Kinetics of (Ti, V, Mo)C Precipitated in γ /α Matrix of Ti-V-Mo Complex Microalloyed Steel

doi:10.11900/0412.1961.2018.00011

Acta Metall Sin

2018, Vol. 54

Issue (8): 1122-1130 DOI: 10.11900/0412.1961.2018.00011

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Kinetics of (Ti, V, Mo)C Precipitated in γ /α Matrix of Ti-V-Mo Complex Microalloyed Steel

Ke ZHANG^1,²(

), Xinjun SUN³, Mingya ZHANG^1,², Zhaodong LI³, Xiaoyu YE⁴, Zhenghai ZHU^1,², Zhenyi HUANG^1,², Qilong YONG³

1 School of Metallurgical Engineering, Anhui University of Technology, Maanshan 243032, China
2 Key Laboratory of Metallurgical Emission Reduction & Resources Recycling, Ministry of Education, Anhui University of Technology, Maanshan 243032, China;
3 Institute of Structural Steels, Central Iron and Steel Research Institute, Beijing 100081, China
4 State Key Laboratory of Vanadium and Titanium Resources Comprehensive Utilization, Panzhihua Group Co., Ltd., Panzhihua 617000, China

Cite this article:

Ke ZHANG, Xinjun SUN, Mingya ZHANG, Zhaodong LI, Xiaoyu YE, Zhenghai ZHU, Zhenyi HUANG, Qilong YONG. Kinetics of (Ti, V, Mo)C Precipitated in γ /α Matrix of Ti-V-Mo Complex Microalloyed Steel. Acta Metall Sin, 2018, 54(8): 1122-1130.

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Abstract

In recent years, in order to develop the higher strength steel, the idea of increasing the strength of the hot rolled ferritic steel via complex Ti microalloyed technology has been widely accepted and applied, such as Ti-Nb, Ti-Mo, Ti-Nb-Mo and Ti-V-Mo. It is important to know the thermodynamics and kinetics of complex Ti contained precipitates for controlling the precipitation behavior of carbides and improving the mechanical properties of complex Ti microalloyed steels. In this work, according to the classical nulceation and growth kinetics theory and the solubility products of various carbides in austenite/ferrite (γ /α) matrix, the precipitation-time-temperature (PTT) curve, nucleation-time (NrT) curve and the nucleation parameters of (Ti, V, Mo)C carbides in γ /α matrix of Ti-V-Mo complex microalloyed steel were obtained through the theoretical calculation. Moreover, the effects of deformation stored energy and the amount of strain-induced precipitation in γ matrix on the precipitation kinetics of (Ti, V, Mo)C were discussed. The results showed that the PTT diagrams of (Ti, V, Mo)C in γ /α matrix showed "C" shape curve, while the NrT curves showed inverse "C" shape curve. The nose temperature of (Ti, V, Mo)C in γ matrix is about 1020~1050 ℃. Increasing the deformation stored energy of γ matrix moves the PPT curve to the upper left. In addition, the NrT curve of (Ti, V, Mo)C precipitated in α matrix moves towards to the lower right by properly increasing the amount of strain-induced precipitation in γ matrix. The maximum nucleation rate temperature of (Ti, V, Mo)C in ferrite is around 630~650 ℃ from the theoretical calculation, which agrees well with the result of experimental observation.

Key words: (Ti,V,Mo)C PTT curve NrT curve kinetics theoretical calculation

Received: 10 January 2018

ZTFLH:

TG142.1

Fund: Supported by National Natural Science Foundation of China (Nos.51704008 and 51674004), National Key Research and Development Program of China (Nos.2017YFB0305100 and 2017YFB0304700), National Basic Research Program of China (No.2015CB654803), Science and Technology Foundation of China Iron & Steel Research Institute Group (No.15G60530A), Youth Scientific Research Foundation of Anhui University of Technology (No.QZ201603) and the Opening Foundation of State Key Laboratory of Vanadium and Titanium Resources Comprehensive Utilization (No.18100009)

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	Articles by authors
	Ke ZHANG
	Xinjun SUN
	Mingya ZHANG
	Zhaodong LI
	Xiaoyu YE
	Zhenghai ZHU
	Zhenyi HUANG
	Qilong YONG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2018.00011 OR https://www.ams.org.cn/EN/Y2018/V54/I8/1122

Table 1 Activation energies of Ti, V and Mo in γ and α matrix^[15]

Table 2 Lattice constants and linear expansion coefficients of TiC, VC and MoC at room temperature^[21,23,24]

Fig.1 Changes of balance contents of solid solution [Ti], [V], [Mo] and [C] of microalloyed elements with temperature in Ti-V-Mo steel

Temperature	0 Jmol^-1			1360 Jmol^-1			3820 Jmol^-1
℃	$d d *$ / nm	lg(I/K)_d	lg(t_0.05/t₀)	$d d *$ / nm	lg(I/K)_d	lg(t_0.05/t₀)	$d d *$ / nm	lg(I/K)_d	lg(t_0.05/t₀)
800	0.46	-15.180	20.83	0.41	-15.07	20.72	0.30	-15.13	20.78
850	0.55	-15.125	20.18	0.49	-14.86	19.91	0.39	-14.65	19.71
900	0.62	-15.135	19.62	0.55	-14.72	19.20	0.45	-14.34	18.82
950	0.67	-15.041	18.98	0.59	-14.53	18.47	0.48	-14.04	17.98
1000	0.73	-15.043	18.49	0.64	-14.40	17.84	0.51	-13.78	17.23
1050	0.83	-15.519	18.53	0.72	-14.56	17.57	0.57	-13.66	16.67
1100	1.02	-17.024	19.64	0.87	-15.30	17.92	0.66	-13.77	16.39
1150	1.37	-21.270	23.54	1.11	-17.38	19.65	0.80	-14.31	16.58
1200	2.17	-36.908	38.85	1.58	-23.73	25.68	1.04	-15.89	17.84

Table 3 Calculation results of nucleation parameters of (Ti, V, Mo)C at different deformation energies in austenite

Fig.2 NrT (a) and PTT (b) curves of (Ti, V, Mo)C precipitated in austenite

Table 4 The fastest precipitation temperatures (T_f) of carbides in austenite of various Ti microalloyed steels

Table 5 Calculation results of nucleation parameters of (Ti, V, Mo)C in ferrite under strain induced precipitation 10%, 30% and 50%

Fig.3 Influences of the amount of strain induced precipitation on NrT (a) and PTT (b) curves of (Ti, V, Mo)C in ferrite under different strain induced precipitations at 920 ℃

Fig.4 Variations of hardness as a function of coiling temperatures for the Ti-V-Mo, Ti-Mo and Ti steels

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