CN110257681B - Polycrystalline cubic boron nitride composite sheet and preparation method thereof - Google Patents

Polycrystalline cubic boron nitride composite sheet and preparation method thereof Download PDF

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CN110257681B
CN110257681B CN201910538131.8A CN201910538131A CN110257681B CN 110257681 B CN110257681 B CN 110257681B CN 201910538131 A CN201910538131 A CN 201910538131A CN 110257681 B CN110257681 B CN 110257681B
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boron nitride
cubic boron
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莫培程
林峰
谢志刚
陈超
陈家荣
贾光
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China Nonferrous Metal Guilin Geology and Mining 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
    • 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
    • B22F3/12—Both compacting and sintering
    • B22F3/14—Both compacting and sintering simultaneously
    • 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
    • C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
    • C22C2026/003—Cubic boron nitrides only

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Abstract

The invention provides a polycrystalline cubic boron nitride composite sheet and a preparation method thereof, and belongs to the field of preparation of superhard composite material cutters. The polycrystalline cubic boron nitride composite sheet provided by the invention is prepared from the following components in percentage by mass: 55 to 95 percent of cubic boron nitride, 4 to 38 percent of bonding agent and 1 to 7 percent of sintering aid; the bonding agent is boron carbide and titanium powder, and the sintering aid comprises aluminum nitride, aluminum oxide and cobalt powder. The invention adds cubic boron nitride and a bonding agent with specific proportion and dosage to ensure that the cubic boron nitride and the bonding agent generate new phase TiN and TiB in situ in the sintering process2And TiC firmly bonds cubic boron nitride, and the bending strength and hardness of the polycrystalline cubic boron nitride composite sheet are effectively improved. The example result shows that the hardness of the polycrystalline cubic boron nitride composite sheet provided by the invention is 3500-4400 HV, and the bending strength is 900-1180 MPa.

Description

Polycrystalline cubic boron nitride composite sheet and preparation method thereof
Technical Field
The invention relates to the field of superhard composite material cutter preparation, in particular to a polycrystalline cubic boron nitride composite sheet and a preparation method thereof.
Background
Polycrystalline cubic boron nitride is a conglomerate which is prepared by sintering a plurality of fine cubic boron nitrides as raw materials under the conditions of high temperature and high pressure with or without additives. Polycrystalline cubic boron nitride overcomes the defects that single crystals are easy to cleave and have anisotropy; meanwhile, the wear-resistant steel also has excellent performances such as higher hardness and wear resistance, good chemical stability and thermal stability. The polycrystalline cubic boron nitride has the advantages of the properties, is widely applied, and particularly plays a great role in cutting machining as a cutter material, such as the machining of materials such as cast iron, iron-based powder metallurgy metal, quenched steel, stainless steel and the like.
However, most of polycrystalline cubic boron nitride has the problem of poor bending strength, so that the polycrystalline cubic boron nitride is easy to break when used as a cutter material, and potential safety hazards exist.
Disclosure of Invention
In view of this, the invention provides a polycrystalline cubic boron nitride compact and a preparation method thereof. The polycrystalline cubic boron nitride composite sheet provided by the invention has high bending strength.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a polycrystalline cubic boron nitride composite sheet which is prepared from the following components in percentage by mass:
55 to 95 percent of cubic boron nitride, 4 to 38 percent of bonding agent and 1 to 7 percent of sintering aid;
the bonding agent is boron carbide and titanium powder, and the sintering aid comprises aluminum nitride, aluminum oxide and cobalt powder.
Preferably, the mass ratio of the boron carbide to the titanium powder is 2-5: 10.
Preferably, the mass ratio of the aluminum nitride to the aluminum oxide to the cobalt powder is 1: 1-3: 1.
Preferably, the grain size of the cubic boron nitride is 1-22 μm.
Preferably, the average grain size of boron carbide in the bonding agent is 5-10 μm, and the average grain size of titanium powder is 1-5 μm.
The invention also provides a preparation method of the polycrystalline cubic boron nitride composite sheet in the technical scheme, which comprises the following steps:
and mixing cubic boron nitride, a binding agent and a sintering aid, and then sintering at high temperature and high pressure to obtain the polycrystalline cubic boron nitride composite sheet.
