CN109338196B - Ti (C, N) -based metal ceramic and preparation method and application thereof - Google Patents
Ti (C, N) -based metal ceramic and preparation method and application thereof Download PDFInfo
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- 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
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/04—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbonitrides
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- 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
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
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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
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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
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- 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
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- 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
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0089—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with other, not previously mentioned inorganic compounds as the main non-metallic constituent, e.g. sulfides, glass
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- 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
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F2005/001—Cutting tools, earth boring or grinding tool other than table ware
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- 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
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
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Abstract
The invention relates to Ti (C, N) -based metal ceramic and a preparation method and application thereof, belonging to the technical field of metal ceramic. The Ti (C, N) -based metal ceramic is prepared from the following raw materials in percentage by mass: ti (C)0.5，N0.5)40‑55％、Ti(C0.3，N0.7)10‑25％、Ni10‑15％、Co10‑15％、Mo10‑20％、WC8‑12％、C0.5‑2％、TaC1‑5％、Y2O30.1-01 percent. In the raw materials of the Ti (C, N) -based cermet, the C/N ratio is considered, so the denitrification and decarburization phenomena in the sintering process are balanced, the compactness of a finished product and the performance of the material are not influenced, and the cermet with good toughness, high hardness and high strength can be obtained without adding inert gas in the sintering process. Has the advantages of simple production and low cost, and is suitable for industrial popularization.
Description
Technical Field
The invention relates to the technical field of metal ceramics, in particular to Ti (C, N) -based metal ceramic and a preparation method and application thereof.
Background
The cermet is two kinds of multiphase composite functional structural material comprising metal binding phase and hard ceramic phase. The high-temperature-resistant engineering structural material has the characteristics of high strength, wear resistance, oxidation resistance and good high-temperature stability of ceramic materials, has the advantages of high plasticity and toughness of metal materials, and is high-performance high-temperature-resistant and good high-temperature chemical stability. The development of Ti (C, N) -based metal ceramics is less than half a century, and the Ti (C, N) -based metal ceramics is concerned by researchers in various countries due to excellent high temperature and time wear resistance, excellent toughness and higher thermal conductivity, and becomes an ideal substitute product of the traditional hard alloy cutter due to the advantages of abundant sources of preparation raw materials, simple process, low preparation cost and the like.
However, compared with the hard open-and-close alloy cutting tool, the toughness of the Ti (C, N) -based metal ceramic material is still poor, and the application and popularization of the Ti (C, N) -based metal ceramic material in a wider range are severely limited.
Disclosure of Invention
In view of the above, it is necessary to provide a Ti (C, N) -based cermet having high performance, good toughness, and high hardness and strength.
The Ti (C, N) -based metal ceramic is characterized by being prepared from the following raw materials in percentage by mass:
in the raw materials of the Ti (C, N) -based cermet, the mutual matching among the raw materials is fully considered, and the C/N ratio is also considered, so the denitrification and decarburization phenomena in the sintering process are balanced, the compactness of a finished product is not influenced, the performance of the material is not influenced, and the inert gas is not added in the sintering process, so that the cermet with good toughness and high hardness and strength can be obtained.
In one embodiment, the mass ratio of the C element to the N element in the raw material is 6-7: 3-4. Preferably 6: 4. By adopting the proportion, the obtained metal ceramic has higher performance.
In one embodiment, the average particle size of the feedstock is as follows:
in one embodiment, the purity of the feedstock is no less than 99.9%.
The invention also discloses a preparation method of the Ti (C, N) -based metal ceramic, which comprises the following steps:
mixing materials: weighing the raw materials, and uniformly mixing to obtain a mixture;
pressing: placing the mixture in a mold, and pressing and molding to obtain a green body;
degumming: heating and degumming the green body;
and (3) sintering: and (4) carrying out vacuum sintering on the degummed green body to obtain the finished product.
According to the preparation method, the carbon-nitrogen ratio (C/N ratio) is fully considered in the raw material proportion, so that the denitrification and decarburization phenomena in the sintering process are balanced, the compactness of a finished product is not influenced, the performance of the material is not influenced, and inert gases such as argon are not filled in the sintering process, so that the production is easier, and the preparation method has the advantages of simplicity and convenience in production and low cost.
