金属包覆FeCuNi粉末对金刚石工具胎体性能的影响

曹新民; 鲍丽; 李振; 程传卫; 陈鹏; 潘建军; 于奇; 于新泉; 陈生超

doi:10.13394/j.cnki.jgszz.2022.0174

金属包覆FeCuNi粉末对金刚石工具胎体性能的影响

doi: 10.13394/j.cnki.jgszz.2022.0174

曹新民^1,,
鲍丽¹,
李振²,
程传卫³,
陈鹏⁴,
潘建军¹,
于奇¹,
于新泉¹,
陈生超^5, ,

1.
郑州机械研究所有限公司, 郑州 450001
2.
郑州新兴产业技术研究促进中心, 郑州 450001
3.
郑州市科技创新服务中心, 郑州 450001
4.
河南信大融合科技有限公司, 郑州 450001
5.
郑机所(郑州)传动科技有限公司, 郑州450001

基金项目: 国家自然科学基金“超多元组分钎料的逆向强化调控机制及其钎焊行为”（52005452）。

详细信息

作者简介:
曹新民，男，1969年生，本科。主要研究方向：制备金刚石工具用混料、冷压、热压及相关成套设备，金刚石工具用合金粉末。E-mail：zzjxyjs@126.com

通讯作者:
陈生超，男，1987年生，在读博士，工程师。主要研究方向：金属材料及热处理。E-mail：csc19871012@163.com

中图分类号: TG74
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- 文章访问数: 27
- HTML全文浏览量: 19
- PDF下载量: 6
- 被引次数: 0
出版历程
- 收稿日期: 2022-10-23
- 修回日期: 2023-10-08
- 录用日期: 2023-10-08
- 网络出版日期: 2024-11-20
- 刊出日期: 2024-10-01

Effect of metal coated FeCuNi powder on properties of diamond tool matrix

1.
Zhengzhou Research Institute of Mechanical Engineering Co., Ltd., Zhengzhou 450001, China
2.
Zhengzhou Emerging Industry Technology Research and Promotion Center, Zhengzhou 450001, China
3.
Zhengzhou Science and Technology Innovation Service Center, Zhengzhou 450001, China
4.
Henan Xinda Fusion Technology Co., Ltd., Zhengzhou 450001, China
5.
ZRIME Gearing Technology Co., Ltd., Zhengzhou 450001, China

摘要

摘要: 为解决Co基金刚石工具成本高，Fe基金刚石工具烧结温度高、把持力弱、胎体易烧死等问题，通过化学法将Cu、Sn、Bi等金属分别包覆于FeCuNi合金粉末表面，制备成金属包覆FeCuNi合金粉末。结果表明：配方中添加金属包覆FeCuNi合金粉末后，三点抗弯强度提高近20%；金属包覆FeCuNi合金粉末烧结过程中，FeCuNi颗粒表面的Sn、Bi率先熔化，与Cu反应形成的Cu-Sn、Cu-Bi等液相能够形成连续的网络状结构，将FeCuNi、Fe、Ni等颗粒包裹和黏结，使得金刚石工具胎体的成分和组织结构分布更加均匀、更加致密，避免了成分偏析的发生。通过以上试验得到初步结论，金属包覆FeCuNi合金粉末可等效替代贵重金属Co，极大地降低金刚石工具生产成本，具有显著的经济效益。
- 金刚石工具 /
- 金属包覆FeCuNi合金粉末 /
- 胎体
Abstract: Objectives: Diamond tools are widely used in fields such as oil drilling, geological exploration, and stone processing, among which sintered metal bond diamond tools have become the most representative due to their wide applicability and strong durability. Cobalt (Co) has become the preferred material for preparing diamond tools due to its excellent physical properties, but its price is relatively expensive. As market competition gradually intensifies, the application range of Co is becoming limited. It has been found that Fe-based pre-alloy powder has similar properties to Co and can be used as an important way to reduce costs. However, Fe-based diamond tools face problems such as high sintering temperature, narrow controllable process range, easy erosion of diamond, weak holding force, and the tendency for the matrix to burn during production. Additionally, the Sn element is prone to segregation and loss during long-term sintering in the furnace, resulting in unstable performance of diamond tools. This article describes the preparation of FeCuNi-Cu/Sn/Bi alloy powder using a multi-layer coating process to improve the densification of diamond matrix sintering and reduce component segregation. Methods: Co powder, Cu powder, Fe powder, Sn powder, Ni powder, and FeCuNi alloy powder were selected, and Cu, Sn, and Bi were respectively plated onto the surface of FeCuNi alloy powder by chemical methods, forming a uniform coating on the surface. Metal powder and diamond were mixed using a three-dimensional mixer for 2 hours. After mixing, the required weight of uniform powder was weighed, and sample blocks with dimensions of 4 mm × 8 mm × 40 mm were prepared using a hot press sintering machine. The mold material was graphite, and 4 sample blocks were prepared for each group. The experiment was repeated twice. For the tested materials, Rockwell hardness was measured, as well as the three-point bending strength. The microstructure and energy spectrum were analyzed using an electron microscope, and the changes in composition, structure, and mechanical properties of the tire body with fewer joints under different processes were compared and analyzed. Four formulations of sintered diamond tool bodies were designed, and their physical properties were tested. Eight samples were prepared for each formulation. After removing the maximum and minimum values, the average value of the data was calculated for analysis. Results: The hardness of the coated alloy powder formulation body decreased from 110 HRB to 106 HRB, but the decrease was less than 4%, indicating that the hardness remained similar. After adding the coated alloy powder, the flexural strength of the tire body increased by more than 10%. Specifically, for the formulation containing FeCuNi-Bi powder, the flexural strength increased from 945 MPa to 1,120 MPa, an increase of nearly 20%. The improvement was due to the even distribution of low-melting point elements coated on the surface of the alloy powder, which reduced the porosity of the matrix during the sintering process, thereby improving the bending strength of the matrix. Analysis of the microstructure of the four sintered tire bodies revealed that Sn in the original formula reacted with metal elements such as Cu in the tire body, gradually forming CuSn alloy. The distribution of Sn was uneven, and segregation was severe. As the sintering temperature increased, some CuSn alloys with higher Sn content began to melt. However, the wettability between the liquid CuSn alloy and Co or Fe particles was poor, and the distribution in the tire body was discontinuous. The vast majority of the CuSn liquid phase could not penetrate the Co and Fe skeleton phases to form a network connection. Under the interaction of sintering temperature and pressure, a strong and dense bond could not be formed, resulting in an uneven microstructure of the tire body and negatively affecting the performance and application of diamond tools. After adding FeCuNi-Cu/Sn/Bi alloy powder to the formula, the distribution of the coated alloy powder was relatively uniform. During sintering, Sn and Bi on the surface of FeCuNi alloy powder particles melted first, reacting with Cu to form liquid phases such as Cu-Sn and Cu-Bi. These phases gradually diffused along the FeCuNi alloy powder particles from the outside to the inside, entering the gaps between Fe, Ni, FeCuNi and other particles. Ultimately, Cu-Sn and Cu-Bi alloys formed a continuous network structure, encapsulating and bonding particles such as FeCuNi, Fe, and Ni, making the composition and microstructure distribution of the diamond tool bodies more uniform and dense, thus avoiding component segregation. Conclusions: FeCuNi-Cu/Sn/Bi alloy powder was prepared by chemically plating Cu, Sn, and Bi onto the surface of FeCuNi alloy powder. After adding the metal-coated alloy powder to the formula, the microstructure of the matrix was refined, and both hardness and strength were improved. The FeCuNi-Cu/Sn/Bi alloy powder, using coating technology, was sintered to obtain a denser matrix with higher diamond holding force and better mechanical properties.
- diamond tools /
- metal coated FeCuNi alloy powder /
- matrix

