CN110616357B - Carbonitride-based cermet and preparation process thereof - Google Patents

Carbonitride-based cermet and preparation process thereof Download PDF

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CN110616357B
CN110616357B CN201910837808.8A CN201910837808A CN110616357B CN 110616357 B CN110616357 B CN 110616357B CN 201910837808 A CN201910837808 A CN 201910837808A CN 110616357 B CN110616357 B CN 110616357B
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carbonitride
based cermet
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CN110616357A (en
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郭伟
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Changsha Zhongxinda Tools Co ltd
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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
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
    • 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
    • B22F3/1003—Use of special medium during sintering, e.g. sintering aid
    • B22F3/1007—Atmosphere
    • 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
    • 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
    • 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
    • C22C29/02—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
    • 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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  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Powder Metallurgy (AREA)

Abstract

In the component of the carbonitride-based cermet, a hard phase has the function of improving the high-temperature red hardness of the material, a disperse phase has the function of improving the impact toughness of the material, and the addition of a disperse phase solid solution can ensure that the metallographic structure of the produced material is more uniform, improve the phase structure composition of the hard phase and greatly improve the strength and the toughness of the carbonitride-based cermet material. After the carbonitride-based cermet provided by the embodiment of the invention is manufactured into a blade, the cutting time is as long as 27min when the wear value of a rear cutter face reaches Vb equal to 0.2mm, the cutting time is obviously superior to that of a blade with the same formula prepared by the prior art, and the cutting edge is not broken.

Description

Carbonitride-based cermet and preparation process thereof
Technical Field
The invention belongs to the technical field of metal ceramics, and particularly relates to carbonitride based metal ceramic and a preparation process thereof.
Background
Hard tool materials for metal working are important components of the manufacturing industry, and determine the machining efficiency, precision, quality and cost of parts in the manufacturing industry. Hard tool materials generally have high hardness, toughness, wear resistance, oxidation resistance, and the like, and are classified into high-speed steels, hard alloys, cermets, and the like according to their components. Cermets have high temperature hardness and strength, but are less ductile and are commonly used for high speed finishing.
Cermets are a class of composite materials consisting of inorganic nonmetallic phases (oxides, carbides, nitrides, etc.) and metallic (or alloy) binder phases. Generally, the ceramic phase particles account for about 15-85% of the total volume of the material and are dispersed in the bonding phase metal. The TiC-based cermet was first developed and commercialized by german scientists in 1929, but the early TiC-based cermet has great material brittleness due to poor wettability of hard particles and nickel, and thus the application is greatly limited. Until the middle and later stages of the 50 th century, Ford research and development personnel find that Mo is added into TiC-Ni base cermet to improve the wettability of a metal matrix to a hard phase and prevent hard particles from growing up, so that the hardness and toughness of the material are greatly improved, and the material is beginning to be widely applied to the field of cutting tools.
In order to improve the cutting performance of titanium carbide-based cermets used as cutting tool materials, TiN, WC, TaC, Nb, Mo are usually added in the prior art2C、HfCZrC and VC, etc. as additives to increase the sinterability of the material and improve the microstructure of the material, however, the effect is not ideal.
Disclosure of Invention
In order to solve the problem of poor cutting performance of titanium carbide-based cermets used as cutting tool materials in the prior art, an object of an embodiment of the present invention is to provide a carbonitride-based cermet. Another object of the embodiments of the present invention is to provide a process for preparing the carbonitride-based cermet.
In order to achieve the purpose, the embodiment of the invention adopts the following technical scheme:
the carbonitride base cermet comprises the following components in parts by weight:
10-30 parts of a bonding phase,
10 to 30 parts of a hard phase,
30-70 parts of a dispersed phase,
the hard phase is (Ti, W, M) CN solid solution, and the M is at least one of Hf, Zr and V;
the dispersed phase is (Ti, Ta, Nb, Mo) CN solid solution.
