微合金钢中碳化物在奥氏体和铁素体中的沉淀析出动力学研究

郑亚旭; 杨钦; 赵紫玉; 魏翠虎; 回士旭; 吴康业

doi:10.7513/j.issn.1004-7638.2024.02.020

微合金钢中碳化物在奥氏体和铁素体中的沉淀析出动力学研究

doi: 10.7513/j.issn.1004-7638.2024.02.020

郑亚旭^{1, 2,},
杨钦¹,
赵紫玉^3, ,,
魏翠虎⁴,
回士旭²,
吴康业²

1.
河北科技大学材料科学与工程学院, 河北省材料近净成形技术重点实验室, 河北石家庄 050018
2.
盐城市联鑫钢铁有限公司, 江苏盐城 224003
3.
唐山科技职业技术学院, 河北唐山 063016
4.
中钢集团邢台机械轧辊有限公司, 河北唐山 063016

基金项目: 国家青年基金（52204341）；国家自然科学基金面上项目（52174311，52274332）；河北省钢铁联合基金（E2021208006，E2022208068）。

详细信息

作者简介:
郑亚旭，1983年出生，女，河北邢台人，博士，研究方向：钢铁材料强韧化，E-mail: zhengyaxu1984@163.com

通讯作者:
赵紫玉，1983年出生，女，河北唐山人，本科，讲师，研究方向：金属压力加工，E-mail: 281622734@qq.com

中图分类号: TF76, TG142.1
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- 被引次数: 0
出版历程
- 收稿日期: 2023-03-21
- 网络出版日期: 2024-04-30
- 刊出日期: 2024-04-30

Study on the precipitation kinetics of carbides in austenite and ferrite of microalloyed steels

Zheng Yaxu^{1, 2
,},
Yang Qin¹,
Zhao Ziyu^{3
, ,},
Wei Cuihu⁴,
Hui Shixu²,
Wu Kangye²

1.
School of Material Science and Engineering, Hebei University of Science and Technology, Hebei Key Laboratory of Material Near-net Forming Technology, Shijiazhuang 050018, Hebei, China
2.
Yancheng Lianxin Steel Co., Ltd., Yancheng 224003, Jiangsu, China
3.
Tangshan Vocational College of Science and Technology, Tangshan 063016, Hebei, China
4.
Sinosteel Xingtai Machinery & Mill Roll Co., Ltd., Xingtai 054025, Hebei, China

摘要

摘要: 根据多元复合析出相的固溶热力学计算和经典形核长大动力学理论，研究了Ti-Mo、Ti-Nb-Mo和Ti-Nb-Mo-V复合微合金化钢中碳化物在奥氏体(γ)和铁素体(α)中沉淀析出规律。研究表明，在γ区，Ti-Mo钢中析出相主要为富Ti的(Ti, Mo)C粒子，在较高温度区间，Ti-Nb-Mo和Ti-Nb-Mo-V钢中主要析出富Ti富Nb的碳化物粒子。在α区，Ti-Mo和Ti-Nb-Mo钢中析出相主要为富Mo的碳化物粒子，Ti-Nb-Mo-V钢主要析出富V的碳化物粒子。Ti-Mo、Ti-Nb-Mo钢中析出相在γ中沉淀析出的PTT曲线和NrT曲线分别呈“C”和反“C”形，而(Ti, Nb, Mo, V)C在奥氏体中沉淀析出NrT曲线呈反“ε”形，随着温度降低开始析出时间先缩短后延长。(Ti, Nb, Mo, V)C在高温奥氏体区形核速率最快，(Ti, Nb, Mo)C次之，(Ti, Mo)C最慢，且对应形核的最快析出温度依次升高。在铁素体区，(Ti, Mo)C和(Ti, Nb, Mo)C的PTT曲线和NrT曲线分别呈现“ε”形和反“ε”形。Ti-Nb-Mo-V钢中碳化物在整个铁素体区的形核速率快于Ti-Mo和Ti-Nb-Mo钢。
- 微合金钢 /
- 碳化物 /
- 热力学计算 /
- 析出动力学 /
- PTT曲线
Abstract: According to the solid solution thermodynamic calculation of the multi-composite precipitated phases and the classical nucleation growth kinetic theory, the deposition and precipitation of carbides in austenite (γ) and ferrite (α) phases in Ti-Mo, Ti-Nb-Mo and Ti-Nb-Mo-V composite microalloyed-steels were studied. It is shown that in γ phase, the precipitates in Ti-Mo steel are mainly Ti-enriched (Ti, Mo) C particles. In the higher temperature range, Ti-Nb-Mo and Ti-Nb-Mo-V steels mainly precipitate carbide particles enriched in Ti and Nb. In the ferritic zone, the precipitates in Ti-Mo and Ti-Nb-Mo steels are mainly Mo-enriched carbide particles, while in Ti-Nb-Mo-V steel, V-enriched carbide particles are mainly precipitated. The PTT and NrT curves of the precipitated phases in Ti-Mo and Ti-Nb-Mo steels show "C" and reverse "C" shapes, respectively, while the NrT curves of (Ti, Nb, Mo, V) C precipitated in austenite show reverse shapes "ε". As the temperature decreases, the precipitation time first decreases and then prolongs. The nucleation rate of (Ti, Nb, Mo, V) C is the fastest in the high-temperature austenitic zone, followed by (Ti, Nb, Mo) C, and that of (Ti, Mo) C is the slowest. The corresponding fastest nucleation precipitation temperature increases in sequence. In the ferritic region, the PTT and NrT curves of (Ti, Mo) C and (Ti, Nb, Mo) C are presented "ε" form and reverse "ε" shape, respectively. The nucleation rate of carbides in Ti-Nb-Mo-V steel is faster in the entire ferritic zone than in Ti-Mo and Ti-Nb-Mo steels.
- microalloy steel /
- carbides /
- thermodynamic calculation /
- precipitation kinetics /
- PTT curves

