CN115198156B - High-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet and preparation method thereof - Google Patents

High-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet and preparation method thereof Download PDF

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CN115198156B
CN115198156B CN202210792469.8A CN202210792469A CN115198156B CN 115198156 B CN115198156 B CN 115198156B CN 202210792469 A CN202210792469 A CN 202210792469A CN 115198156 B CN115198156 B CN 115198156B
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CN115198156A (en
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欧阳家虎
周生健
王玉金
陈磊
刘占国
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Harbin Institute of Technology
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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
    • 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
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Abstract

A high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet and a preparation method thereof relate to a cermet and a preparation method thereof. Objects of the inventionAims to solve the problems of great technical difficulty and poor mechanical property of preparing 100-300nm ultrafine crystal Ti (C, N) -based metal ceramic. The high strength and toughness superfine crystal Ti (C, N) -base cermet consists of Ti (C, N) 45-65 weight portions and Mo 10-30 weight portions 2 C. 3 to 10 portions of one or a mixture of two of NbC and HfC and 0.5 to 3 portions of Cr 3 C 2 And 10-30 parts of metal elements. The method comprises the following steps: 1. weighing; 2. ball milling and mixing; 3. drying and granulating; 4. compression molding; 5. and (5) sintering. The high-toughness ultrafine-grained Ti (C, N) -based cermet prepared by the method has high hardness and bending strength, and good fracture toughness.

Description

High-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet and preparation method thereof
Technical Field
The invention relates to a metal ceramic and a preparation method thereof.
Background
The Ti (C, N) -based cermet usually takes Ti (C, N) as a hard phase, ni, co and other metals as a bonding phase and transition metal carbide as an additive phase, and has hardness, wear resistance and oxidation resistance at high temperature (700-1100 ℃) obviously superior to WC-Co hard alloy, fracture toughness obviously superior to superhard materials and ceramic cutter materials, the manufactured cutter has the characteristics of high cutting speed, good quality of a processed surface, good wear resistance, long service life of the cutter and the like, makes up for the blank between WC-Co hard alloy and a ceramic cutter in the range of processing materials, and becomes a potential substitute material of WC-Co hard alloy.
At present, the further improvement of the performance of the cutter material through grain refinement is the hot point direction and the main trend of the development of the cutter material. The ultra-fining and even nano-fining of hard phase crystal grains have been studied in WC-Co hard alloy in great quantity, and satisfactory matching of hardness and toughness is obtained. However, compared to WC — Co cemented carbide, the composition of Ti (C, N) -based cermet is more complicated and limited by the technical problem of preparing high-purity ultrafine carbon (nitride) powder, and in the published reports, studies on ultrafine-grained Ti (C, N) -based cermet having a grain size of 100 to 300nm have been rarely reported. Few researches on ultra-fine grain Ti (C, N) -based cermet only focus on the refinement of the grain size of Ti (C, N) hard phase, but ignore the change of the grain growth driving force in the liquid phase sintering process caused by the grain size difference of Ti (C, N) and carbide addition phase, so that the prepared Ti (C, N) -based cermet has serious grain coarsening phenomenon, poor microstructure uniformity and poor mechanical property.
Disclosure of Invention
The invention aims to solve the problems of high technical difficulty and poor mechanical property of 100-300nm ultrafine grain Ti (C, N) -based cermet, and provides high-strength and high-toughness ultrafine grain Ti (C, N) -based cermet and a preparation method thereof.
The high strength and toughness superfine crystal Ti (C, N) -base cermet consists of Ti (C, N) 45-65 weight portions and Mo 10-30 weight portions 2 C. 3 to 10 portions of one or a mixture of two of NbC and HfC and 0.5 to 3 portions of Cr 3 C 2 And 10-30 parts of metal elements.