In one embodiment, in the mixing step, wet mixing is adopted, an organic solvent is used as a dispersion medium, the hard alloy balls are used as a ball milling medium, and raw materials are mixed and ground to obtain slurry; and drying and sieving the slurry to obtain a mixture. It is understood that the organic solvent may be selected as desired, such as absolute ethanol, and the like.
In one embodiment, in the compaction process, the green compact is formed by dry pressing under the pressure of 60-80MPa, and then is kept for 10-20 minutes by a cold isostatic press under the pressure of 180-220MPa to obtain a formed green compact.
In one embodiment, in the degumming step, degumming is performed by heating at 500-.
In one embodiment, in the sintering step, the vacuum degree is less than or equal to 10-3Pa, temperature 1400 ℃ and 1600 ℃ for 0.5-2 hours. Preferably 1 hour.
The invention also discloses application of the Ti (C, N) -based metal ceramic in preparing a cutter.
Compared with the prior art, the invention has the following beneficial effects:
the Ti (C, N) -based cermet has the advantages of good toughness, high hardness and high strength, and the fracture toughness of the cermet is about 6.82 MPa.m1/2～8.65MPa·m1/2The Vickers hardness is about 16.5 GPa-19.9 GPa, and the relative density is about 93.81% -98.07%; the grain size is about 0.78-2.82 μm, and the bending strength can reach 996 MPa; has high performance.
According to the preparation method of the Ti (C, N) -based metal ceramic, inert gases such as argon are not required to be filled in the sintering process, so that the production is easier, and the preparation method has the advantages of simplicity and convenience in production and low cost, and is suitable for industrial popularization.
Drawings
FIG. 1 is a schematic process flow diagram of a preparation method of a Ti (C, N) -based cermet in example 1;
FIG. 2 is an SEM image of the microstructure of the Ti (C, N) -based cermet prepared in example 1.
Detailed Description
To facilitate an understanding of the invention, the invention will now be described more fully with reference to the accompanying drawings. Preferred embodiments of the present invention are shown in the drawings. This invention may, however, be embodied in many different forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete.
Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. The terminology used in the description of the invention herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention.
Example 1
The Ti (C, N) -based metal ceramic is prepared from the following raw materials in percentage by mass:
TABLE 1 raw materials formulation table
In the formula, the mass ratio C/N of the C element to the N element is 6: 4.
the Ti (C, N) -based metal ceramic is prepared by the following method of powder metallurgy sintering, and the main process flow of the Ti (C, N) -based metal ceramic is shown in figure 1.
(1) And (3) mixing materials.
The wet mixing is adopted, absolute ethyl alcohol is used as a dispersion medium, YG8 hard alloy balls are used as a ball milling medium, and the ball-to-material ratio (the mass ratio of the ball milling medium to the raw materials) is 8: 1. The powder is used as raw material, and the raw materials of each component are weighed by an analytical balance to prepare slurry with required proportion according to requirements.
And then, drying the mixed slurry in an automatic constant-temperature drying oven at 60 ℃, and sieving by a 100-mesh sieve to obtain experimental powder, namely the mixed material.
(2) And (5) compacting.
Weighing a predetermined amount of mixture, placing the mixture into a mold, performing dry pressing molding by using a manual FLS hydraulic press under the pressure of 70MPa, pressing a certain amount of sample in each group, and then maintaining the pressure for 15 minutes by using a cold isostatic press under the pressure of 200MPa to obtain a molded green body.
(3) And (5) degumming.
The pressed green body was placed in a vacuum tube furnace of Beijing Wenitt, and heated to 600 ℃ in a vacuum atmosphere to degum for one hour.
(4) And (5) sintering.
And (3) vacuum sintering: placing the degummed green body in a high-temperature high-vacuum sintering furnace, wherein the vacuum degree is less than or equal to 10-3Pa, the sintering temperature is 1400-1600 ℃, and the Ti (C, N) -based metal ceramic A is prepared.
