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CN116121579B - Preparation method of MoCoB-WCoB (high-temperature co-fired ceramic) based composite material - Google Patents

Preparation method of MoCoB-WCoB (high-temperature co-fired ceramic) based composite material Download PDF

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CN116121579B
CN116121579B CN202211489844.8A CN202211489844A CN116121579B CN 116121579 B CN116121579 B CN 116121579B CN 202211489844 A CN202211489844 A CN 202211489844A CN 116121579 B CN116121579 B CN 116121579B
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mocob
wcob
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CN116121579A (en
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申宇鹏
赵昱
张伟
谢五喜
刘运飞
孙兵兵
张正中
刘晓军
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Xian Modern Chemistry Research Institute
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
    • C22C1/053—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor with in situ formation of hard compounds
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/12—Metallic powder containing non-metallic particles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/02—Compacting only
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/1039—Sintering only by reaction
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/14—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on borides
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E40/00—Technologies for an efficient electrical power generation, transmission or distribution
    • Y02E40/60—Superconducting electric elements or equipment; Power systems integrating superconducting elements or equipment

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Powder Metallurgy (AREA)

Abstract

The invention discloses a preparation method of MoCoB-WCoB matrix composite. The disclosed method comprises the following steps: pressing and forming mixed powder of Mo, co, B and W powder after ball milling to obtain a blank, and then sintering the blank in a vacuum carbon tube furnace to prepare MoCoB-WCoB-based composite material; the weight percentages are as follows: 34.0 to 46.0 percent of Mo, 38.0 to 52.0 percent of Co, 3.0 to 7.0 percent of B and 5.0 to 15.0 percent of W. In the invention, two hard phases MoCoB and WCoB are generated through solid-phase in-situ reaction in the sintering process, and the WCoB is used as an 'endogeneous' reinforcing phase, so that the method has the advantages of no surface pollution and high interface bonding strength; the MoCoB-WCoB-based composite material has compact microstructure, fine grains, good compactness, high hardness and the like.

