冷轧变形量及退火温度对纯钛无缝管组织及性能影响

李晓煜; 程小伟; 肖强; 唐敏; 刘昕; 李露; 秦回一

doi:10.7513/j.issn.1004-7638.2025.01.009

冷轧变形量及退火温度对纯钛无缝管组织及性能影响

doi: 10.7513/j.issn.1004-7638.2025.01.009

李晓煜^{1, 2,},
程小伟^{1, 2},
肖强^{1, 2},
唐敏^{1, 2},
刘昕^{1, 2},
李露³,
秦回一³

1.
钒钛资源综合利用国家重点实验室, 四川攀枝花 617000
2.
成都先进金属材料产业技术研究院股份有限公司, 四川成都 610300
3.
攀钢集团江油长城特殊钢有限公司, 四川江油 621701

详细信息

作者简介:
李晓煜，1985年出生，河南平顶山人，女，博士，高级工程师，主要从事钛合金材料研究，E-mail：lxy_rwth@163.com

中图分类号: TF823
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出版历程
- 收稿日期: 2024-02-05
- 刊出日期: 2025-02-27

Influences of cold rolling deformation and annealing temperature on the microstructures and properties of pure titanium seamless tubes

LI Xiaoyu^{1, 2
,},
CHENG Xiaowei^{1, 2},
XIAO Qiang^{1, 2},
TANG Min^{1, 2},
LIU Xin^{1, 2},
LI Lu³,
QIN Huiyi³

1.
State Key Laboratory of Vanadium and Titanium Resources Comprehensive Utilization, Panzhihua 617000, Sichuan, China
2.
Chengdu Institute of Advanced Metallic Materials Technology and Industry Co., Ltd., Chengdu 610300, Sichuan, China
3.
Jiangyou Changcheng Special Steel Co., Ltd. of Pangang Group, Jiangyou 621701, Sichuan, China

摘要

摘要: 对两种不同冷轧变形量的TA1纯钛管采用不同温度（450、470、490 ℃）进行退火处理，研究了变形量及退火温度对纯钛管微观组织形貌、织构演变及力学性能的影响。结果表明：小变形量纯钛冷轧管内部存在大量孪晶，主要以{$ \text{11}\bar {\text{2}}\text{2} $}<$ 1\text{1}\bar {\text{2}}\bar {\text{3}}\text{ > } $压缩孪晶和{$ \text{10}\bar {\text{1}}\text{2} $}$ \text{ < 10}\bar {\text{1}}\text{1 > } $拉伸孪晶为主。增大变形量，纯钛冷轧管晶粒变形严重，孪晶数量减少且以压缩孪晶为主。大变形量冷轧管具有强烈的<$ \text{10}\bar {\text{1}}\text{0} $>//AD织构，而小变形量冷轧管以基面双峰织构为主。随着退火温度升高，大变形量无缝管再结晶含量逐渐增加。经490 ℃退火处理后，大变形量纯钛管再结晶程度达到50.5%，抗拉强度显著降低，同时冷轧变形织构变弱，基面双峰织构增强。而小变形无缝管退火后组织变化不明显，强度下降趋势平缓，组织由基面双峰织构逐渐向<$ \text{10}\bar {\text{1}}\text{0} $>//AD织构转变。
- 冷轧变形 /
- TA1 /
- 退火温度 /
- 组织演变 /
- 力学性能
Abstract: Pure titanium tubes with different cold rolling deformations were annealed at different temperatures (450、470、490 ℃) to investigate the influences of deformations and annealing temperatures on the microstructures, texture evolution and mechanical properties of tubes. It is shown that the microstructure of the cold-rolled tubes with small deformation contains a great amount of twins, which mainly consist of {$ \text{11}\bar {\text{2}}\text{2} $}<$1 \text{1}\bar {\text{2}}\bar {\text{3}}\text{ > } $ compression twins and {$ \text{10}\bar {\text{1}}\text{2} $}$ \text{ < 10}\bar {\text{1}}\text{1 > }\text{} $tensile twins. The grains in the cold-rolled tubes with the greater deformation were severely deformed, along with the reduction of twins amount which is dominated by compression twins. The microstructure of tubes with the large deformation shows a strong texture of <$ \text{10}\bar {\text{1}}\text{0} $>//AD, and the other tube with small deformation shows a basal bimodal basal texture. The recrystallization proportion of the pure titanium tube, which is more severely deformed, increases gradually with the increase in annealing temperatures and its ratio reaches 50.5% after 490 ℃ annealing. Meanwhile, the tensile strength of the strongly deformed tubes decreases dramatically after 490 ℃ annealing, with the weakening of the cold-rolled texture and intensifying of the bimodal basal texture. The microstructural change of seamless tubes with the small deformation is not obvious, with a gentle reduction of the tensile strength, and the texture changes gradually from the bimodal basal texture to <$ \text{10}\bar {\text{1}}\text{0} $>//AD texture with the increase in annealing temperatures.
- cold rolling deformation /
- TA1 /
- annealing temperature /
- microstructural evolution /
- mechanical properties