The preparation method of the high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet is completed by the following steps:
1. weighing:
(1) weighing 45-65 parts of Ti (C, N) and 10-30 parts of Mo according to parts by weight 2 C. 3 to 10 portions of one or a mixture of two of NbC and HfC and 0.5 to 3 portions of Cr 3 C 2 And 10-30 parts of metal elements to obtain a raw material;
(2) adding 100 parts of raw materials, 0.5-2 parts of carbon black and 1-5 parts of polyvinyl alcohol into a water/absolute ethyl alcohol mixed solution to obtain slurry;
2. ball milling and mixing:
ball-milling the slurry under the protection of nitrogen atmosphere to obtain ball-milled slurry;
3. drying and granulating:
drying the ball-milled slurry under a vacuum condition to obtain metal ceramic mixed powder;
4. compression molding:
filling the metal ceramic mixed powder into a powder pressing mold, applying pressure of 50-200 MPa for pressing and molding, and maintaining the pressure for 1-5 min to obtain a pressed blank;
5. and (3) sintering:
sintering the pressed compact by adopting vacuum sintering, nitrogen sintering or air pressure sintering, and cooling along with a furnace to obtain the high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet.
The principle of the invention is as follows:
for Ti (C, N) -based cermets prepared by liquid phase sintering, grain growth can be described by the Ostwald ripening mechanism, i.e., unsaturated coordination atoms on the surface of particles with smaller particle size (higher surface energy) will preferentially dissolve into the liquid phase metal and precipitate on the surface of undissolved particles by liquid phase diffusion, with the driving force being the difference in chemical potential between particles of different sizes; the driving force for grain growth can be expressed as:
Figure BDA0003730845800000021
wherein Δ g-driving force for grain growth (J.m) -3 )；
γ sl Solid/liquid interfacial energy (J/m) 2 )；
V m Molar volume of the solid phase (mol. M) -3 )；
Figure BDA0003730845800000022
-a critical grain size (m) that is neither growing nor dissolving;
d-size of growing or dissolved grains (m).
Based on this, the key of the invention is to prepare high-toughness ultrafine-grained Ti (C, N) -based cermet by synergistically refining the grain size of hard phase and additive phase to reduce the grain growth driving force.
The invention has the following beneficial effects:
(1) The invention is based on Ti (C, N) and Mo 2 C. bC, hfC and Cr 3 C 2 The idea of reducing the grain growth driving force by the cooperative refinement of the particle size realizes the preparation of 100-300nm high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet;
(2) The high-toughness ultrafine-grained Ti (C, N) -based cermet prepared by the method has uniform microstructure, fine grain size (100-300 nm), high hardness and bending strength, and good fracture toughness; wherein the Vickers hardness is more than or equal to 1700kgf mm -2 Bending strength is more than or equal to 2000MPa, and fracture toughness is more than or equal to 9.0 MPa.m 1/2 ；
(3) The high-toughness ultrafine-grained Ti (C, N) -based cermet prepared by the invention follows the traditional preparation process of coarse-grained and medium-grained Ti (C, N) -based cermets, does not need new process steps, is simple to operate and is suitable for large-scale industrial production.
Drawings
FIG. 1 is an SEM image of a high toughness ultra-fine grained Ti (C, N) -based cermet prepared in example 1;
FIG. 2 is an SEM image of a high toughness ultra-fine grained Ti (C, N) -based cermet prepared in example 2.
Detailed Description
The following examples further illustrate the present invention but are not to be construed as limiting the invention. Modifications and substitutions to methods, procedures, or conditions of the invention may be made without departing from the spirit of the invention.
The first embodiment is as follows: the high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet of the embodiment comprises, by weight, 45-65 parts of Ti (C, N) and 10-30 parts of Mo 2 C. 3 to 10 parts of one or a mixture of two of NbC and HfC, 0.5 to 3 parts of Cr 3 C 2 And 10-30 parts of metal elements.
The second embodiment is as follows: the present embodiment differs from the present embodiment in that: the metal element is Ni or Co. Other steps are the same as in the first embodiment.