Description

Preparation method of MoCoB-WCoB (high-temperature co-fired ceramic) based composite material
Technical Field
The invention relates to a preparation method of MoCoB-WCoB matrix composite material, belonging to the field of structural functional material. Provides a novel method with short preparation period, stable process and easy industrialization for preparing MoCoB-base metal ceramic.
Background
The ternary boride-based metal ceramic is a boride-based composite material prepared according to the reaction boride sintering principle, has the advantages of high hardness, good wear resistance, corrosion resistance, high strength of metal, good plastic toughness and the like of the ceramic, and is widely applied to the fields of cutters, turning molds and the like. The hard phase in ternary boride-based metal ceramic is not added as a raw material, but is generated by in-situ reaction of intermediate product binary boride and metal by a solid phase, and belongs to an 'endogenous' hard phase, the surface of the ternary boride-based metal ceramic is free from pollution, the problem of poor compatibility with a matrix is avoided, and the interface bonding strength is high. MoCoB-based cermet is novel ternary boride-based cermet developed in recent years, consists of MoCoB hard phase and Co binding phase, has the advantages of high hardness, good wear resistance, strong high-temperature oxidation resistance and the like, and has great potential in the field of wear-resistant materials.
The MoCoB-based cermet prepared at present has good hardness and can be used as wear-resistant parts of a car door mould, a turning tool, a milling cutter and the like. However, with the rapid development of technology, high-performance materials are layered endlessly, the performance of materials to be processed is gradually improved, and MoCoB-based metal ceramics are required to further improve the hardness so as to keep market competitiveness. The hardness of the biphase ceramic matrix composite material can be improved by adding the second phase ceramic to the cermet. For example:
The paper research of the influence of TiB 2 addition on MoCoB-base metal ceramic structure and performance in the journal of hard alloy shows that the addition of TiB 2 results in the influence of second-phase TiB 2 particles on MoCoB-Co metal ceramic microstructure and mechanical performance, so that the hardness of the composite material is improved and the maximum hardness reaches 88.9HRA. Although the hardness of the composite material can be improved by adding TiB 2 in the prior art, the TiB 2 reinforcing phase belongs to an ' external reinforcing phase, is not an ' internal ' reinforcing phase, and can reduce the wettability between an original MoCoB hard phase and a Co binding phase, so that the interface strength is reduced, and the service safety and the service life of the composite material are affected. In addition, the addition of TiB 2 has a relatively limited effect on improving the hardness of the composite material.
Disclosure of Invention
Aiming at the defects or shortcomings of the prior art, the invention provides a preparation method of MoCoB-WCoB matrix composite.
For this purpose, the preparation method provided by the invention comprises the following steps: sequentially ball-milling, pressing and forming mixed powder of Mo, co, B and W powder to obtain a blank, and then sintering the blank in a vacuum carbon tube furnace to prepare MoCoB-WCoB matrix composite;
The weight percentages are as follows: 34.0 to 46.0 percent of Mo, 38.0 to 52.0 percent of Co, 3.0 to 7.0 percent of B and 5.0 to 15.0 percent of W.
Optionally, the sintering process parameters are as follows: raising the temperature from room temperature to 1350-1450 ℃ at a heating rate of 5-15 ℃/min, preserving the temperature for 0-60 min, and cooling to room temperature.
Further, the MoCoB-WCoB-based composite material comprises three phases: moCoB hard phase, co-based binder phase, WCoB reinforcement phase. The hardness of the MoCoB-WCoB matrix composite is 88.8-90.6 HRA, and the density is 97.73-98.91%.
Compared with the prior art, ① the composite material produced by the invention comprises three phases: moCoB hard phase, co-based binder phase, WCoB reinforcement phase; ② The WCoB reinforcing phase is not directly added into the raw material, but generated by the raw material powder through solid phase in-situ reaction, is an 'endogenous' reinforcing phase, and has the advantages of no surface pollution and high interface bonding strength; ③ The MoCoB-WCoB-based composite material has compact microstructure, fine grains, good compactness, high hardness and the like.
Drawings
FIG. 1 is an XRD pattern for MoCoB-WCoB-based composites in example 2 of the present invention;
FIG. 2 is a photograph of a microstructure of MoCoB-WCoB-based composite material in example 2 of the present invention.
Detailed Description
Unless specifically stated otherwise, scientific and technical terms and methods herein have been understood or implemented by those of ordinary skill in the relevant art based on the knowledge of one of ordinary skill in the relevant art. It should also be understood that the temperature, hold time, and the like referred to herein are approximations for purposes of illustration. Although methods and materials similar or equivalent to those described herein can be used in the practice of the present disclosure, some suitable methods and materials are described below. Publications, patent applications, patents, and other references mentioned herein are incorporated by reference in their entirety to the extent that any conflict arises. In addition, the materials, methods, material ratios, and examples are illustrative only and not intended to be limiting. In a specific scheme, a person skilled in the art can optimize the material proportion and the operation parameter value involved in the method according to the disclosure of the invention by adopting a conventional experimental period to achieve the aim of the invention.
The purpose of the press forming according to the invention is to initially densify the powdery raw material, the shape and size of the green body produced depending on the shape of the mould. The molds used in the prior art of ceramics, such as molds with volume dimensions greater than 3mm by 3mm, are suitable for use in the present invention.
Based on the disclosure of the present invention, a person skilled in the art may optimize specific sintering by using a conventional experimental means for different formulation materials and effects of the present invention, and the specific sintering process adopted in the following examples is only one specific example to explain the scheme of the present invention, and the sintering process of the present invention is not limited thereto. The sintering process conditions are exemplified by raising the temperature from room temperature to 1350-1450 ℃ at a heating rate of 5-15 ℃/min, and maintaining the temperature for 0-60 min, and then furnace cooling to room temperature.
The invention is illustrated in further detail by the following examples. The raw materials Mo, W, co and B powder used in the embodiment of the invention are all commercial chemical pure powder reagents, and a planetary ball mill (QM-3 SP 4) is adopted for ball milling. The present invention is not limited to these specific devices.
The density of MoCoB-WCoB based composite material is tested by adopting an Archimedes drainage method; the hardness of MoCoB-WCoB-based composites was measured using an HRS-150 Rockwell hardness tester.
Example 1:
In the embodiment, mo, co, B and W powder with purity not lower than 99.0% are selected as raw materials, and the raw materials are as follows by mass percent: 46.0% Mo, 46% Co, 3.0% B, 5.0% W;
Ball milling and compacting the mixed powder to prepare a cylindrical (diameter 44mm, height 8-9 mm) blank;
then placing the blank into a vacuum carbon tube furnace for sintering, wherein the sintering process parameters are as follows: the temperature was raised from room temperature to 1350 ℃ at a heating rate of 5 ℃/min and incubated for 0min, after which the furnace cooled to room temperature.
The MoCoB-WCoB-based composite material prepared in this example contained MoCoB hard phase, co-based binder phase and WCoB reinforcement phase, and had a hardness of 89.2HRA and a density of 97.73%.
Example 2:
In the embodiment, mo, co, B and W powder with purity not lower than 99.0% are selected as raw materials, and the raw materials are as follows by mass percent: 40.0% of Mo, 45% of Co, 5% of B and 10.0% of W;
Ball milling and compacting the mixed powder to prepare a cylindrical (diameter 44mm, height 8-9 mm) blank;
Then placing the blank into a vacuum carbon tube furnace for sintering, wherein the sintering process parameters are as follows: the temperature was raised from room temperature to 1400℃at a heating rate of 10℃per minute and kept at that temperature for 30 minutes, after which the furnace was cooled to room temperature.
The MoCoB-WCoB-based composite material prepared in this example comprises MoCoB hard phase, co-based binder phase and WCoB reinforcement phase (XRD pattern see figure 1), and microstructure is shown in figure 2; the hardness of the composite material is 90.6HRA, and the compactness is 98.54%.
Example 3:
in the embodiment, mo, co, B and W powder with purity not lower than 99.0% are selected as raw materials, and the raw materials are as follows by mass percent: 34.0% of Mo, 44.0% of Co, 7.0% of B and 15.0% of W;
Ball milling and compacting the mixed powder to prepare a cylindrical (diameter 44mm, height 8-9 mm) blank;
Then placing the blank into a vacuum carbon tube furnace for sintering, wherein the sintering process parameters are as follows: the temperature was raised from room temperature to 1450℃at a heating rate of 15℃per minute and kept at that temperature for 60 minutes, after which the furnace was cooled to room temperature.
The MoCoB-WCoB-based composite material prepared in this example contained MoCoB hard phase, co-based binder phase and WCoB reinforcement phase, and had a hardness of 88.8HRA and a density of 98.91%.
Comparative example:
The comparative example differs from example 2 in mass: the raw materials do not contain W powder.
The MoCoB-based cermet obtained in this comparative example contained MoCoB hard phase and Co-based binder phase, and had a hardness of 87.6HRA and a density of 97.39%.
The test properties of the above-described composite materials of examples and comparative examples are shown in Table 1.
Table 1 microstructure and mechanical Properties of the composite Material
Sample of Hardness/HRA Density of the product
Comparative example 87.6 97.39％
Example 1 89.2 97.73％
Example 2 90.6 98.54％
Example 3 88.8 98.91％
As can be seen from the test results in Table 1, compared with the comparative example, the MoCoB-WCoB-based composite material prepared by the method has the advantages that the hardness and the compactness are both increased, the compactness is increased by about 1.5%, the hardness is up to 90.6HRA, the hardness is increased by 3.0HRA, and a larger breakthrough is achieved.

