Research Progress on the Influence of Metastable Austenite on the Fracture Toughness of High-Strength Steels

doi:10.11900/0412.1961.2024.00142

Acta Metall Sin

2025, Vol. 61

Issue (1): 77-87 DOI: 10.11900/0412.1961.2024.00142

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Research Progress on the Influence of Metastable Austenite on the Fracture Toughness of High-Strength Steels

TANG Jingtao, YAO Yingjie, ZHANG Youyou, WU Wenhua, LI Yubo, CHEN Hao(

), YANG Zhigang

Key Laboratory of Advanced Materials of Ministry of Education, School of Materials Science and Engineering, Tsinghua University, Beijing 100084, China

Cite this article:

TANG Jingtao, YAO Yingjie, ZHANG Youyou, WU Wenhua, LI Yubo, CHEN Hao, YANG Zhigang. Research Progress on the Influence of Metastable Austenite on the Fracture Toughness of High-Strength Steels. Acta Metall Sin, 2025, 61(1): 77-87.

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Abstract

Incorporating metastable austenite is the one of the key strategies for achieving synergistic improvement in the strength and ductility of high-strength steels. Through in situ deformation-induced martensitic transformation during tensile loading, metastable austenite can delay necking while enhancing work-hardening capacity. Concurrently, ultrahigh-strength steel components are facing increasing demands in terms of lightweightness and service in complex environments; hence, they will be required to have a higher fracture toughness without compromising strength. Research has focused on incorporating the tougher austenite phase in high-strength steels to improve their fracture toughness and preserve ductility. Metastable austenite contributes to enhanced fracture toughness through transformation toughening and its interactions with cracks, which can deflect or blunt cracks. However, freshly formed martensite, a product of martensitic transformation, can reduce the toughening effect or even deteriorate fracture toughness due to its inherent brittleness and effect on the local stress state. This paper reviews recent research progress on the relationship between metastable austenite and fracture toughness of high-strength steels, examining the toughening and embrittlement mechanisms of the phase. In addition, it outlines future design principles for metastable austenite incorporation in high-strength steels to achieve synergistic improvements in strength and toughness.

Key words: metastable austenite fracture toughness phase transformation

Received: 07 May 2024

ZTFLH:

TG142

Fund: National Key Research and Development Program of China(2022YFE0110800);National Natural Science Foundation of China(52201011);National Natural Science Foundation of China(51922054)

Corresponding Authors: CHEN Hao, professor, Tel: (010)62781646, E-mail: hao.chen@mail.tsinghua.edu.cn

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	TANG Jingtao
	YAO Yingjie
	ZHANG Youyou
	WU Wenhua
	LI Yubo
	CHEN Hao
	YANG Zhigang

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https://www.ams.org.cn/EN/10.11900/0412.1961.2024.00142 OR https://www.ams.org.cn/EN/Y2025/V61/I1/77

Fig.1 Ashby plot showing the strength-ductility trade-off of some high-strength steels (For example: twinning-induced plasticity(TWIP) steel^[38,39], duplex steel^[40-42], transformation-induced plasticity(TRIP)-aided steel^[43,44], secondary hardening steel^[45-49], and Maraging steel^[50-52])

Fig.2 Transformation zone schematics of energy adsorption theory (a) and crack tip shielding theory (b), crack propagation resistance curve predicted by transformation toughening theory (c), and the dependence of toughening behavior on the critical transformation stress (d) (h—semi-major axis of the elliptical transformation zone, βh—semi-minor axis of the elliptical transformation zone, r—distance between the edge of transformation zone and the crack tip, θ—angle between the line which originates from the crack tip connecting the transformation-zone edge, and the crack plane, ΔK_I—increment of the stress intensity factor resulted by phase transformation, $Δ K I C$ —critical value of ΔK_I, Δa—crack length, $K I C$ —type I stress intensity factor, σ_M—critical stress for martensitic transformation)

Fig.3 Contour maps of strain triaxiality distributions exposed to different TRIP treatments and with varying carbon concentrations^[57] ( $ε 33 c t$ —through-thickness strain, I'—axis: horizontal distance from the crack tip, h'—vertical distance from the crack tip)

Fig.4 Cracking as a consequence of the fresh martensite produced by retained austenite phase transformation
(a) martensite cleavage^[57]
(b) martensite-martensite interfacial cracking^[57] (c, d) martensite-matrix interfacial cracking^[56,57] (Where orange arrows in Fig.4d point to martensite-matrix interface decohesion while green arrows show martensite cracking)

Fig.5 Changes of energy release rate ( $G I C γ$ ) due to phase transformation, corresponding evaluated $G I C γ$ from energy adsorption theory, and the carbon concentration in retained austenite varying with quenching & partitioning process^[77] (The sample axis represents the quenching & partitioning parameters, e.g. QP260(60) indicates partitioning at 260 ^oC for 60 min)

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