The third concrete implementation mode: the present embodiment differs from the first or second embodiment in that: the high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet comprises, by weight, 45-65 parts of Ti (C, N) and 20 parts of Mo 2 C. 5 parts of one or a mixture of two of NbC and HfC and 1 part of Cr 3 C 2 And 10-30 parts of metal elements. Other stepsThe steps are the same as in the first or second embodiment.
The fourth concrete implementation mode: the difference between this embodiment and one of the first to third embodiments is: the preparation method of the high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet is completed by the following steps:
1. weighing:
(1) 45 to 65 portions of Ti (C, N) and 10 to 30 portions of Mo are weighed according to the weight portion 2 C. 3 to 10 portions of one or a mixture of two of NbC and HfC and 0.5 to 3 portions of Cr 3 C 2 And 10-30 parts of metal elements to obtain a raw material;
(2) adding 100 parts of raw materials, 0.5-2 parts of carbon black and 1-5 parts of polyvinyl alcohol into the water/absolute ethyl alcohol mixed solution to obtain slurry;
2. ball-milling and mixing:
ball-milling the slurry under the protection of nitrogen atmosphere to obtain ball-milled slurry;
3. drying and granulating:
drying the ball-milled slurry under a vacuum condition to obtain metal ceramic mixed powder;
4. compression molding:
filling the metal ceramic mixed powder into a powder pressing mold, applying pressure of 50-200 MPa for pressing and molding, and maintaining the pressure for 1-5 min to obtain a pressed blank;
5. and (3) sintering:
sintering the pressed compact by adopting vacuum sintering, nitrogen sintering or air pressure sintering, and cooling along with a furnace to obtain the high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet. The other steps are the same as those in the first to third embodiments.
The fifth concrete implementation mode: the difference between this embodiment and the first to the fourth embodiments is: ti (C, N), mo in step one (1) 2 C、NbC、HfC、Cr 3 C 2 And the particle size of the metal element is 100 nm-300 nm, and the oxygen content is less than 0.5wt.%. The other steps are the same as those in the first to fourth embodiments.
The sixth specific implementation mode: the difference between this embodiment and one of the first to fifth embodiments is: the solid content of the slurry in the step one (2) is 40-70 wt%; the volume ratio of water to absolute ethyl alcohol in the water/absolute ethyl alcohol mixed solution in the first step (2) is 3. The other steps are the same as those in the first to fifth embodiments.
The seventh embodiment: the difference between this embodiment and one of the first to sixth embodiments is: the ball milling in the step two is roller ball milling or stirring ball milling, the grinding ball used in the ball milling is a hard alloy ball, the ball-material ratio is (4-20): 1, and the ball milling time is 12-48 h. The other steps are the same as those in the first to sixth embodiments.
The specific implementation mode is eight: the difference between this embodiment and one of the first to seventh embodiments is: the vacuum sintering method in the fifth step comprises the following specific steps: placing the pressed blank in a sintering furnace, vacuumizing to below 50Pa, starting heating, heating to 1000-1300 ℃ at the heating rate of 5-10 ℃/min, preserving heat at 1000-1300 ℃ for 1-2 h, heating to 1400-1500 ℃ at the heating rate of 1-5 ℃/min, and preserving heat at 1400-1500 ℃ for 1-2 h. The other steps are the same as those in the first to seventh embodiments.
The specific implementation method nine: the difference between this embodiment and the first to eighth embodiments is: placing the pressed compact in a sintering furnace, vacuumizing to below 50Pa, starting heating, heating to 1000-1300 ℃ at the heating rate of 5-10 ℃/min, preserving heat for 1-2 h at 1000-1300 ℃, then heating to 1400-1500 ℃ at the heating rate of 1-5 ℃/min, introducing high-purity nitrogen of 1-10 kPa, and preserving heat for 1-2 h at the temperature of 1400-1500 ℃ under nitrogen. The other steps are the same as those in the first to eighth embodiments.