HTML全文

图 1 温度对Ti、Mo、Nb和V平衡固溶量的影响

Figure 1. Effect of temperature on equilibrium solid solution of Ti, Mo, Nb and V

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图 2 温度对钢中C平衡固溶量(a)和奥氏体中析出相体积分数(b)的影响

Figure 2. Effect of temperature on C equilibrium solid solution in steel (a) and volume fraction of the precipitated phases in austenite(b)

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图 3 化学式系数随温度变化的曲线

Figure 3. A curve of chemical formula coefficient as a function of temperature

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图 4 钢中碳化物在奥氏体中均匀形核的NrT曲线和PTT曲线

Figure 4. (a) NrT and (b) PTT curves of uniform nucleation of carbides in austenite in steels

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图 5 Ti-Mo、Ti-Nb-Mo和Ti-Nb-Mo-V钢中碳化物在奥氏体中位错线上形核的NrT曲线和PTT曲线

Figure 5. (a) NrT curves and (b) PTT curves of carbides nucleated in austenite dislocation lines in Ti-Mo, Ti-Nb-Mo and Ti-Nb-Mo-V steels

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图 6 铁素体区加热温度对Ti-Mo、Ti-Nb-Mo和Ti-Nb-Mo-V钢中微合金元素平衡固溶量的影响

Figure 6. Effect of heating temperature of ferritic zone on the equilibrium solid solution of microalloying elements in Ti-Mo, Ti-Nb-Mo and Ti-Nb-Mo-V steels

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图 7 温度对化学式系数的影响

Figure 7. Effect of temperature on chemical formula coefficients

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图 8 铁素体区温度对Ti-Mo、Ti-Nb-Mo和Ti-Nb-Mo-V钢中析出相体积分数的影响

Figure 8. Effect of ferritic zone temperature on volume fraction of precipitated phases in Ti-Mo, Ti-Nb-Mo and Ti-Nb-Mo-V steels

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图 9 试验钢中析出相在铁素体中均匀形核的的NrT曲线和PTT曲线

Figure 9. NrT and PTT curves of uniform nucleation of the precipitated phases in ferrite in experimental steels

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图 10 Ti-Mo、Ti-Nb-Mo和Ti-Nb-Mo-V钢中析出相在铁素体中位错线上形核的NrT曲线和PTT曲线

Figure 10. NrT curves and PTT curves of the precipitated phases nucleation on dislocations in ferrite in Ti-Mo, Ti-Nb-Mo and Ti-Nb-Mo-V steels

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表 1 Ti-Mo、Ti-Nb-Mo和Ti-Nb-Mo-V钢的主要化学成分

Table 1. Main chemical compositions of Ti-Mo, Ti-Nb-Mo and Ti-Nb-Mo-V steels %

编号	钢种	C	Si	Mn	N	Ti	Mo	Nb	V
1^#	Ti-Mo	0.07	0.23	1.5	0.003	0.1	0.28	0	0
2^#	Ti-Nb-Mo	0.09	0.23	1.5	0.003	0.1	0.28	0.07	0
3^#	Ti-Nb-Mo-V	0.11	0.23	1.5	0.003	0.1	0.28	0.07	0.25

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表 2 复合微合金钢中碳化物在奥氏体/铁素体中析出动力学的相关参数

Table 2. Parameters related to the precipitation kinetics of carbides in γ/α in composite microalloy steels

析出相		固溶度积	M元素的扩散激活能/kJ	点阵常数/nm	线胀系数$ \mathrm{\alpha }/{\mathrm{K}}^{-1} $
TiC	γ	2.75-7000/T	251	0.4318	$ 7.86\times {10}^{-6} $
TiC	α	4.4-9575/T	248	0.4318	$ 7.86\times {10}^{-6} $
NbC	γ	2.96-7510/T	266.5	0.4469	$ 7.02\times {10}^{-6} $
NbC	α	5.43-10960/T	252	0.4469	$ 7.02\times {10}^{-6} $
MoC	γ	4.251-3468/T	240	0.4277	$ 6.88\times {10}^{-6} $
MoC	α	6.163-7583/T	229	0.4277	$ 6.88\times {10}^{-6} $
VC	γ	6.72-9500/T	264	0.4182	$ 8.29\times {10}^{-6} $
VC	α	4.55-8300/T	241	0.4182	$ 8.29\times {10}^{-6} $