Preferably, the pressure of the high-temperature high-pressure sintering is 4-6 GPa, the temperature is 1300-1600 ℃, and the heat preservation time is 5-12 min.
Preferably, the high-temperature high-pressure sintering method further comprises pretreatment, wherein the pretreatment comprises vacuum heat treatment and reduction treatment.
Preferably, the temperature of the vacuum heat treatment is 800-1200 ℃, and the vacuum degree is 10-1Pa～10-3Pa, the time is 1-3 h.
Preferably, the temperature of the reduction treatment is 400-600 ℃, and the time is 0.5-2 h.
The invention provides a polycrystalline cubic boron nitride composite sheet which is prepared from the following components in percentage by mass: 55 to 95 percent of cubic boron nitride, 4 to 38 percent of bonding agent and 1 to 7 percent of sintering aid; the bonding agent is boron carbide and titanium powder, and the sintering aid comprises aluminum nitride, aluminum oxide and cobalt powder. The invention adds cubic boron nitride and a bonding agent with specific proportion and dosage to generate new phase TiN and TiB in situ in the sintering process2And TiC, reinforcement (TiN, TiB)2And TiC) react inside the sintered body to form and grow, and the surface is free of pollution. When in use, the reinforcement has good compatibility with the matrix and high interface bonding strength. And the generated new phases (TiN, TiB)2And TiC) firmly bonds the cubic boron nitride, so that the bending strength and the hardness of the polycrystalline cubic boron nitride composite sheet are effectively improved. According to the polycrystalline cubic boron nitride composite sheet, boron carbide and titanium powder are used as the binding agents, so that the advantages of a metal binding agent and a ceramic binding agent are achieved, and the bending strength and hardness of the polycrystalline cubic boron nitride composite sheet are effectively improved; the invention adopts aluminum nitride, aluminum oxide and cobalt powder as sintering aids, is in a molten state in the sintering process, provides a liquid phase for in-situ reaction, and improves the sintering performance of cubic boron nitride. The example result shows that the hardness of the polycrystalline cubic boron nitride composite sheet provided by the invention is 3500-4400 HV, and the bending strength is 900-1180 MPa.
Drawings
The present invention will be described in further detail with reference to the accompanying drawings and specific embodiments.
Fig. 1 is an XRD pattern of the polycrystalline cubic boron nitride compact prepared in example 1;
fig. 2 is a cross-sectional scan of the polycrystalline cubic boron nitride compact prepared in example 1.
Detailed Description
The invention provides a polycrystalline cubic boron nitride composite sheet which is prepared from the following components in percentage by mass: 55 to 95 percent of cubic boron nitride, 4 to 38 percent of bonding agent and 1 to 7 percent of sintering aid, and further preferably 65 to 85 percent of cubic boron nitride, 12.5 to 30 percent of bonding agent and 2.5 to 5 percent of sintering aid; the bonding agent is boron carbide and titanium powder, and the sintering aid comprises aluminum nitride, aluminum oxide and cobalt powder.
In the present invention, the mass ratio of the boron carbide to the titanium powder is preferably 2 to 5:10, and more preferably 4:10, and the mass ratio of the aluminum nitride, the aluminum oxide, and the cobalt powder is preferably 1:1 to 3:1, and more preferably 1:2: 1.
In the present invention, the cubic boron nitride preferably has a particle size of 1 to 22 μm, and more preferably 5 to 12 μm, and in one embodiment of the present invention, the cubic boron nitride preferably consists of three cubic boron nitrides having different particle sizes, the particle sizes of the three cubic boron nitrides are preferably 3 μm, 6 μm, and 8 μm, respectively, and the weight ratio of the three cubic boron nitrides having different particle sizes is preferably 5: 3: in the other three embodiments of the present invention, the cubic boron nitride is preferably composed of two cubic boron nitrides having different particle sizes, the particle sizes of the two cubic boron nitrides are preferably 3 μm and 6 μm, respectively, and the weight ratio of the two cubic boron nitrides having different particle sizes is preferably 1: 1; the average particle size of the boron carbide is preferably 5-10 μm, and more preferably 8 μm; the average particle size of the titanium powder is preferably 1-5 μm, and more preferably 3 μm; the average particle size of the aluminum nitride is preferably 50-200 nm, and more preferably 100-150 nm; the average particle size of the alumina is preferably 0.1-1 μm, and more preferably 0.5 μm; the average particle size of the cobalt powder is preferably 1-5 μm, and more preferably 3 μm.