Example 2
The Ti (C, N) -based metal ceramic is prepared from the following raw materials in percentage by mass:
TABLE 2 raw materials formulation table
In the formula, the mass ratio of the C element to the N element is 7: 3.
Ti (C, N) -based cermet B was prepared according to the method of example 1.
Examples of the experiments
The Ti (C, N) -based cermet products prepared in the above examples and comparative examples were subjected to a performance test.
1. And (4) a test method.
Bending strength: the bending strength of the sample is tested on a WDW-5E universal material testing machine of a gold testing machine in the time of Jinan by adopting a three-point bending method. The sintered samples were made to a size of 3mm × 4mm × 30mm with a span of 20mm, a loading rate of 0.5mm/min, 10 samples per group were tested, and the average value was taken as the final measurement result.
Vickers hardness: the HVS-30ZJC/LCD Vickers hardness tester of Shanghai Tammin optical instruments is adopted, the loading load is 100N, and the loading time is 15 s. 8 samples were tested for each data point, and 10 points were measured for each sample and averaged.
And (3) microscopic structure observation: the microstructure morphology of the Ti (C, N) ceramic sample was observed in a back-scattered mode using a Nova-Nano SEM430A scanning electron microscope in the Netherlands.
Fracture toughness: in this experiment, an indentation method was used. With the aid of the above Vickers hardness tester, after a certain load is applied to the polished surface of the sample by the indenter, the size of the indentation and the length of the indentation crack are observed under a 40-fold microscope, and then the fracture toughness value is calculated, and the formula adopted in the experiment is shown as the following formula:
wherein 2a and 2c are the diagonal length of the indentation and the total length (mm) of the crack, and Hv is the Vickers hardness value
(kg/mm2)。
And (3) testing the relative density: the density of the sample was measured by archimedes' method and then divided by the theoretical density.
The grain size was measured by counting the grain size using the Nano Measurer software, and the number of the counted grains per sample was 350, and the average value was taken.
2. And (6) testing results.
TABLE 4 Performance test results
From the above results, it can be seen that the Ti (C, N) -based cermet products prepared in example 1 have the best properties, while the Ti (C, N) -based cermet products prepared in example 2 have reduced properties.
When the Ti (C, N) -based cermet prepared in example 1 is observed under a microscope, an SEM image of the cermet is shown in fig. 2, and it can be seen from the SEM image that the cermet has uniform grain size and high toughness and strength, thereby achieving the purpose of toughening and reinforcing the cermet material.
The technical features of the embodiments described above may be arbitrarily combined, and for the sake of brevity, all possible combinations of the technical features in the embodiments described above are not described, but should be considered as being within the scope of the present specification as long as there is no contradiction between the combinations of the technical features.
The above-mentioned embodiments only express several embodiments of the present invention, and the description thereof is more specific and detailed, but not construed as limiting the scope of the invention. It should be noted that, for a person skilled in the art, several variations and modifications can be made without departing from the inventive concept, which falls within the scope of the present invention. Therefore, the protection scope of the present patent shall be subject to the appended claims.
Claims (9)
1. The Ti (C, N) -based metal ceramic is characterized by being prepared from the following raw materials in percentage by mass:
in the raw materials, the mass ratio of the C element to the N element is 6: 4.
2. The Ti (C, N) -based cermet according to claim 1, characterized in that the average grain size of the raw material is as follows:
3. the Ti (C, N) -based cermet according to claim 1, characterized in that the purity of the raw material is no less than 99.9%.
4. A method for producing a Ti (C, N) -based cermet according to any of claims 1-3, characterized by comprising the steps of:
mixing materials: weighing the raw materials, and uniformly mixing to obtain a mixture;
pressing: placing the mixture in a mold, and pressing and molding to obtain a green body;
degumming: heating and degumming the green body;
and (3) sintering: and (4) carrying out vacuum sintering on the degummed green body to obtain the finished product.
5. The method for producing a Ti (C, N) -based cermet according to claim 4, wherein in the mixing step, the raw materials are mixed and ground by using a wet mixing method, an organic solvent as a dispersion medium, and cemented carbide balls as a ball milling medium to obtain a slurry; and drying and sieving the slurry to obtain a mixture.
