铸轧辊套表面超高速激光熔覆钴基熔覆层高温耐磨性能

尹燕; 李志慧; 李辉; 李治恒; 路超; 张瑞华

doi:10.12073/j.hjxb.20210122001

铸轧辊套表面超高速激光熔覆钴基熔覆层高温耐磨性能

尹燕^1,,
李志慧¹,
李辉^{2, 3},
李治恒⁴,
路超^{2, 3},
张瑞华^{2, 3}

1.
兰州理工大学，省部共建有色金属先进加工与再利用国家重点实验室，兰州，730050
2.
中国钢研科技集团有限公司，北京，100081
3.
阳江市五金刀剪产业技术研究院，阳江，529533
4.
新疆大学，乌鲁木齐，830047

基金项目: 阳江市高功率激光应用实验室建设(2018057)；海上风电高速激光熔覆防腐涂层制备工艺及应用(SDZX2020009)；粤东西北新型研发机构建设(20180902)

详细信息

作者简介:
尹燕，博士，教授；主要研究方向激光增材制造；Email：yinyan@lut.cn

中图分类号: TG 456.7
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出版历程
- 收稿日期: 2021-01-21
- 网络出版日期: 2021-12-01
- 刊出日期: 2021-09-29

High-temperature wear resistance of Co-based cladding layers by ultra-high speed laser cladding on the surface of the cast-rolling roller sleeve

YIN Yan^1,,
LI Zhihui¹,
LI Hui^{2, 3},
LI Zhiheng⁴,
LU Chao^{2, 3},
ZHANG Ruihua^{2, 3}

1.
State Key Laboratory of Advanced Processing and Recycling of Nonferrous Metals, Lanzhou University of Technology, Lanzhou, 730050, China
2.
Central Iron and Steel Research Institute, Beijing, 100081, China
3.
Yangjiang Hardware Knife Cut Industrial Technology Research Institute, Yangjiang, 529533, China
4.
Xinjiang University, Urumchi, 830047, China

摘要

摘要: 为了提高铸轧辊辊套的使用寿命，采用超高速激光熔覆技术在32Cr3Mo1V铸轧辊辊套表面制备了钴基熔覆层.分析了熔覆层的表面形貌、显微组织及高温摩擦磨损性能，并与优选常规激光熔覆层进行了对比. 结果表明，优选的超高速以及常规激光熔覆层均表面平整，与基体结合良好，无明显裂纹、气孔等缺陷. 超高速激光熔覆层显微组织非常均匀细小，枝晶轴间距极小，很大程度上抑制了枝晶偏析的范围，使得熔覆层的元素分布更加均匀. 在700 ℃高温摩擦磨损试验中，超高速激光熔覆层产生的氧化物磨屑更小，更容易发生团聚效应，有利于釉质层的形成，熔覆层变形量更小，对釉质层进行了有效支撑，出现大面积具有减摩耐磨作用的釉质层，表现出优异的耐高温摩擦磨损性能.
- 激光技术 /
- 超高速激光熔覆 /
- 钴基熔覆层 /
- 显微结构 /
- 高温摩擦磨损性能
Abstract: In order to improve the service life of the cast-rolling roller sleeve, a Co-based cladding layer was prepared on the surface of the 32Cr3Mo1V cast-rolling roller sleeve using ultra-high-speed laser cladding technology. The surface morphology, microstructure, high-temperature friction and wear properties of the cladding layer were analyzed. And which was compared with that of the preferred conventional laser cladding layer. The results show that the preferred ultra-high-speed and conventional laser cladding layers all have a smooth surface and a good combination with the substrate without obvious cracks, pores and other defects. In contrast, the microstructure of the layer by ultra-high-speed laser cladding is very uniform and fine. And the dendrite axis spacing is extremely small, which largely suppresses the range of dendrite segregation. As a result, the more uniform distribution of element was obtained. During the process of 700 ℃ high temperature friction and wear test, the super oxide wear debris produced from the high-speed laser cladding layer is more smaller compared with that of conventional laser cladding layer. Therefore the agglomeration effect is more likely to occur, which is conducive to the formation of the enamel layer with anti-friction resistance. As the same time, the deformation of the layer by ultra-high-speed laser cladding is smaller, which has more effectively support for the enamel layer, consequently a large area enamel layer can be obtained. Thus the ultra-high-speed laser cladding layer exhibits excellent high-temperature friction and wear resistance.
- laser technology /
- ultra-high speed laser cladding /
- Co-based cladding layers /
- microstructure /
- property of high-temperature friction and wear

