EFFECT OF METASTABLE AUSTENITE ON MECHANI-CAL PROPERTY AND MECHANISM IN CRYOGENICSTEEL APPLIED IN OCEANEERING

doi:10.11900/0412.1961.2015.00312

Acta Metall Sin

2016, Vol. 52

Issue (4): 385-393 DOI: 10.11900/0412.1961.2015.00312

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EFFECT OF METASTABLE AUSTENITE ON MECHANI-CAL PROPERTY AND MECHANISM IN CRYOGENICSTEEL APPLIED IN OCEANEERING

Changjun WANG¹(

),Jianxiong LIANG¹,Zhenbao LIU¹,Zhiyong YANG¹,Xinjun SUN²,Qilong YONG²

1 Institute of Special Steels, Central Iron and Steel Research Institute, Beijing 100081, China
2 Institute of Engineering Steels, Central Iron and Steel Research Institute, Beijing 100081, China

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Changjun WANG,Jianxiong LIANG,Zhenbao LIU,Zhiyong YANG,Xinjun SUN,Qilong YONG. EFFECT OF METASTABLE AUSTENITE ON MECHANI-CAL PROPERTY AND MECHANISM IN CRYOGENICSTEEL APPLIED IN OCEANEERING. Acta Metall Sin, 2016, 52(4): 385-393.

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Abstract

With the development of marine resources and its emerging markets, the marine equipments such as offshore drilling platform, subsea oil and gas transportation pipeline, and storage equipment of oil and gas are developing actively. It is urgent to develop a new type of steel with low cost and excellent toughness to satisfy the demand of marine equipment. In this work, the morphology of austenite and phase transition process in medium manganese steel during quenching and tempering (QT) and quenching, lamellarizing and tempering (QLT) heat treatments were investigated by using EBSD, HRTEM and thermal dilatometer. The results show that the discrepancy of stability in austenite caused by its shape, size and location leads to the more excellent toughness during QLT heat treatment compared to QT. It has been found from thermodynamical and dynamical viewpoint that the formation rates of reverted austenite during QLT heat treatment are significantly larger relative to QT due to the partition process of C and Mn elements in the lamellarizing stage. Moreover, two growth models of film-type reverted austenite are distinct during two heat treatments: the unidimensional two-sided growth mode during QT and unidimensional one-sided growth mode during QLT.

Key words: reverted austenite low temperature toughness thermal dilatometer growth model

Received: 15 June 2015

Fund: Supported by National Basic Research Program of China (No.2014CB643306)

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	Changjun WANG
	Jianxiong LIANG
	Zhenbao LIU
	Zhiyong YANG
	Xinjun SUN
	Qilong YONG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2015.00312 OR https://www.ams.org.cn/EN/Y2016/V52/I4/385

Fig.1 Schematics of heat treatment process of quenching+lamellarizing+tempering (QLT) (a) and quenching+tempering (QT) (b) for experimental steel (A_C1—austenitic start transformation temperature, A_C3—austenitic finish transformation temperature)

Fig.2 Tensile properties of tested steels under different heat treatments at room temperature

Fig.3 Impact energy (A_kv) of tested steels under different heat treatments and temperatures

Fig.4 Graphs of band contrast (BC) (a, d), grain boundaries with austenite (b, e) and bcc and fcc phases (c, f) of tested steel after QT (a~c) and QLT (d~f) treatments (Blue and black lines in Figs.4b and e represent grain orientation angles which are between 5°~15° and larger than 15°, respectively; blue color in Figs.4c and f represents bcc phase, red color in Figs.4b, c, e and f represents fcc phase)

Fig.5 Bright-field TEM images (a, c) and SAED patterns (b, d) of tested steel after QT (a, b) and QLT (c, d) treatments

Fig.6 TEM image of reverted austenite (a) and EDS analysis of Mn scanning along the line in Fig.6a (b) of tested steel after QLT heat treatment

Fig.7 Dilatation curve of tested steel during QLT process (a) and XRD spectra of retained austenite at each state (b) (M_s—martensitic start transformation temperature, M_f—martensitic finish transformation temperature, L—length, ΔL—length change)

Fig.8 SEM images (a, c) and EDS analysis scanning along the lines in Figs.8a and c (b, d) of tested steel after water quenching (Q) (a, b) and QL (c, d) treatments

Fig.9 Driving force of tested steel in the transformation of ferrite and cementite to austenite as a function of Mn concentration at 650 ℃

Fig.10 Effect of Mn concentration in tested steels on semi-thickness of austenite S_A as a function of time at 650 ℃

Fig.11 Comparison between calculated and measured thicknesses of austenite after QT and QLT treatments

Fig.12 Schematic of microstructure evolution of tested steel under QLT treatment

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