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Acta Metall Sin  2016, Vol. 52 Issue (2): 224-232    DOI: 10.11900/0412.1961.2015.00280
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EFFECT OF RETAINED AUSTENITE ON DUCTILITY AND TOUGHNESS OF A LOW ALLOYED MULTI-PHASE STEEL
Zhenjia XIE,Chengjia SHANG(),Wenhao ZHOU,Binbin WU
School of Materials Science and Engineering, University of Science and Technology Beijing, Beijing 100083, China
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Zhenjia XIE,Chengjia SHANG,Wenhao ZHOU,Binbin WU. EFFECT OF RETAINED AUSTENITE ON DUCTILITY AND TOUGHNESS OF A LOW ALLOYED MULTI-PHASE STEEL. Acta Metall Sin, 2016, 52(2): 224-232.

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Abstract  

High performance steels require not only high strength, but also the combination of high ductility, high toughness and good weldability. Retained austenite in multi-phase steels has been widely reported to be helpful for obtaining high strength, high ductility and high toughness. In this work, steel with multi-phase microstructure consisting of intercritical ferrite, tempered martensite/bainite and different volume fractions retained austenite was obtained by intercritical annealing and tempering at 600~680 ℃. The volume fractions of retained austenite were 2%, 5%, 10% for samples tempered at 600, 650 and 680 ℃, respectively. The effect of retained austenite on ductility and toughness was studied in detail. Results showed that there was no obvious change in strength by varying the volume fraction of retained austenite, yield strength of the steel was 540~590 MPa, tensile strength was 720~780 MPa. Retained austenite could largely improve both the ductility and toughness of the steel. With increasing the volume fraction of retained austenite from 2% to 10%, the uniform elongation and total elongation were enhanced from 10.3% and 23.8% to 20.4% and 33.8%, respectively. The underlying reason for the improvement of ductility was attributed to the transformation induced plasticity of retained austenite by providing sustainable high work hardening rate. The improvement of toughness by retained austenite became more obvious when testing temperature was lower. When impact test temperature was higher than -60 ℃, the Charpy impact energy of samples with 2%~10% retained austenite were larger than 120 J. When test temperature was -80 ℃, Charpy impact energy of sample with 2% retained austenite decreased to 14 J, while that of sample with 10% retained austenite remained as 60~80 J when test temperature was as low as -80 and -100 ℃. Results from instrument impact test indicated that retained austenite was helpful for enhancing plasticity before crack initiation at low temperature, leading to improvement of crack initiation energy, resulting in excellent low temperature toughness.

Key words:  multi-phase steel      retained austenite      ductility      low temperature toughness     
Received:  27 May 2015     
Fund: Supported by National Basic Research Program of China (No.2010CB630801)

URL: 

https://www.ams.org.cn/EN/10.11900/0412.1961.2015.00280     OR     https://www.ams.org.cn/EN/Y2016/V52/I2/224

Fig.1  SEM images for experimental steel after firstly austenitization and quenching (a), secondly intercritical annealing (b), thirdly tempering at 600 ℃ (c), 650 ℃ (d) and 680 ℃ (e)
Fig.2  EBSD images for experimental steel after tempering at 600 ℃ (a), 650 ℃ (b) and 680 ℃ (c)
Fig.3  XRD spectra for experimental steel after tempering at different temperatures (fγ—volume fraction of retained austenite; T600, T650 and T680 correspond to experimental steel tempered at 600, 650 and 680 ℃, respectively)
Fig.4  Bright-field (a) and dark-field (b) TEM images of retained austenite for experimental steel after tempering at 680 ℃ (Inset in Fig.4b shows the SAED pattern)
Sample σs / MPa σb / MPa Au / % A / % Ev / J
-40 ℃ -80 ℃
T600 596 746 10.3 23.8 133 14
T650 590 720 16.0 31.8 142 30
T680 541 783 20.4 33.8 122 65
Table 1  Mechanical properties of experimental steel after tempering at different temperatures
Fig.5  Charpy impact energies at different temperatures for experimental steel after tempering at 600 and 680 ℃
Fig.6  Fracture morphologies near V-notch root (a, c, e) and crack propagation area far away from V-notch (b, d, f) for experimental steel after tempering at 600 ℃ (a, b), 650 ℃ (c, d) and 680 ℃ (e, f)
Fig.7  Instantaneous work hardening exponent (n*) versus true strain (ε) curves for experimental steel after tempering at different temperatures
Fig.8  Load and absorbed energy versus displacement for experimental steel tempered at 600 and 680 ℃ after impact test at -80 ℃
Fig.9  EBSD images far away from (a) and near (b) fracture for experimental steel tempered at 680 ℃ after impact test at -80 ℃
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