In the carbonitride-based cermet component, the addition of the hard phase has the effect of improving the high-temperature red hardness of the material, and the addition of the dispersed phase has the effect of improving the phase structure composition of the hard phase, so that the produced material tissue is more uniform, and the toughness of the carbonitride-based cermet material is greatly improved. By combining the factors, the final cermet material has high toughness, high-temperature red hardness, and excellent wear resistance, heat resistance and impact resistance.
In addition, the carbonitride-based cermet according to the embodiment of the present invention may be prepared by using hard phase (Ti, W, M) CN solid solutions and dispersed phase (Ti, Ta, Nb, Mo) CN solid solutions with different chemical compositions according to different requirements.
When the titanium carbide-based cermet is used as a cutting tool material, the added TiN not only has the effect of inhibiting the growth of crystal grains, but also has the effect of reducing the friction coefficient between the material and a workpiece, so that the crater resistance is improved, and the wear resistance of the cermet material is improved. Through the test, the following results are found: when the content of TiN is less than 10%, the above-mentioned effect cannot be obtained; on the other hand, when the content of TiN is more than 25%, not only the wettability with the binder phase is adversely affected, but also the toughness of the matrix material is lowered, so that the content of TiN is only 25% at the maximum.
WC is known to have the effect of improving the wettability of the titanium carbide-based cermet to the hard phase, thereby improving the toughness of the titanium carbide-based cermet. But WC in an amount of less than 10% does not perform the above-mentioned function. On the other hand, if the addition amount exceeds 30%, the oxidation resistance and wear resistance of the carbide-based cermet tend to be lowered, and the addition amount is 30% at the maximum.
The addition of HfC, ZrC and VC can not only improve the hardness of the hard phase, but also improve the bonding strength of the grain boundary between the hard phase and the bonding phase, thereby remarkably improving the wear resistance and the heat resistance of the titanium carbide-based metal ceramic. If the amount of HfC, ZrC and VC added is less than 0.5%, the above effect cannot be obtained, and if the amount is more than 5%, the wettability of the binder phase and the hard phase is lowered, so that the toughness of the titanium carbide-based cermet is lowered.
The hard phase is added for improving the red hardness of the metal ceramic material and improving the wear resistance of the cutter material. Because the high-temperature red hardness of WC, HfC, ZrC and VC is better than that of TiC, the high-temperature performance of the material can be improved after the high-temperature red hardness is added. The amount of the hard phase added is 10 to 30% based on the whole material, and if it exceeds 30%, the toughness of the material may be deteriorated.
The purpose of adding TaC and NbC into the titanium carbide-based cermet is to improve the high-temperature strength of the matrix material, and Ta and Nb generated by partial decomposition of TaC and NbC form a solid solution with the binder phase, and further improve the strength of the binder phase. When the addition amount of TaC and NbC is less than 3%, the above-mentioned effects are not obtained, and on the other hand, when the addition amount is 50%, the wear resistance and oxidation resistance tendency of the titanium carbide-based cermet is lowered, and therefore 50% of TiC is added at most.
Mo and Mo are known2C has the function of improving the wettability of the relative hard phase of the bonding, thereby improving the toughness of the titanium carbide-based metal ceramic. But Mo2C addition amountBelow 10% this effect cannot be achieved; on the other hand, if the addition amount exceeds 30%, the oxidation resistance and wear resistance of the titanium carbide-based cermet will be reduced, so the addition amount is not more than 30%.
By adding TiN, WC, Mo2C, TaC and the like, can properly reduce the content of TiC and expand the application range of the TiC-based cermet cutting tool, and the prior art adopts TiN, WC and Mo2C. TaC, etc., in the form of pure carbides, while TiN, WC, Mo2C. TaC and the like are added in a solid solution form (W, Ti, Ta, Mo) CN, so that the effect is better, and the product quality is more stable.