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图 1 Cu包覆FeCuNi合金面扫描元素分布图

Figure 1. Scanning element distribution of Cu-coated FeCuNi alloy

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图 2 Sn包裹FeCuNi合金面扫描元素分布图

Figure 2. Scanning element distribution of Sn-coated FeCuNi alloy

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图 3 Bi包裹FeCuNi合金面扫描元素分布图

Figure 3. Scanning element distribution of Bi-coated FeCuNi alloy

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图 4 不同配方烧结胎体显微形貌照片

Figure 4. Microstructures of sintered matrix with different formulations

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表 1 FeCuNi合金粉末基本性能

Table 1. Properties of FeCuNi alloy powder

合金粉末	Fe质量分数 ω₁ / %	Cu质量分数 ω₂ / %	Ni质量分数 ω₃ / %	理论密度 ρ / (g·cm⁻³)
FeCuNi	64.50	28.50	7.00	8.08

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表 2 金刚石工具胎体配方

Table 2. Formulation of diamond tool matrix

配方	质量分数 ω / %
配方	Co	Fe	Cu	Sn	Ni	合金粉末
配方A	30.00	36.00	26.00	8.00	—	—
配方B	—	40.70	17.50	8.00	3.80	30.00（FeCuNi-Cu）
配方C	—	40.70	17.50	8.00	3.80	30.00（FeCuNi-Sn）
配方D	—	40.70	17.50	8.00	3.80	30.00（FeCuNi-Bi）

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表 3 不同配方金刚石工具胎体性能

Table 3. Performance of diamond tool matrix with different formulations

配方	硬度 H /HRB	抗弯强度 σ /MPa
配方A	110	945
配方B	106	1080
配方C	107	1067
配方D	106	1120

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表 4 配方A烧结胎体能谱分析

Table 4. Energy spectrum analysis of sintered matrix of formula A

序号	Cu质量分数 ω₁' / %	Sn质量分数 ω₂' / %	Ni质量分数 ω₃' / %	Fe质量分数 ω₄' / %
相点1	54.36	32.26	11.77	1.61
相点2	78.82	14.41	3.47	3.30
相点3	15.10	—	5.59	79.31

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表 5 添加金刚石胎体抗弯强度

Table 5. Bending strength of adding diamond matrix

配方	抗弯强度 (未添加金刚石) $ {\sigma }_{1} $ / MPa	抗弯强度 (添加金刚石) $ {\sigma }_{2} $ / MPa	抗弯强度损失率 η / %
配方A	945	718	24
配方B	1080	885	18
配方C	1067	886	17
配方D	1120	930	17

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