HTML全文

图 1 试样A熔覆层的表面形貌和粗糙度

Figure 1. Surface morphology and roughness of Co-based coatings of sample A. (a) surface morphology; (b) surface roughness

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图 2 试样B熔覆层的表面形貌与粗糙度

Figure 2. Surface morphology and roughness of Co-based coatings of sample B. (a) surface morphology; (b) surface roughness

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图 3 熔覆层横剖面形貌

Figure 3. Cross-section morphology of cladding layer. (a) sample A; (b) sample B

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图 4 熔覆层中部组织 SEM 照片

Figure 4. SEM morphology of middle part of Co-basedcoatings. (a) sample A; (b) sample B

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图 5 试样A熔覆层元素过渡区的EDS分析结果

Figure 5. EDS analysis of element transition zone in cladding layer of sample A. (a) line scanning area; (b) element distribution

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图 6 试样B熔覆层元素过渡区的EDS分析

Figure 6. EDS analysis of element transition zone in cladding layer of sample B. (a) line scanning area; (b) element distribution

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图 7 熔覆层枝晶的显微组织形貌

Figure 7. Microstructure morphology of dendrites of Co-based coatings. (a) sample A; (b) sample B

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图 8 熔覆层与基材磨痕的OM照片

Figure 8. OM images of Co-based coatings and substrate wear scar. (a) substrate; (b) sample A; (c) sample B

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图 9 熔覆层与基材磨痕的SEM照片

Figure 9. SEM images of Co-based coatings and substrate wear scar. (a) substrate; (b) sample A; (c) sample B

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图 10 熔覆层与基材的摩擦系数

Figure 10. Friction coefficient of substrate and Co-based coatings

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图 11 熔覆层与基材的磨痕的中心深度

Figure 11. Center depth of Co-based coatings and substrate wear scar. (a) substrate; (b) sample A; (c) sample B

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图 12 熔覆层与基材磨痕的平面投影形貌

Figure 12. Plane projection topography of Co-based coatings and substrate wear scar. (a) substrate; (b) sample A; (c) sample B

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图 13 熔覆层与基材的磨损体积

Figure 13. Wear volume of Co-based coatings and substrate

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表 1 Co基合金粉末的化学成分(质量分数，%)

Table 1 Chemical composition of Co-based powder

C	Cr	Si	Fe	W	Ni	Mo	Mn	Co
1.14	29.95	1.26	1.92	5.47	2.31	0.65	0.24	余量

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表 2 优化后的激光熔覆工艺参数

Table 2 Optimized laser cladding process parameters

试样	功率 P/kW	熔覆速度 v/(m·min⁻¹)	离焦量 f/mm	搭接率 η(%)
A	2.5	15	5	83
B	1.35	0.6	5	50

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表 3 图7中不同点EDS分析结果(质量分数, %)

Table 3 Result of EDS analyse for different points in Fig.7

位置	Co	Cr	Fe	Si	C
a	58.17	24.81	5.67	0.95	5.51
b	46.81	31.83	3.68	0.73	10.37
c	40.61	19.84	25.88	1.06	6.17
d	25.64	27.68	16.96	—	12.59

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表 4 图9中不同点EDS成分分析(质量分数, %)

Table 4 EDS analyse of the elements at different points in Fig.9

位置	Co	Cr	O	Ni	Fe	W	Si	C
e	—	16.51	24.33	—	59.15	—	—	—
f	—	1.29	27.37	—	68.03	—	—	3.31
g	40.79	16.91	23.15	—	14.31	1.95	—	2.89
h	32.57	16.15	25.62	—	17.39	2.36	0.74	4.9
i	30.32	19.24	24.67	4.57	12.68	3.04	1.04	1.09
j	39.47	14.56	23.69	3.28	10.48	2	0.85	5.67

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