Jianxin XIE. Plastic Deformation Behavior and Fracture Mechanism of Rare Earth H13 Steel Based on In Situ TEM Tensile Study[J]. Acta Metall Sin, 2020, 56(12): 1592-1604.

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摘要:

采用原位TEM拉伸结合离位EBSD分析，研究了稀土H13钢在拉伸过程中的组织演化和裂纹扩展行为。结果表明，稀土H13钢拉伸试样晶界处的应力集中和粗大的颗粒状夹杂物是裂纹萌生的主要来源；拉伸过程中多处裂纹萌生后汇聚成较大的主裂纹，主裂纹沿着与拉伸方向垂直的方向扩展到试样边缘，主裂纹具有“Z”字形的锯齿状特征。裂纹附近区域的应力分布不均匀，与应力相对较低的区域相比，应力相对较高区域的V1/V2变体对的晶界长度分数从56.5%增加到58.8%，V1/V3&V5变体对的晶界长度分数从16.3%增加到21.6%；变体对的晶界长度分数增加表明了孪生马氏体含量的提高，从而有效缓解晶界处的应力集中，有利于减少裂纹萌生并提高塑韧性。拉伸过程中，稀土H13钢试样晶界处的残余奥氏体发生应力诱导相变；马氏体基体内的位错发生大量增殖，并在大角度晶界和碳化物析出处形成明显的位错塞积，其中晶界处的位错塞积促进了残余奥氏体的应力诱导相变。

关键词 ：稀土H13钢, 断裂机制, 原位TEM拉伸, 母相奥氏体取向重构, 马氏体变体

Abstract：

Fatigue failure caused by crack propagation is one of the main failure modes of H13 die steel. Because H13 die steel is mainly used under operational conditions involving high-pressure cycling or high friction, its crack initiation and propagation behavior play a critical role in fatigue failure. However, to the best of the authors' knowledge, few reports on the direct observation of deformation and crack propagation behavior of H13 die steel exist, which limits the understanding of the fracture mechanism of H13 die steel. In this work, an in situ TEM tensile study combined with post-mortem EBSD analysis was employed to investigate the microstructure evolution and crack propagation behavior of rare earth (RE) H13 steel. Results indicate that the stress concentration at the grain boundaries and coarse granular inclusions in the tensile specimen were the main sources of crack initiation. After crack initiation and during the tensile process, many cracks converged into the main crack. The main crack propagated along the direction perpendicular to the tensile direction, exhibiting zigzag-shaped features. The stress distribution in the area near a crack in a specimen was heterogeneous; the length fraction of V1/V2 inter-variant boundaries in the relatively high-stress area increased from 56.5% to 58.8% compared with the relatively low-stress area, and the length fraction of V1/V3&V5 inter-variant boundaries increased from 16.3% to 21.6%. The increase in the length fraction of V1/V2 inter-variant boundaries indicated an increase in the twin martensite fraction, which effectively relieved the stress concentration at the grain boundaries and reduced crack initiation. During the tensile process, the austenite retained at the grain boundaries underwent stress-induced phase transformation and was partially transformed into V1/V2 and V1/V3&V5 variant pairs. The dislocation propagation in martensite contributed to dislocation pile-up at high-angle grain boundaries and carbide precipitation. Moreover, the dislocation pile-up at the high-angle grain boundaries promoted the stress-induced phase transformation of the retained austenite.

Key words： rare earth H13 steel fracture mechanism in situ TEM tension parent austenite orientation reconstruction martensite variant

收稿日期: 2020-05-06

ZTFLH:

TG11

基金资助:国家重点研发计划项目(2016YFB0300900);国家自然科学基金-辽宁联合基金项目(U1708251)

作者简介: 朱健，男，1993年生，博士生

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图1 原位拉伸试样形状和尺寸

图2 稀土H13钢热处理试样马氏体基体的明场像、暗场像和选区电子衍射(SAED)花样(a, b) retained austenite films (c, d) blocky retained austenite

图3 稀土H13钢热处理试样精细组织的TEM明场像(a) dislocation (b) precipitate (c) twin martensite(d) enlarged view of square area in Fig.3c (e) GBs (f) stacking fault

图4 稀土H13钢原位拉伸试样裂纹形貌的TEM像(a) main crack area I (b) main crack area II (c) secondary crack area

图5 拉伸杆行程由48.3 μm增加到110.7 μm时稀土H13钢原位拉伸试样微观组织形貌演化的TEM像(a) microvoid initiated from GBs and dislocation pile-up at GBs(b) dislocations across GBs and dislocation pile-up at carbides (c, d) dislocation wall, dislocation tangle and dislocation cell formed in different grains (e, f) newly formed dislocation pile-up at GBs and carbide

图6 稀土H13钢原位拉伸试样主裂纹附近区域微观组织的TEM像(a) crack initiated from the triple boundaries and dislocation free zone (DFZ)(b) dislocation pile-up and microvoid at carbide(c) DFZ and crack initiations along GBs (d~f) microvoid at carbide with size of 0.2 μm

图7 稀土H13钢原位拉伸试样主裂纹形貌的SEM像和裂纹边缘选区的离位EBSD分析Color online(a) left area of central perforation(b) right area of central perforation(c) Kikuchi band contrast map of square area in Fig.7b(d) phase distribution (red: retained austenite, blue: martensite)(e) inverse pole figure (IPF)

图8 稀土H13钢原位拉伸试样主裂纹边缘G1和G2选区的离位EBSD分析Color online(a) parent austenite orientation reconstruction (b, e) Kikuchi band contrast maps (c, f) phase maps (d, g) IPFs

图9 稀土H13钢原位拉伸试样主裂纹边缘G1和G2选区的马氏体和母相奥氏体取向分布Color online(a, d) parallel orientation relation between [1ˉ1ˉ1]α and [1ˉ01]γ directions (b, e) stereographic projection for parent austenite and martensite (c, f) parallel orientation relation between (011)α plane and (111)γ plane

图10 稀土H13钢原位拉伸试样主裂纹边缘G1和G2选区的马氏体和母相奥氏体取向重构计算结果Color online(a, d) boundary distributions (b, e) parent austenite orientation reconstructions (c, f) grain maps

图11 稀土H13钢原位拉伸试样主裂纹边缘G1和G2选区的离位EBSD数据计算结果Color online(a, d) band slopes of Kikuchi zone (b, e) twin distribution images (c, f) variant pairs distributions

图12 稀土H13钢原位拉伸试样主裂纹边缘G1和G2选区的变体对的晶界长度分数

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