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

doi:10.11900/0412.1961.2020.00141

Acta Metall Sin

2020, Vol. 56

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

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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

Cite this article:

ZHU Jian, ZHANG Zhihao, XIE Jianxin. Plastic Deformation Behavior and Fracture Mechanism of Rare Earth H13 Steel Based on In Situ TEM Tensile Study. Acta Metall Sin, 2020, 56(12): 1592-1604.

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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

Received: 06 May 2020

ZTFLH:

TG11

Fund: National Key Research and Development Program of China(2016YFB0300900);National Natural Science Foundation of China-Liaoning Joint Fund(U1708251)

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	Jian ZHU
	Zhihao ZHANG
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https://www.ams.org.cn/EN/10.11900/0412.1961.2020.00141 OR https://www.ams.org.cn/EN/Y2020/V56/I12/1592

Fig.1 Shape and size of in situ tensile specimen (Circle in the middle of specimen shows the location of central double-jet electropolishing perforation)

Fig.2 Bright-field (a, c) and dark-field (b, d) TEM images of rare earth H13 steel specimen after heat treatment (RA—retained austenite. Insets in Figs.2b and d show the selected area electron diffraction (SAED) patterns)

Fig.3 Bright-field TEM images of the fine structure of rare earth H13 steel specimen after heat treatment (GBs—grain boundaries)

Fig.4 TEM images showing crack morphologies of in situ tensile specimen of rare earth H13 steel (TD—tensile direction, FD—fracture direction)

Fig.5 TEM images showing the microstructure evolutions of in situ tensile specimen of rare earth H13 steel during tensile process when tensile displacement increased from 48.3 μm to 110.7 μm (a~f), respectively

Fig.6 TEM images of area near main crack of in situ tensile specimen of rare earth H13 steel

Fig.7 SEM images of main crack and selected area post-mortem EBSD analyses near crack edge of in situ tensile specimen of rare earth H13 steel

Fig.8 Post-mortem EBSD analyses of selected areas G1 (b~d) and G2 (e~g) near main crack of in situ tensile specimen of rare earth H13 steel

Fig.9 Orientation distributions of martensite and parent austenite of selected areas G1 (a~c) and G2 (d~f) in Fig.8a near main crack of in situ tensile specimen of rare earth H13 steel

Fig.10 Orientation reconstruction results of martensite and parent austenite of selected areas G1 (a~c) and G2 (d~f) near main crack of in situ tensile specimen of rare earth H13 steel (green line: block boundary, red line: packet boundary, black line: parent austenite grain boundary, PAGB)

Fig.11 Post-mortem EBSD data calculation results of selected areas G1 (a~c) and G2 (d~f) near main crack of in situ tensile specimen of rare earth H13 steel (black line: PAGB, white line: 5°<θ<15°, red line:15°≤θ≤45°, green line: θ>45°, color bars of Figs.11c and f show indexes of variant numbers, insets in Figs.11c and f show the indexed variants)

Fig.12 Length fractions of inter-variant boundaries for selected areas G1 and G2 near main crack of in situ tensile specimen of rare earth H13 steel

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