The specific implementation mode is ten: the difference between this embodiment and one of the first to ninth embodiments is as follows: the air pressure sintering method in the fifth step comprises the following specific steps: placing the pressed compact in a sintering furnace, vacuumizing to below 50Pa, starting heating, heating to 1000-1300 ℃ at the heating rate of 5-10 ℃/min, preserving heat for 1-2 h at 1000-1300 ℃, then heating to 1400-1500 ℃ at the heating rate of 1-5 ℃/min, introducing high-purity argon gas of 3-10 MPa, and preserving heat for 1-2 h at the temperature of 1400-1500 ℃ under argon gas. The other steps are the same as those in the first to ninth embodiments.
The following examples were used to demonstrate the beneficial effects of the present invention:
example 1: a preparation method of high-toughness ultrafine-grained Ti (C, N) -based cermet is completed according to the following steps:
1. weighing:
(1) weighing 60 parts of Ti (C) according to parts by weight 0.5 N 0.5 ) 20 parts of Mo 2 C. 5 parts of NbC and 1 part of Cr 3 C 2 And 14 parts of Ni to obtain a raw material;
ti (C) described in step one 0.5 N 0.5 )、Mo 2 C、NbC、Cr 3 C 2 And Ni has a particle size of 100nm to 300nm and an oxygen content of less than 0.5wt.%;
(2) adding 100 parts of raw materials, 0.5 part of carbon black and 3 parts of polyvinyl alcohol into a water/absolute ethyl alcohol mixed solution to obtain slurry;
2. ball milling and mixing:
ball-milling the slurry under the protection of nitrogen atmosphere to obtain ball-milled slurry;
the solid content of the slurry in the step one (2) is 50wt.%; the volume ratio of water to absolute ethyl alcohol in the water/absolute ethyl alcohol mixed solution in the step one (2) is 3;
the ball milling in the step two is roller ball milling, the grinding balls used in the ball milling are hard alloy balls, the ball-to-material ratio is 10, and the ball milling time is 24 hours;
3. drying and granulating:
drying the ball-milled slurry under a vacuum condition to obtain metal ceramic mixed powder;
4. compression molding:
filling the metal ceramic mixed powder into a powder pressing mold, applying 150MPa pressure for pressing and molding, and maintaining the pressure for 3min to obtain a pressed blank;
5. and (3) sintering:
and placing the pressed compact in a sintering furnace, vacuumizing to below 50Pa, starting heating, heating to 1300 ℃ at the heating rate of 10 ℃/min, preserving heat for 1h at 1300 ℃, then heating to 1450 ℃ at the heating rate of 5 ℃/min, preserving heat for 1.5h at 1450 ℃, and cooling along with the furnace to obtain the high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet.
The high toughness ultra fine grained Ti (C, N) -based cermet prepared in example 1 had uniform microstructure, fine grains (100-300 nm), and excellent overall properties, wherein the Vickers hardness was 1720 kgf. Mm -2 Flexural strength of 2150MPa and fracture toughness of 9.2MPa · m 1/2 。
Example 2: the present example is different from example 1 in that: step one (1), weighing 60 parts of Ti (C) according to parts by weight 0.5 N 0.5 ) 18 parts of Mo 2 C. 7 parts of HfC and 1 part of Cr 3 C 2 And 14 parts of Ni to obtain a raw material; ti (C) as described in step one 0.5 N 0.5 )、Mo 2 C、HfC、Cr 3 C 2 And Ni has a particle size of 100nm to 300nm and an oxygen content of less than 0.5wt.%. The other steps and parameters were the same as in example 1.
FIG. 2 is an SEM image of a high toughness ultra-fine grained Ti (C, N) -based cermet prepared in example 2;
as can be seen from FIG. 2, by synergistically refining the particle sizes of the hard phase and the additive phase, the grain growth driving force can be effectively reduced, and the preparation of 100-300nm ultra-fine grain Ti (C, N) -based cermet is realized.