The specific sources of the cubic boron nitride, the bonding agent and the sintering aid are not particularly limited, and the conventional commercial products in the field can be adopted. In the invention, the sintering aid is used for providing a liquid phase in the high-temperature and high-pressure sintering process, which is beneficial to the sintering process; the aluminum nitride in the sintering aid has excellent performances of high thermal conductivity, low thermal expansion coefficient and good impact resistance, can reduce the internal thermal stress of the polycrystalline cubic boron nitride, and can inhibit the cBN from generating phase change and converting into hBN; the addition of cobalt powder in the sintering aid can also enhance the conductivity, thereby facilitating the subsequent processing of the product.
The invention also provides a preparation method of the polycrystalline cubic boron nitride composite sheet in the technical scheme, which comprises the following steps:
and mixing cubic boron nitride, a binding agent and a sintering aid, and then sintering at high temperature and high pressure to obtain the polycrystalline cubic boron nitride composite sheet.
In the present invention, the mixing is preferably performed by ball milling, and the ball milling is preferably performed in a ball milling tank. In the invention, the ball-milled mixed medium is preferably ethanol, the ball-milled dispersion medium preferably comprises sodium polystyrene sulfonate and/or polyethyleneimine, and the ball-milled ball-to-material ratio of the ball-milled balls is preferably 3-5: 1, more preferably 4:1, the rotation speed of the ball milling is preferably 200-300 r/min, more preferably 250r/min, and the time of the ball milling is preferably 4-6 h.
After the mixing is finished, the mixed materials are preferably dried, screened and filled into a mold in sequence. In the invention, the drying temperature is preferably 70-100 ℃, more preferably 80 ℃, and the drying time is preferably 10-16 h, more preferably 12 h. In the present invention, the particle size of the sieve is preferably 50 to 200 mesh, and more preferably 100 mesh. In the present invention, the die filling is preferably performed in a molybdenum cup die for high pressure synthesis, and in the present embodiment, the diameter of the molybdenum cup die is preferably 14 mm. The specific operation of the die filling is not particularly limited in the invention, and the conventional die filling operation of a person skilled in the art can be adopted.
Before the high-temperature and high-pressure sintering, the invention preferably also comprises the step of pretreating the mixture of the cubic boron nitride, the binding agent and the sintering aid, wherein the pretreatment preferably comprises vacuum heat treatment and reduction treatment.
In the invention, the temperature of the vacuum heat treatment is preferably 800-1200 ℃, more preferably 900-1000 ℃, and the vacuum degree of the vacuum heat treatment is preferably 10-1～10-3Pa, more preferably 10-2Pa, and the time of the vacuum heat treatment is preferably 1-3 h. The specific operation of the vacuum heat treatment is not particularly limited in the present invention, and the conventional vacuum heat treatment operation can be adopted by those skilled in the art. In the invention, the vacuum heat treatment is used for removing impurities and moisture in the components and ensuring the purity of powder, thereby ensuring the performance of the polycrystalline cubic boron nitride composite sheet.
In the invention, the temperature of the reduction treatment is preferably 400-600 ℃, more preferably 450-500 ℃, the reducing atmosphere of the reduction treatment is preferably hydrogen, and the time of the reduction treatment is preferably 0.5-2 h, more preferably 1 h. The specific operation of the reduction treatment is not particularly limited, and the conventional reduction treatment operation can be adopted by a person skilled in the art. In the invention, the reduction treatment is to reduce the oxidized metal powder and ensure the purity of the powder, thereby ensuring the performance of the polycrystalline cubic boron nitride composite sheet.