The metallographic structure of the produced material is more uniform by adding the disperse phase solid solution, the phase structure of the hard phase is improved, the toughness of the material is greatly improved, the effect can be achieved only when the addition amount of the hard phase is more than 30%, and the addition proportion is more than 50% when the better performance is obtained so as to form a continuous network structure.
The hard phase solid solution and the disperse phase solid solution of the additive adopted in the embodiment of the invention are in the form of solid solutions, and the hard alloy is prepared by only mixing the two solid solutions with the bonding phase. In the prior art, the additive is usually a plurality of different carbide or nitride alloy powders, and during preparation, different carbide or nitride alloy powder additives, such as TiC powder, TaC powder, ZrC powder and the like, need to be added respectively, however, various different additives are added respectively, on one hand, different additives need to be weighed separately, and multiple weighing can cause error accumulation, and finally the accuracy of the total amount of the additive is affected; on the other hand, the purity of various additives is different, and the purity of the final product is difficult to control by adding various additives, so that the final product contains more impurities easily. The additive provided by the embodiment of the invention is in the form of two solid solutions, various elements needing to be added can be prepared into the solid solutions in advance according to the performance requirements of the metal ceramics, only one substance of the solid solutions needs to be added when the hard alloy is prepared, and errors caused by multiple weighing and impurities possibly brought by various different additives are avoided.
Preferably, the amount of dispersed phase added is greater than 30% to be effective.
It is further preferred that the amount of dispersed phase is greater than 50% in order to form a continuous tissue structure.
Preferably, the bonding phase is formed by mixing Co powder and Ni powder according to the mass ratio of (1-2): 1.
More preferably, the average particle size of the Co powder is 0.8 to 1.5 μm.
Still more preferably, the average particle size of the Co powder is 1.0. mu.m.
More preferably, the average particle size of the Ni powder is 0.5 to 1.5 μm.
Still more preferably, the Ni powder has an average particle diameter of 0.8 μm.
Preferably, the average particle size of the hard phase is 1 to 2 μm.
Preferably, the molar percentages of Ti, W and M in the (Ti, W, M) CN solid solution are:
W：15～30mol％，
M：3～15mol％，
the balance being Ti.
Preferably, the particle size of the dispersed phase solid solution powder is controlled to be 2-3 μm.
Preferably, the (Ti, Ta, Nb, Mo) CN solid solution comprises the following components in percentage by mass:
TiN：10～30％
TaC：10～20％
NbC：10～20％
Mo2C：20～30％
the balance being TiC.
Preferably, in the (Ti, Ta, Nb, Mo) CN solid solution, TiC, TiN, TaC, NbC and Mo2The mass ratio of C is 30:30:10:10: 20.
The preparation process of the carbonitride-based cermet comprises the following steps:
s1: weighing the bonding phase and the hard phase according to the proportion, and wet-grinding and uniformly mixing to obtain mixed powder;
s2: adding a forming agent into the mixed powder obtained in the step S1, drying, granulating, and then pressing and forming to obtain a blank body;
s3: and (5) sintering the blank obtained in the step S2 to obtain the carbonitride-based cermet.
Preferably, the wet-milling medium in step S1 is absolute ethanol, and the addition amount of the absolute ethanol is 700m L per kilogram of the powder raw material.
Preferably, the wet milling time is 36-60 h.
Further preferably, the time for wet milling is 48 h.
Preferably, the ball-material ratio of wet grinding is (4-6): 1.
further preferably, the wet-milled balls/material ratio is 5: 1.
preferably, the forming agent is PEG. The concentration of PEG was 4%.
Preferably, the sintering temperature is 1450-1500 ℃, and the sintering time is 1-2 h.
The embodiment of the invention has the beneficial effects
After the carbonitride-based cermet provided by the embodiment of the invention is manufactured into a blade, the cutting time is as long as 27min when the wear value of a rear cutter face reaches Vb of 0.2mm, the cutting time is obviously superior to that of a blade with the same formula prepared by the prior art, and the cutting edge is not broken.