6. The method of claim 4, wherein the green compact is formed by dry pressing at a pressure of 60-80MPa, and then by holding pressure of 180-220MPa for 10-20 min with a cold isostatic press.
7. The method of claim 4, wherein the degumming step comprises heating to degum the Ti (C, N) -based cermet at 500-700 ℃ for 0.5-1.5 hours under a vacuum atmosphere.
8. The method for producing a Ti (C, N) -based cermet according to claim 4, wherein the sintering step is carried out in a vacuum of 10 or less-3Pa, temperature 1400 ℃ and 1600 ℃ for 0.5-2 hours.
9. Use of the Ti (C, N) -based cermet according to any one of claims 1-3 for the manufacture of a cutting tool.
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| CN110484763A (en) * | 2019-08-06 | 2019-11-22 | 广东工业大学 | A kind of cermet and its preparation method and application based on novel adhesive |
| CN110684919A (en) * | 2019-11-13 | 2020-01-14 | 沈阳金锋特种刀具有限公司 | Wear-resistant and corrosion-resistant Ti (C, N) cermet material and preparation method thereof |
| CN113234950B (en) * | 2021-04-01 | 2022-03-08 | 三峡大学 | Preparation method of Ti (C, N) -based metal ceramic |
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| JPS6417837A (en) * | 1987-07-10 | 1989-01-20 | Toshiba Corp | Erosion shield alloy |
| SE469385B (en) * | 1990-12-21 | 1993-06-28 | Sandvik Ab | MADE TO MAKE A SINTERED CARBON Nitride Alloy BEFORE FINISHING |
| EP0563203A1 (en) * | 1990-12-21 | 1993-10-06 | Sandvik Ab | Method of producing a sintered carbonitride alloy for intermittent machining of materials difficult to machine. |
| EP0563204A1 (en) * | 1990-12-21 | 1993-10-06 | Sandvik Ab | Method of producing a sintered carbonitride alloy for fine milling. |
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| CN103774021B (en) * | 2012-10-19 | 2015-11-25 | 郑汉东 | The preparation method of Ti (C, N) based ceramic metal |
| CN102925777B (en) * | 2012-11-01 | 2014-06-11 | 南京航空航天大学 | High-obdurability Ti (C, N) base metal ceramic and preparation method thereof |
| CN103556086B (en) * | 2013-10-21 | 2015-12-02 | 西安科技大学 | A kind of high temperature resistance wear-resistant Ti(C, N) preparation method of ceramic-metal composite |
| CN103710603B (en) * | 2013-12-27 | 2016-01-20 | 华中科技大学 | Without magnetic gradient structure Ti (C, N) based ceramic metal and preparation method thereof |
| CN104630590B (en) * | 2015-02-12 | 2016-08-24 | 成都邦普切削刀具股份有限公司 | A kind of composite hard alloy material and preparation method thereof |
| CN104630533B (en) * | 2015-02-12 | 2016-08-17 | 成都邦普切削刀具股份有限公司 | A kind of preparation method of the composite hard alloy of cutter material |
| CN105983688A (en) * | 2015-03-04 | 2016-10-05 | 海南大学 | Fast preparation method for Ti(C1-x, Nx) (0<=x<=1)-Fe composite powder |
| CN107881389B (en) * | 2017-11-06 | 2019-06-25 | 株洲科力特新材料有限公司 | Ti (C, N) based ceramic metal and the preparation method for being used to prepare it |
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6417837A (en) * | 1987-07-10 | 1989-01-20 | Toshiba Corp | Erosion shield alloy |
| SE469385B (en) * | 1990-12-21 | 1993-06-28 | Sandvik Ab | MADE TO MAKE A SINTERED CARBON Nitride Alloy BEFORE FINISHING |
| EP0563203A1 (en) * | 1990-12-21 | 1993-10-06 | Sandvik Ab | Method of producing a sintered carbonitride alloy for intermittent machining of materials difficult to machine. |
| EP0563204A1 (en) * | 1990-12-21 | 1993-10-06 | Sandvik Ab | Method of producing a sintered carbonitride alloy for fine milling. |
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