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表 3 Ti-Mo、T-Nb-Mo和Ti-Nb-Mo-V钢中碳化物在奥氏体中均匀形核的形核参量

Table 3. Uniform nucleation parameters of carbides in austenite in Ti-Mo, T-Nb-Mo and Ti-Nb-Mo-V steels

T/ ℃	Ti-Mo		Ti-Nb-Mo		Ti-Nb-Mo-V
T/ ℃	lg(I/K)	lg(t_{0.05 a}/t_{0 a})	lg(I/K)	lg(t_{0.05 a}/t_{0 a})	lg(I/K)	lg(t_{0.05 a}/t_{0 a})
700	−20.79	26.49	−21.50	27.20	−20.55	26.85
750	−20.56	25.68	−20.92	26.14	−20.63	26.21
800	−20.67	25.15	−20.53	25.27	−20.87	25.72
850	−21.28	25.01	−20.38	24.62	−20.89	25.13
900	−22.72	25.47	−20.53	24.22	−20.50	24.31
950	−25.85	27.10	−21.13	24.16	−20.25	23.63
1000	−33.14	31.54	−22.45	24.61	−20.66	23.45
1050	−55.11	45.80	−25.09	25.99	−22.02	23.96
1100	−194.45	138.33	−30.60	29.31	−25.04	25.61

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表 4 Ti-Mo、Ti-Nb-Mo和Ti-Nb-Mo-V钢中碳化物在奥氏体中位错线上形核的计算结果

Table 4. Calculation results of carbide nucleation in austenite dislocation line in Ti-Mo, Ti-Nb-Mo and Ti-Nb-Mo-V steels

T/ ℃	Ti-Mo		Ti-Nb-Mo		Ti-Nb-Mo-V
T/ ℃	lg(I/K)_d	lg(t_{0.05 da}/t_{0 da})	lg(I/K)_d	lg(t_{0.05 da}/t_{0 da})	lg(I/K)_d	lg(t_{0.05 da}/t_{0 da})
700	−15.90	22.41	−16.43	23.19	−16.08	23.13
750	−15.71	21.57	−16.17	22.25	−15.90	22.24
800	−15.74	21.00	−16.01	21.49	−15.95	21.65
850	−16.09	20.80	−16.00	20.93	−16.06	21.15
900	−17.03	21.25	−16.19	20.61	−16.03	20.57
950	−19.22	22.98	−16.70	20.66	−16.10	20.12
1000	−24.71	28.05	−17.74	21.28	−16.56	20.13
1050	−42.61	45.56	−19.83	22.98	−17.68	20.85
1100	−167.31	169.90	−24.29	27.09	−20.10	22.90

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表 5 试验钢中碳化物在铁素体中均匀形核的计算结果

Table 5. Calculation results of uniform nucleation of carbides in ferrite in experimental steels

T/℃	Ti-Mo		Ti-Nb-Mo		Ti-Nb-Mo-V
T/℃	lg(I/K)	lg(t_{0.05 a}/t_{0 a})	lg(I/K)	lg(t_{0.05 a}/t_{0 a})	lg(I/K)	lg(t_{0.05 a}/t_{0 a})
500	−64.57	57.76	−43.81	44.65	−25.71	32.34
550	−87.03	71.80	−54.66	50.90	−25.51	31.24
600	−129.97	99.61	−83.74	69.41	−25.38	30.31
650	−156.16	116.42	−137.18	104.27	−25.20	29.46
700	−70.89	59.21	−70.52	59.20	−25.27	28.85
750	−53.80	47.46	−51.04	45.66	−26.36	28.99
800	−62.22	52.60	−62.15	52.53	−29.61	30.60

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表 6 试验钢中碳化物在铁素体中位错线上形核的计算结果

Table 6. Calculation results of carbide nucleation in ferrite dislocation in experimental steels

T/℃	Ti-Mo		Ti-Nb-Mo		Ti-Nb-Mo-V
T/℃	lg(I/K)	lg(t_{0.05 a}/t_{0 a})	lg(I/K)	lg(t_{0.05 a}/t_{0 a})	lg(I/K)	lg(t_{0.05 a}/t_{0 a})
500	−31.79	41.50	−18.37	28.80	−16.1589	26.34
550	−47.79	56.56	−23.77	33.21	−15.4401	24.65
600	−81.13	89.09	−42.06	50.63	−14.8082	23.18
650	−103.85	111.15	−81.54	89.34	−14.2538	21.90
700	−40.7	47.64	−37.35	44.52	−13.7491	20.74
750	−30.17	36.75	−27.27	33.88	−13.2546	19.65
800	−36.86	42.97	−36.17	42.25	−12.7449	18.59

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