Drawings
FIG. 1 is a metallographic structure diagram of a cermet cutting material A prepared in example 5.
FIG. 2 is a metallographic structure diagram of a cermet cutting material B prepared in comparative example 1.
Detailed Description
The embodiment of the invention provides carbonitride-based cermet and a preparation process thereof. In the carbonitride-based cermet component, the hard phase has the effect of improving the high-temperature red hardness of the material, the dispersed phase has the effect of improving the impact toughness of the material, the metallographic structure of the produced material is more uniform by adding the dispersed phase solid solution, the phase structure composition of the hard phase is improved, and the strength and the toughness of the carbonitride-based cermet material are greatly improved.
In order to better understand the above technical solutions, the above technical solutions will be described in detail with reference to specific embodiments.
Example 1
The embodiment provides a carbonitride-based cermet, which comprises the following components in parts by weight:
20 parts of bonding phase, 10 parts of hard phase and 70 parts of dispersed phase.
In the carbonitride-based cermet, the bonding phase is formed by mixing Co powder and Ni powder according to a mass ratio of 1: 1. The average particle size of the Co powder was 0.8. mu.m. The average particle size of the Ni powder was 0.8. mu.m.
The hard phase is (Ti, W, M) CN solid solution, and the M is at least one of Hf, Zr and V;
(Ti, W, M) the molar percentages of Ti, W and M in solid solution in CN are:
w: 15 mol%, M: 3 mol% and the balance Ti. The hard phase has an average particle diameter of 1 to 2 μm.
The dispersed phase is (Ti, Ta, Nb, Mo) CN solid solution. In the (Ti, Ta, Nb, Mo) CN solid solution, the mass ratio of TiC, TiN, TaC, NbC and Mo2C is 30:30:10:10: 20.
The particle size of the dispersed phase solid solution powder is controlled to be 2-3 μm.
Example 2
The embodiment provides a carbonitride-based cermet, which comprises the following components in parts by weight:
30 parts of bonding phase and 20 parts of hard phase; 50 parts of a dispersed phase.
In the carbonitride-based cermet, the bonding phase is formed by mixing Co powder and Ni powder according to a mass ratio of 2: 1. The average particle size of the Co powder was 1.0. mu.m. The average particle diameter of the Ni powder was 1.0. mu.m.
The hard phase is (Ti, W, M) CN solid solution, and the M is at least one of Hf, Zr and V;
(Ti, W, M) the molar percentages of Ti, W and M in solid solution in CN are:
w: 30 mol%, M: 15 mol% and the balance Ti.
The particle size of the hard phase solid solution powder is controlled to be 1-2 μm.
The dispersed phase is (Ti, Ta, Nb, Mo) CN solid solution. In the (Ti, Ta, Nb, Mo) CN solid solution, the mass ratio of TiC, TiN, TaC, NbC and Mo2C is 30:30:10:10: 2.
The particle size of the dispersed phase solid solution powder is controlled to be 2-3 μm.
Example 3
The embodiment provides a carbonitride-based cermet, which comprises the following components in parts by weight:
20 parts of bonding phase and 20 parts of hard phase; 60 parts of a dispersed phase.
The bonding phase is formed by Co and Ni;
the hard phase is (Ti, W, M) CN solid solution, and the M is at least one of Hf, Zr and V;
the dispersed phase is (Ti, Ta, Nb, Mo) CN solid solution.
In the carbonitride-based cermet, the bonding phase is formed by mixing Co powder and Ni powder according to a mass ratio of 1.5: 1. The average particle size of the Co powder was 0.8. mu.m. The average particle diameter of the Ni powder was 1.0. mu.m.
The hard phase solid solution has an average particle diameter of 1 to 2 μm. The particle size of the dispersed phase solid solution powder is controlled to be 2-3 μm.