Claims (2)

1. A method for preparing MoCoB-WCoB-based composite material, the method comprising: sequentially ball-milling, pressing and forming mixed powder of Mo, co, B and W powder to obtain a blank, and then sintering the blank in a vacuum carbon tube furnace to prepare MoCoB-WCoB matrix composite;
The weight percentages are as follows: 34.0 to 46.0 percent of Mo, 38.0 to 52.0 percent of Co, 3.0 to 7.0 percent of B and 5.0 to 15.0 percent of W;
The sintering process parameters are as follows: raising the temperature from room temperature to 1350-1450 ℃ at a heating rate of 5-15 ℃/min, preserving the temperature for 0-60 min, and then cooling the furnace to room temperature;
The MoCoB-WCoB matrix composite material comprises three phases: moCoB hard phase, co-based binder phase, WCoB reinforcement phase.
2. The method of preparing MoCoB-WCoB based composite material according to claim 1, wherein the hardness of the MoCoB-WCoB based composite material is 88.8-90.6 HRA and the density is 97.73% -98.91%.
CN202211489844.8A 2022-11-25 2022-11-25 Preparation method of MoCoB-WCoB (high-temperature co-fired ceramic) based composite material Active CN116121579B (en)

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Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112080678A (en) * 2020-09-15 2020-12-15 广东博杰特新材料科技有限公司 Ternary boride alloy screw material and production process thereof
CN113355611A (en) * 2021-06-15 2021-09-07 上海海事大学 Carbon fiber reinforced MoCoB metal ceramic and preparation method thereof

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05132734A (en) * 1991-11-08 1993-05-28 Japan Steel Works Ltd:The Wear and corrosion resistant composite materials
JP3134767B2 (en) * 1996-04-03 2001-02-13 住友金属鉱山株式会社 Boride cermet spraying powder
JP3628601B2 (en) * 2000-09-07 2005-03-16 秋田県 WC-WB, WC-W2B or WC-WB-W2B composite having high hardness and high Young's modulus characteristics and method for producing the same
DE10117657B4 (en) * 2001-04-09 2011-06-09 Widia Gmbh Complex boride cermet body and use of this body
CN103468994B (en) * 2013-09-17 2015-04-08 北京科技大学 Method for preparing molybdenum nickel chromium boron multivariant boride metal ceramic
CN104404388A (en) * 2014-10-31 2015-03-11 武汉科技大学 Ceramic steel composite material and its preparation method
CN106222512A (en) * 2016-08-26 2016-12-14 郴州市泰益表面涂层技术有限公司 A kind of polynary boride-based superhard bimetal screw rod and preparation method thereof
CN107868898B (en) * 2017-10-31 2019-09-17 武汉科技大学 A kind of WCoB-TiC-SiC multiphase metal ceramics material and preparation method thereof
CN107904474B (en) * 2017-11-02 2019-06-21 北京科技大学 A kind of molybdenum cobalt boron ternary boride based cermet material and preparation method thereof
CN109299561A (en) * 2018-10-09 2019-02-01 北京科技大学 Method for screening transition metal doping elements that can improve the hardness of cemented carbide
JP7366707B2 (en) * 2019-11-22 2023-10-23 株式会社日本製鋼所 Sintered material and its manufacturing method
CN115011830B (en) * 2022-05-30 2023-09-22 河源富马硬质合金股份有限公司 Molybdenum cobalt boron ternary boride-based metal ceramic material and preparation method thereof

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112080678A (en) * 2020-09-15 2020-12-15 广东博杰特新材料科技有限公司 Ternary boride alloy screw material and production process thereof
CN113355611A (en) * 2021-06-15 2021-09-07 上海海事大学 Carbon fiber reinforced MoCoB metal ceramic and preparation method thereof

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