In the invention, the high-temperature high-pressure sintering is preferably carried out in a cubic press, the pressure of the high-temperature high-pressure sintering is preferably 4-6 GPa, and further preferably 5.5GPa, the temperature of the high-temperature high-pressure sintering is preferably 1300-1600 ℃, and further preferably 1400-1500 ℃, and the heat preservation time of the high-temperature high-pressure sintering is preferably 5-12 min, and further preferably 6 min.
The invention adopts an in-situ synthesis method to generate a plurality of reinforcing phases (such as TiB) in situ through chemical reaction among boron carbide, titanium powder and boron nitride particles in a sintered body2TiC, TiN, etc.), thereby achieving the purpose of improving the mechanical property of the PCBN composite sheet. The reinforced phase is formed and grown in the sintered body through reaction, the surface is free of pollution, the compatibility of the matrix and the reinforced body is good, the interface bonding strength is high, and the strength and the hardness of the PCBN composite sheet can be improved.
In the invention, multiple reinforcing phases TiB are generated in situ among boron carbide, titanium powder and boron nitride particles in the sintered body2The reaction equation of TiC and TiN is shown as formula 1-2:
2BN+3Ti＝2TiN+TiB2 formula 1
B4C+3Ti＝2TiB2+ TiC formula 2
The polycrystalline cubic boron nitride compact and the method for manufacturing the polycrystalline cubic boron nitride compact according to the present invention will be described in detail with reference to the following examples, which should not be construed as limiting the scope of the present invention.
Example 1
cBN, B were prepared in the following proportions4C. Ti powder, AlN, Al2O3And Co powder:
the cubic boron nitride micro powder consists of three granularities, namely 8 microns, 6 microns and 3 microns, and the weight ratio of the three is 2: 3: 5, the three account for 85 percent of the total weight; the average particle size of boron carbide powder is 10 μm, the average particle size of titanium powder is 5 μm, and the two particles account for 12.5% of the total weight of the powder; the average particle size of the aluminum nitride powder is 50nm, the average particle size of the alumina powder is 0.5 mu m, the average particle size of the cobalt powder is 1 mu m, and the aluminum nitride powder, the alumina powder and the cobalt powder account for 2.5 percent of the total weight of the powder.
Ball-milling the components in a ball mill, and adding ethanol as a mixed medium; adding sodium polystyrene sulfonate and polyethyleneimine into an ethanol solution as a dispersion medium, wherein the ball-milling ball-material ratio is 4:1, the rotating speed is 250r/min, and the time is 6 h; drying at 80 deg.C for 12 hr, and sieving with 100 mesh sieve.
Loading the mixed materials into a molybdenum cup mold with diameter of 14mm for high-pressure synthesis at 1000 deg.C and vacuum degree of 10-2And (3) carrying out vacuum treatment on the mixed material under the Pa condition for 1 hour.
The sample is subjected to hydrogen reduction treatment at the temperature of 500 ℃ in the atmosphere of hydrogen for 0.5 h.
And synthesizing the processed sample into the polycrystalline cubic boron nitride composite sheet in a cubic press at high temperature and high pressure, wherein the pressure is 5.5GPa, the temperature is 1500 ℃, and the heat preservation time is 5 min. The prepared polycrystalline cubic boron nitride composite sheet is subjected to mechanical property test, and the test results are shown in table 1.
FIG. 1 is an XRD (X-ray diffraction) pattern of the polycrystalline cubic boron nitride composite sheet prepared in example 1, and it can be seen from the XRD pattern that the components are subjected to in-situ synthesis reaction in the sintering process, and a plurality of reinforcing phases TiB are generated in situ among boron carbide, titanium powder and boron nitride particles in a sintered body2、TiC、TiN。
Fig. 2 is a cross-sectional scan of the polycrystalline cubic boron nitride compact prepared in example 1, and it can be seen that the newly formed reinforcing phase is uniformly distributed around the cBN grains, and the cBN grains are well bonded together.