The addition amount of the hard phase is 20 percent, and the molar percentages of Ti, W and M in (Ti, W and M) CN solid solution are as follows:
w: 20 mol%, M: 9 mol% and the balance Ti.
The addition amount of the dispersed phase is 60%, and TiC, TiN, TaC, NbC and Mo in the dispersed phase solid solution (Ti, Ta, Nb, Mo) CN solid solution2The mass ratio of C is 30:30:10:10: 20.
Example 4
The embodiment provides a preparation process of carbonitride-based cermet, which comprises the following steps:
s1: weighing the bonding phase and the hard phase according to the proportion, and wet-grinding and uniformly mixing to obtain mixed powder;
s2: adding a forming agent into the mixed powder obtained in the step S1, drying, granulating, and then pressing and forming to obtain a blank body;
s3: and (5) sintering the blank obtained in the step S2 to obtain the carbonitride-based cermet.
In the preparation process, the wet grinding medium in the step S1 is absolute ethyl alcohol, the addition amount of the absolute ethyl alcohol is 700m L added to each kilogram of powder raw material, the wet grinding time is 36-60 h, the ball-to-material ratio of the wet grinding is (4-6): 1, the concentration of PEG is 4%, the sintering temperature is 1450-1500 ℃, and the sintering time is 1-2 h.
Example 5
In this example, a carbonitride based cermet having a Co content of 6 to 10 wt.% and a Ni content of 6 to 10 wt.% was prepared.
The hard phase solid solution comprises the following components:
a1 solid solution TiC: TiN: WC: HfC is 30:30:35:5, and the powder granularity is 2-3 mu m;
a2 solid solution TiC: TiN: WC: ZrC is 30:30:33:7, and the powder granularity is 2-3 mu m;
a3 solid solution TiC: TiN: WC: VC is 30:30:37:3, and the powder granularity is 2-3 mu m;
a4 solid solution TiC: TiN: WC: ZrC is 30:30:37:3, and the powder particle size is 2-3 mu m;
the components of the solid solution of the dispersed phase are as follows: TiC: TiN: TaC, NbC: mo2C is 30:30:10:10:20, and the powder granularity is 2-3 mu m.
The preparation method of the carbonitride-based cermet comprises the following steps:
(1) respectively weighing Co and Ni according to a formula in a table 1, and weighing a hard phase solid solution and a dispersed phase solid solution, wherein the average particle sizes of the Co and the Ni are respectively 1 mu m;
(2) using absolute ethyl alcohol as a wet grinding medium, and carrying out ball milling for 60h to uniformly mix the raw materials, wherein: the ball-material ratio is 5:1, and the addition amount of the ball-milling medium is 700 ml per kg of the powder raw material;
(3) and mixing the materials with PEG, drying and granulating for 2h, pressing into a blade blank, sintering at 1475 ℃ for 1h in vacuum, and sintering at 4-6 MPa for 0.5h in Ar gas for low pressure to obtain metal ceramic cutter materials A1, A2, A3 and A4.
TABLE 1
Figure BDA0002192754160000081
Comparative example 1
In this example, a carbonitride based cermet was prepared, which was different from example 5 in that in example 5, TiC, TiN, WC, TaC, Mo2C, etc. are added as solid solution (W, Ti, Ta, Mo) CN, in this case TiC, TiN, WC, TaC, NbC, Mo2The carbide forms of C and the like are independently added to prepare the traditional TiC base metal ceramic cutter material with the same component.
Cermet cutting tool materials B1, B2, B3, and B4 were obtained according to the composition ratios of table 2 under the same preparation conditions as in example 5 without changing the element ratios.
TABLE 2
Figure BDA0002192754160000082
Detection example 1
Tool materials of the cermet tool material a series prepared in example 5 and the cermet tool material B series prepared in comparative example 1 were manufactured into CNMG120408 inserts and were dulled to an R of 0.05mm at the insert edge. The outer circle of 45 steel HB270 was cut under conditions of V250 m/min, F0.2 and Ap 1.0, the cutting time was measured when the flank wear value of each insert reached Vb 0.2mm, and the edge chipping condition was observed, and the measurement and observation results are shown in table 3.