The ultra-fine grain cermet of the high toughness ultra-fine grain Ti (C, N) -based cermet prepared in example 2 had a uniform microstructure, fine grains (100 to 300 nm), and excellent comprehensive properties, wherein the Vickers hardness was 1740 kgf. Mm -2 Bending strength of 2200MPa and fracture toughness of 9.5 MPa-m 1/2 。
Example 3: the present embodiment is different from embodiment 1 in that: step one (1), weighing 60 parts of Ti (C) according to parts by weight 0.5 N 0.5 ) 18 parts of Mo 2 C. 3.5 parts of NbC powder, 3.5 parts of HfC powder and 1 part of Cr powder 3 C 2 And 14 parts of Ni to obtain a raw material; ti (C) described in step one 0.5 N 0.5 )、Mo 2 C、NbC、HfC、Cr 3 C 2 And Ni has a particle size of 100nm to 300nm and an oxygen content of less than 0.5wt.%. Other steps and parameters were the same as in example 1。
The ultrafine grained cermet prepared in example 3 had a uniform microstructure, fine grains (100 to 300 nm), and excellent overall properties, in which the Vickers hardness was 1720 kgf. Mm -2 Bending strength of 2050MPa and fracture toughness of 9.2 MPa-m 1/2 。
Example 4: the present example is different from example 1 in that: and fifthly, placing the pressed compact in a sintering furnace, vacuumizing to below 50Pa, starting heating, heating to 1300 ℃ at the heating rate of 10 ℃/min, preserving heat for 1h at 1300 ℃, then heating to 1500 ℃ at the heating rate of 5 ℃/min, preserving heat for 1.5h at 1500 ℃, and cooling along with the furnace to obtain the high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet. The other steps and parameters were the same as in example 1.
The ultra-fine grain cermet prepared in example 4 has a uniform microstructure, fine grains (100 to 300 nm), and excellent overall properties, in which the Vickers hardness is 1710kgf mm -2 The bending strength is 2100MPa, and the fracture toughness is 9.5 MPa.m 1/2 。
Example 5: the present embodiment is different from embodiment 1 in that: and fifthly, placing the pressed compact in a sintering furnace, vacuumizing to below 50Pa, starting heating, heating to 1300 ℃ at the heating rate of 10 ℃/min, preserving heat for 1h at 1300 ℃, then heating to 1450 ℃ at the heating rate of 5 ℃/min, introducing high-purity nitrogen with the pressure of 5kPa, preserving heat for 1h at the temperature of 1450 ℃ in nitrogen, and cooling along with the furnace to obtain the high-strength-toughness ultrafine-grain Ti (C, N) -based cermet. The other steps and parameters were the same as in example 1.
The ultra-fine grain cermet prepared in example 5 has a uniform microstructure, fine grains (100-300 nm), and excellent overall properties, in which the Vickers hardness is 1735 kgf. Mm -2 Flexural strength of 2150MPa and fracture toughness of 9.4MPa · m 1/2 。
Example 6: the present example is different from example 1 in that: and fifthly, placing the pressed compact in a sintering furnace, vacuumizing to below 50Pa, starting heating, heating to 1300 ℃ at the heating rate of 10 ℃/min, preserving heat for 1h at 1300 ℃, then heating to 1450 ℃ at the heating rate of 5 ℃/min, introducing high-purity argon gas with the pressure of 3MPa, preserving heat for 1h at the temperature of 1450 ℃ under the argon gas, and cooling along with the furnace to obtain the high-strength-toughness ultrafine-grain Ti (C, N) -based cermet. The other steps and parameters were the same as in example 1.