Example 2
cBN, B were prepared in the following proportions4C. Ti powder, AlN, Al2O3And Co powder:
the cubic boron nitride micro powder consists of two granularities, namely 3 microns and 6 microns, and the weight ratio of the two is 1:1, the weight of the two components accounts for 65 percent of the total weight; the average particle size of boron carbide powder is 10 μm, the average particle size of titanium powder is 5 μm, and the two particles account for 30% of the total weight of the powder; the average particle size of the aluminum nitride powder is 50nm, the average particle size of the alumina powder is 0.5 mu m, the average particle size of the cobalt powder is 1 mu m, and the three account for 5 percent of the total weight of the powder.
Ball-milling the components in a ball mill, and adding ethanol as a mixed medium; adding sodium polystyrene sulfonate and polyethyleneimine into an ethanol solution as a dispersion medium, wherein the ball-milling ball-material ratio is 3:1, the rotating speed is 200r/min, and the time is 6 h; drying at 80 deg.C for 12 hr, and sieving with 100 mesh sieve.
Loading the mixed materials into a molybdenum cup mold with diameter of 14mm for high-pressure synthesis at 900 deg.C and vacuum degree of 10-2And (3) carrying out vacuum treatment on the mixed material under the Pa condition for 1 hour.
The sample is subjected to hydrogen reduction treatment at the temperature of 450 ℃ under the condition that the atmosphere is hydrogen for 0.5 h.
And synthesizing the processed sample into the polycrystalline cubic boron nitride composite sheet in a cubic press at high temperature and high pressure, wherein the pressure is 5.5GPa, the temperature is 1400 ℃, and the heat preservation time is 5 min. The prepared polycrystalline cubic boron nitride composite sheet is subjected to mechanical property test, and the test results are shown in table 1.
Example 3
cBN, B were prepared in the following proportions4C. Ti powder, AlN, Al2O3And Co powder:
the cubic boron nitride micro powder consists of two granularities, namely 3 microns and 6 microns, and the weight ratio of the two is 1:1, the two account for 55 percent of the total weight; the average particle size of boron carbide powder is 10 μm, the average particle size of titanium powder is 5 μm, and the two particles account for 38% of the total weight of the powder; the average particle size of the aluminum nitride powder is 50nm, the average particle size of the alumina powder is 0.5 mu m, the average particle size of the cobalt powder is 1 mu m, and the aluminum nitride powder, the alumina powder and the cobalt powder account for 7 percent of the total weight of the powder.
Ball-milling the components in a ball mill, and adding ethanol as a mixed medium; adding sodium polystyrene sulfonate and polyethyleneimine into an ethanol solution as a dispersion medium, wherein the ball-milling ball-material ratio is 3:1, the rotating speed is 200r/min, and the time is 6 h; drying at 80 deg.C for 12 hr, and sieving with 100 mesh sieve.
Loading the mixed materials into a molybdenum cup mold with diameter of 14mm for high-pressure synthesis at 800 deg.C and vacuum degree of 10-3And (3) carrying out vacuum treatment on the mixed material under the Pa condition for 1 hour.
The sample is subjected to hydrogen reduction treatment at the temperature of 600 ℃ under the condition that the atmosphere is hydrogen for 0.5 h.
And synthesizing the processed sample into the polycrystalline cubic boron nitride composite sheet in a cubic press at high temperature and high pressure, wherein the pressure is 4GPa, the temperature is 1600 ℃, and the heat preservation time is 5 min. The prepared polycrystalline cubic boron nitride composite sheet is subjected to mechanical property test, and the test results are shown in table 1.
Example 4
cBN, B were prepared in the following proportions4C. Ti powder, AlN, Al2O3And Co powder:
the cubic boron nitride micro powder consists of two granularities, namely 3 microns and 6 microns, and the weight ratio of the two is 1:1, the weight of the two components accounts for 95 percent of the total weight; the average particle size of boron carbide powder is 10 μm, the average particle size of titanium powder is 5 μm, and the two particles account for 4% of the total weight of the powder; the average particle size of the aluminum nitride powder is 50nm, the average particle size of the alumina powder is 0.5 mu m, the average particle size of the cobalt powder is 1 mu m, and the aluminum nitride powder, the alumina powder and the cobalt powder account for 1 percent of the total weight of the powder.