HTML全文

图 1 取样位置示意

Figure 1. Schematic diagram of sampling

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图 2 不同退火温度下纯钛管纵向组织

Ø25 mm×2 mm：（a）冷轧态；（b）450 ℃；（c）470 ℃；（d）490 ℃；Ø57 mm×5 mm：（e）冷轧态；（f）450 ℃；（g）470 ℃；（h）490 ℃

Figure 2. Longitudinal microstructures of pure titanium tubes annealed at different temperatures

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图 3 不同退火温度下纯钛管IPF图

Ø25 mm×2 mm：（a）冷轧态；（b）450 ℃；（c）470 ℃；（d）490 ℃；Ø57 mm×5 mm：（e）冷轧态；（f）450 ℃；（g）470 ℃；（h）490 ℃

Figure 3. IPF diagrams of pure titanium tubes annealed at different temperature

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图 4 不同退火温度下纯钛管晶界取向差分布

Ø25 mm×2 mm：（a）冷轧态；（b）450 ℃；（c）470 ℃；（d）490 ℃；Ø57 mm×5 mm：（e）冷轧态；（f）450 ℃；（g）470 ℃；（h）490 ℃

Figure 4. Misorientation distribution of pure titanium tubes with different annealing temperatures

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图 5 纯钛管的{0001}和{$ \text{10}\bar {\text{1}}\text{0} $}极图

Ø25 mm×2 mm：（a）冷轧态；（b）450 ℃；（c）470 ℃；（d）490 ℃；Ø57 mm×5 mm：（e）冷轧态；（f）450 ℃；（g）470 ℃；（h）490 ℃

Figure 5. Pole figures of {0001} and {$ \text{10}\bar {\text{1}}\text{0} $} of pure titanium tubes

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图 6 不同退火温度对纯钛管拉伸性能影响

(a)抗拉强度；(b)延伸率

Figure 6. Influence of annealing temperature on the tensile properties of pure titanium tubes

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表 1 TA1钛合金铸锭化学成分

Table 1. Chemical composition of the TA1 ingot %

Fe	C	N	H	O	Ti
0.034	0.005	0.003	0.006	0.032	Bal.

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表 2 不同变形量纯钛管的组织特征

Table 2. Microstructural characterization of pure titanium tubes with different deformation degrees

钛管规格 / mm	退火温度/ ℃	平均晶粒尺寸/μm	再结晶分数/%	孪晶占比/%
钛管规格 / mm	退火温度/ ℃	平均晶粒尺寸/μm	再结晶分数/%	压缩孪晶 {$ \text{11}\bar {\text{2}}\text{2} $} $ < 1 \text{1}\bar {\text{2}}\bar {\text{3}} > $	拉伸孪晶 {$ \text{10}\bar {\text{1}}\text{2} $} $ < 10\bar {\text{1}}1 > $
Ø25×2	初始态	3.41	1.7	2.08	0.73
	450	3.50	11.6	1.31	0.77
	470	3.45	27.0	1.82	0.98
	490	3.67	50.5	1.64	0.96
Ø57×5	初始态	4.71	0.7	2.10	2.51
	450	4.31	1.3	2.35	2.67
	470	4.79	1.5	2.53	2.73
	490	4.79	5.3	2.11	2.24

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