The ultra-fine grain cermet prepared in example 6 has a uniform microstructure, fine grains (100 to 300 nm), and excellent overall properties, in which the Vickers hardness is 1750 kgf. Mm -2 Flexural strength of 2400MPa and fracture toughness of 9.6 MPa-m 1/2 。

Claims (3)

1. A preparation method of high-toughness ultrafine-grained Ti (C, N) -based cermet is characterized in that the preparation method of the high-toughness ultrafine-grained Ti (C, N) -based cermet is completed according to the following steps:
1. weighing:
(1) weighing 45-65 parts of Ti (C, N) and 10-30 parts of Mo according to parts by weight 2 C. 3 to 10 parts of one or a mixture of two of NbC and HfC, and 0.5 to 3 parts of Cr 3 C 2 And 10-30 parts of metal elements to obtain a raw material;
the metal element in the step one (1) is Ni or Co;
ti (C, N), mo in step one (1) 2 C、NbC、HfC、Cr 3 C 2 The particle size of the metal element ranges from 100nm to 300nm, and the oxygen content is lower than 0.5 wt%;
(2) adding 100 parts of raw materials, 0.5-2 parts of carbon black and 1-5 parts of polyvinyl alcohol into a water/absolute ethyl alcohol mixed solution to obtain slurry;
2. ball milling and mixing:
ball-milling the slurry under the protection of nitrogen atmosphere to obtain ball-milled slurry;
3. drying and granulating:
drying the ball-milled slurry under a vacuum condition to obtain metal ceramic mixed powder;
4. compression molding:
filling the metal ceramic mixed powder into a powder pressing die, then applying pressure of 50MPa to 200MPa to press and form, and keeping the pressure for 1min to 5min to obtain a pressed blank;
5. and (3) sintering:
sintering the pressed compact by adopting vacuum sintering, nitrogen sintering or air pressure sintering, and cooling along with a furnace to obtain high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet;
the vacuum sintering method in the fifth step specifically comprises the following steps: placing the pressed blank in a sintering furnace, vacuumizing to below 50Pa, starting heating, heating to 1000-1300 ℃ at a heating rate of 5-10 ℃/min, preserving heat at 1000-1300 ℃ for 1h-2h, then heating to 1400-1500 ℃ at a heating rate of 1-5 ℃/min, and preserving heat at 1400-1500 ℃ for 1h-2h;
the nitrogen sintering method in the fifth step specifically comprises the following steps: placing the pressed blank in a sintering furnace, vacuumizing to below 50Pa, starting heating, heating to 1000-1300 ℃ at a heating rate of 5-10 ℃/min, preserving heat at 1000-1300 ℃ for 1h-2h, then heating to 1400-1500 ℃ at a heating rate of 1-5 ℃/min, introducing high-purity nitrogen of 1kPa-10kPa, and preserving heat at 1400-1500 ℃ for 1h-2h;
the air pressure sintering method in the fifth step specifically comprises the following steps: placing the pressed compact in a sintering furnace, vacuumizing to below 50Pa, starting heating, heating to 1000-1300 ℃ at a heating rate of 5-10 ℃/min, preserving heat at 1000-1300 ℃ for 1h-2h, then heating to 1400-1500 ℃ at a heating rate of 1-5 ℃/min, introducing high-purity argon gas at 3-10MPa, and preserving heat at 1400-1500 ℃ for 1h-2h;
the grain size of the high-strength and high-toughness ultrafine-grained Ti (C, N) -based cermet is 100-300nm, and the Vickers hardness is more than or equal to 1700 kgf.mm -2 Bending strength is not less than 2000MPa, and fracture toughness is not less than 9.0 MPa.m 1/2 。
2. The method for preparing the high-toughness ultra-fine grain Ti (C, N) -based cermet according to claim 1, wherein the slurry in the step one (2) has a solid content ranging from 40wt.% to 70wt.%; the volume ratio of water to absolute ethyl alcohol in the water/absolute ethyl alcohol mixed solution in the first step (2) is 3.
3. The preparation method of the high-toughness ultrafine-grained Ti (C, N) -based cermet according to claim 1, wherein the ball milling in the second step is roller ball milling or stirring ball milling, the ball milling ball is cemented carbide ball, the ball-to-material ratio is (4-20): 1, and the ball milling time is 12h-48h.
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