Ball-milling the components in a ball mill, and adding ethanol as a mixed medium; adding sodium polystyrene sulfonate and polyethyleneimine into an ethanol solution as a dispersion medium, wherein the ball-milling ball-material ratio is 3:1, the rotating speed is 200r/min, and the time is 6 h; drying at 80 deg.C for 12 hr, and sieving with 100 mesh sieve.
Loading the mixed materials into a molybdenum cup mold with diameter of 14mm for high-pressure synthesis at 1200 deg.C and vacuum degree of 10-1And (3) carrying out vacuum treatment on the mixed material under the Pa condition for 1 hour.
The sample is subjected to hydrogen reduction treatment at the temperature of 400 ℃ under the condition of hydrogen atmosphere for 0.5 h.
And synthesizing the processed sample into the polycrystalline cubic boron nitride composite sheet in a cubic press at high temperature and high pressure, wherein the pressure is 6GPa, the temperature is 1300 ℃, and the heat preservation time is 5 min. The prepared polycrystalline cubic boron nitride composite sheet is subjected to mechanical property test, and the test results are shown in table 1.
Table 1 mechanical property parameters of polycrystalline cubic boron nitride compacts prepared in examples 1 to 2
Hardness (HV) Bending strength (MPa) Hardness testing method Strength testing method
Example 1 4100～4300 950～1000 Indentation method Three-point bending resistance method
Example 2 3750～3900 1100～1180 Indentation method Three-point bending resistance method
Example 3 3500～3700 950～1100 Indentation method Three-point bending resistance method
Example 4 4200～4400 900～1000 Indentation method Three-point bending resistance method
The results of the above embodiments show that the polycrystalline cubic boron nitride composite sheet provided by the invention has good mechanical properties, the hardness is 3500-4400 HV, and the bending strength is 900-1180 MPa. The technical problems that the polycrystalline cubic boron nitride is easy to break when used as a cutter material and has potential safety hazards in the prior art can be effectively solved.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.

Claims (10)

1. The polycrystalline cubic boron nitride compact is characterized by being prepared from the following components in percentage by mass:
55 to 95 percent of cubic boron nitride, 4 to 38 percent of bonding agent and 1 to 7 percent of sintering aid;
the bonding agent is boron carbide and titanium powder, and the sintering aid comprises aluminum nitride, aluminum oxide and cobalt powder.
2. The polycrystalline cubic boron nitride compact of claim 1, wherein the mass ratio of the boron carbide to the titanium powder is 2-5: 10.
3. The polycrystalline cubic boron nitride compact of claim 1, wherein the mass ratio of the aluminum nitride to the aluminum oxide to the cobalt powder is 1 (1-3) to 1.
4. The polycrystalline cubic boron nitride compact of claim 1, wherein the cubic boron nitride has a particle size of 1 to 22 μm.
5. The polycrystalline cubic boron nitride compact of claim 1, wherein the average particle size of the boron carbide in the binder is 5 to 10 μm and the average particle size of the titanium powder is 1 to 5 μm.
6. A method of making a polycrystalline cubic boron nitride compact according to any one of claims 1 to 5, comprising the steps of:
and mixing cubic boron nitride, a binding agent and a sintering aid, and then sintering at high temperature and high pressure to obtain the polycrystalline cubic boron nitride composite sheet.
7. The preparation method according to claim 6, wherein the pressure of the high-temperature high-pressure sintering is 4-6 GPa, the temperature is 1300-1600 ℃, and the holding time is 5-12 min.
8. The method according to claim 6 or 7, wherein the high-temperature high-pressure sintering is preceded by a pretreatment comprising a vacuum heat treatment and a reduction treatment.
9. The method according to claim 8, wherein the temperature of the vacuum heat treatment is 800 to 1200 ℃ and the degree of vacuum is 10-1Pa～10-3Pa, the time is 1-3 h.
10. The method according to claim 8, wherein the reduction treatment is carried out at a temperature of 400 to 600 ℃ for 0.5 to 2 hours.
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