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Acta Metall Sin  2020, Vol. 56 Issue (12): 1581-1591    DOI: 10.11900/0412.1961.2020.00124
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Effect of Hot Rolling Deformation on Microstructure and Mechanical Properties of a High-Ti Wear-Resistant Steel
XU Shuai1, SUN Xinjun1(), LIANG Xiaokai1, LIU Jun2, YONG Qilong1
1 Department of Structural Steels, Central Iron & Steel Research Institute, Beijing 100081, China
2 Jiangyin Xingcheng Special Steel Co., Ltd., Jiangyin 214400, China
Cite this article: 

XU Shuai, SUN Xinjun, LIANG Xiaokai, LIU Jun, YONG Qilong. Effect of Hot Rolling Deformation on Microstructure and Mechanical Properties of a High-Ti Wear-Resistant Steel. Acta Metall Sin, 2020, 56(12): 1581-1591.

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Abstract  

To improve the wear performance of steel without increasing its hardness, a high-Ti wear-resistant steel was reinforced with TiC particles. The effects of hot rolling deformation on the microstructure and mechanical properties of the wear-resistant steel containing 0.61%Ti after quenching and tempering were studied in hot rolling experiments with different reduction ratios. The steel products were subjected to microstructure and precipitate characterization and mechanical-property tests. Increasing the rolling deformation improved the strength, toughness, and plasticity of the tested steel. The yield strength, tensile strength, and total elongation were increased from 1202 MPa, 1437 MPa, and 7.4%, respectively, at a reduction ratio of 3∶1 to 1311 MPa, 1484 MPa, and 9.9%, respectively, at a reduction ratio of 30∶1. Meanwhile, increasing the reduction ratio from 3∶1 to 10∶1 remarkably increased the absorbed energy at room temperature (obtained in a Charpy impact test) from 11 J to 24 J. As the rolling deformation increased, the micron-sized net-like TiC particles that precipitated during solidification were gradually refined and homogenized, and the prior austenite grain size was also refined. Next, the strengthening mechanisms of the steel were quantitatively analyzed. The yield strength, calculated by adding the root mean squares of the dislocation and precipitate strengthening values, well agreed with the measured yield strength. The increasing yield strength of the tested steel at higher rolling reduction ratios is mainly attributable to increased grain-boundary strengthening and precipitation strengthening. As the strength of the steel increased, the toughness and plasticity also increased, mainly because the large TiC particles were refined and homogenized during the rolling deformation.

Key words:  high-Ti wear-resistant steel      rolling reduction ratio      TiC precipitation      mechanical property      strengthening mechanism     
Received:  17 April 2020     
ZTFLH:  TG142  
Fund: National Key Research and Development Program of China(2017YFB0305100)

URL: 

https://www.ams.org.cn/EN/10.11900/0412.1961.2020.00124     OR     https://www.ams.org.cn/EN/Y2020/V56/I12/1581

Fig.1  Schematic of rolling and heat treatment process of high-Ti wear-resistant steel (W.Q.—water quenching, A.C.—air cooling)
Sample No.The actual thickness of the plate after each pass / mmTotal reduction ratio
90-3090-72-58-(950 ℃)-44-35-(850 ℃)-303∶1
90-1890-72-58-(950 ℃)-44-33-(850 ℃)-24-185∶1
90-1290-72-58-(950 ℃)-44-33-24-18-(850 ℃)-14-127.5∶1
90-990-72-58-(950 ℃)-44-33-24-18-(850 ℃)-13-910∶1
90-390-72-58-(950 ℃)-44-33-24-18-13-9-(850 ℃)-6-4-330∶1
Table 1  Rolling process of high Ti wear-resistant steel with different rolling deformations
Fig.2  SEM images of matrix microstructure in high-Ti wear-resistant steel samples No.90-30 (a), No.90-18 (b), No.90-12 (c), No.90-9 (d) and No.90-3 (e)
Fig.3  OM images of prior-austenite microstructures in high-Ti wear-resistant steel samples No.90-30 (a), No.90-18 (b), No.90-12 (c), No.90-9 (d) and No.90-3 (e)
Fig.4  OM images of TiC particles in as-cast high-Ti wear-resistant steel (a) and samples No.90-30 (b), No.90-18 (c), No.90-12 (d), No.90-9 (e) and No.90-3 (f)
Sample No.

Volume fraction

%

Average area

μm2

Average diameter

μm

Maximum diameter

μm

Aspect ratio
90-301.1110.193.0713.672.85
90-181.099.312.8511.842.47
90-121.078.452.669.962.21
90-91.087.872.579.122.03
90-31.107.222.518.081.94
Table 2  Metallographic statistics of TiC particles in high-Ti wear-resistant steel
Fig.5  TEM images of TiC precipitate in samples No.90-30 (a), No.90-12 (b) and No.90-3 (c), and HRTEM image (d), SAED pattern (e) and EDS result (f) of TiC particle in sample No.90-12 (d(111)—interplanar spacing of (111))
Fig.6  TiC particle diameter distributions of sample No.90-18 measured by quantitative metallography (a) and SAXS (b)
Fig.7  TiC particle diameter distribution of high-Ti wear- resistant steel with different rolling processes
Fig.8  Strength (a), elongation (b) and Charpy impact absorbed energy (c) of high-Ti wear-resistant steel with different rolling processes
Sample No.σ0ΔσpΔσdΔσsΔσgΔσp2+Δσd2σy(6)σy(7)σy(exp)
90-305780410466230418149511711202
90-185777406466256413152211921217
90-1257142424466290447165012601220
90-957165425466295456168012741227
90-357176436466347470174113401311
Table 3  Various strengthening increments and comparisons of yield strengths between the experimental and calculated results with Eqs.(6) and (7) in high-Ti wear-resistant steel with different rolling processes
Fig.9  XRD spectra of high-Ti wear-resistant steel with different rolling processes(a) full peaks pattern(b) local magnification pattern of (200) diffraction peak
Sample No.FWHM / (°)Dislocation density 1015 m-2
(110)(200)(211)
90-300.3190.6090.6132.154
90-180.3200.5710.5852.116
90-120.3450.5980.6182.301
90-90.3370.6080.6262.311
90-30.3470.6430.6132.443
Table 4  Dislocation density and full wave at half maximum (FWHM) in high-Ti wear-resistant steel with different rolling processes
Fig.10  SEM image (a) and EDS result (b) of TiC particle in fracture morphology
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