TABLE 3
Figure BDA0002192754160000091
As can be seen from table 3, the carbonitride-based cermet according to the embodiments of the present invention has significantly superior cutting performance compared to the conventional TiC-based cermet material, and the a-based tool made of the carbonitride-based cermet according to the embodiments of the present invention can greatly improve the cutting ability and the service life of the tool compared to the B-based tool made of the conventional cermet.
Detection example 2
In this example, metallographic structure diagrams of the cermet cutting material a prepared in example 5 and the cermet cutting material B prepared in comparative example 1 were observed, as shown in fig. 1 and 2.
In the drawing, FIG. 1 is a metallographic structure diagram (after etching) of a cermet cutting material A prepared in example 5, in which a gray phase is a hard phase, a white phase of a core is a dispersed phase, and a black phase is an etched binder phase (Co, Ni).
FIG. 2 is a metallographic structure diagram (after corrosion) of a cermet cutting material B prepared in comparative example 1. As can be seen from a comparison between fig. 1 and fig. 2, the material structure of the a-series cermet material prepared in example 5 is more uniform, because the addition of the hard phase in the carbonitride based cermet component of the a-series cermet material prepared in example 5 increases the high temperature red hardness of the material, and the addition of the dispersed phase improves the phase structure composition of the hard phase, so that the produced material structure is more uniform, thereby greatly improving the toughness of the carbonitride based cermet material, and combining the above factors, the final cermet material has high toughness, good high temperature red hardness, excellent wear resistance, heat resistance and impact resistance.

Claims (10)

1. The carbonitride-based cermet is characterized by comprising the following components in parts by weight:
10-30 parts of a bonding phase,
10 to 30 parts of a hard phase,
30-70 parts of a dispersed phase,
the hard phase is (Ti, W, M) CN solid solution, wherein M is at least one of Hf, Zr and V;
the dispersed phase is (Ti, Ta, Nb, Mo) CN solid solution.
2. The carbonitride-based cermet according to claim 1, wherein the binder phase is Co powder and Ni powder in a mass ratio of (1-2): 1.
3. The carbonitride-based cermet according to claim 2, characterized in that the Co powder has an average particle diameter of 0.8 to 1.5 μm.
4. The carbonitride-based cermet according to claim 2, characterized in that the Ni powder has an average particle diameter of 0.5 to 1.5 μm.
5. The carbonitride-based cermet according to claim 1, characterized in that the molar percentages of Ti, W and M in solid solution in the (Ti, W, M) CN are:
W：15～30mol％，
M：3～15mol％，
the balance being Ti.
6. The carbonitride based cermet according to claim 1, characterized in that the (Ti, Ta, Nb, Mo) CN solid solution consists of the following components in mass percent:
TiN：10～30％，
TaC：10～20％，
NbC：10～20％，
Mo2C：20～30％，
the balance being TiC.
7. The process for producing a carbonitride based cermet according to any one of claims 1 to 6, characterized by comprising the steps of:
s1: weighing the bonding phase and the hard phase according to the proportion, and wet-grinding and uniformly mixing to obtain mixed powder;
s2: adding a forming agent into the mixed powder obtained in the step S1, drying, granulating, and then pressing and forming to obtain a blank body;
s3: and (5) sintering the blank obtained in the step S2 to obtain the carbonitride-based cermet.
8. The process for preparing carbonitride-based cermet according to claim 7, wherein the wet milling medium of step S1 is absolute ethanol.
9. The process for preparing a carbonitride based cermet according to claim 7 wherein the forming agent is PEG.
10. The process for preparing carbonitride based cermet according to claim 7, wherein the sintering temperature is 1450-1500 ℃ and the sintering time is 1-2 hours.
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