CN112142481B - A kind of binder for synthesizing polycrystalline cubic boron nitride material and using method thereof - Google Patents
A kind of binder for synthesizing polycrystalline cubic boron nitride material and using method thereof Download PDFInfo
- Publication number
- CN112142481B CN112142481B CN201910564429.6A CN201910564429A CN112142481B CN 112142481 B CN112142481 B CN 112142481B CN 201910564429 A CN201910564429 A CN 201910564429A CN 112142481 B CN112142481 B CN 112142481B
- Authority
- CN
- China
- Prior art keywords
- boron nitride
- cubic boron
- binder
- intermetallic compound
- polycrystalline cubic
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 229910052582 BN Inorganic materials 0.000 title claims abstract description 76
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 title claims abstract description 76
- 239000011230 binding agent Substances 0.000 title claims abstract description 57
- 239000000463 material Substances 0.000 title claims abstract description 36
- 230000002194 synthesizing effect Effects 0.000 title claims abstract description 23
- 238000000034 method Methods 0.000 title abstract description 15
- 239000000843 powder Substances 0.000 claims abstract description 43
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 35
- 238000005245 sintering Methods 0.000 claims abstract description 17
- 239000010936 titanium Substances 0.000 claims abstract description 17
- 239000002245 particle Substances 0.000 claims abstract description 15
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 13
- 238000009489 vacuum treatment Methods 0.000 claims abstract description 13
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 12
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 8
- 238000002156 mixing Methods 0.000 claims abstract description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 5
- 238000000498 ball milling Methods 0.000 claims description 27
- 238000000227 grinding Methods 0.000 claims description 15
- 239000000203 mixture Substances 0.000 claims description 9
- 239000010935 stainless steel Substances 0.000 claims description 6
- 229910001220 stainless steel Inorganic materials 0.000 claims description 6
- 230000015572 biosynthetic process Effects 0.000 claims description 3
- 238000003786 synthesis reaction Methods 0.000 claims description 3
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims description 2
- 238000012856 packing Methods 0.000 claims 1
- 239000002131 composite material Substances 0.000 abstract description 2
- 238000005516 engineering process Methods 0.000 abstract description 2
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 2
- 229910052721 tungsten Inorganic materials 0.000 abstract description 2
- 229910052720 vanadium Inorganic materials 0.000 abstract description 2
- 229910052751 metal Inorganic materials 0.000 description 14
- 239000002184 metal Substances 0.000 description 14
- 239000000919 ceramic Substances 0.000 description 7
- 238000005452 bending Methods 0.000 description 6
- 239000011812 mixed powder Substances 0.000 description 5
- 239000012071 phase Substances 0.000 description 5
- GJNGXPDXRVXSEH-UHFFFAOYSA-N 4-chlorobenzonitrile Chemical compound ClC1=CC=C(C#N)C=C1 GJNGXPDXRVXSEH-UHFFFAOYSA-N 0.000 description 3
- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 description 3
- 229910033181 TiB2 Inorganic materials 0.000 description 3
- 238000005299 abrasion Methods 0.000 description 3
- 239000000853 adhesive Substances 0.000 description 3
- 230000001070 adhesive effect Effects 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 229910010038 TiAl Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000011049 filling Methods 0.000 description 2
- 229910017083 AlN Inorganic materials 0.000 description 1
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 239000007767 bonding agent Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 229910003465 moissanite Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 239000004065 semiconductor Substances 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/63—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B using additives specially adapted for forming the products, e.g.. binder binders
- C04B35/6303—Inorganic additives
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
- C04B35/583—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on boron nitride
- C04B35/5831—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on boron nitride based on cubic boron nitrides or Wurtzitic boron nitrides, including crystal structure transformation of powder
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/40—Metallic constituents or additives not added as binding phase
- C04B2235/402—Aluminium
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/40—Metallic constituents or additives not added as binding phase
- C04B2235/404—Refractory metals
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/656—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes characterised by specific heating conditions during heat treatment
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/658—Atmosphere during thermal treatment
- C04B2235/6581—Total pressure below 1 atmosphere, e.g. vacuum
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Ceramic Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Structural Engineering (AREA)
- Organic Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Ceramic Products (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
Abstract
本发明涉及超硬复合材料技术，具体涉及一种聚晶立方氮化硼材料合成用粘结剂及其使用方法。所述粘结剂为金属间化合物；所述金属间化合物中含有铝、钛和M；所述M选自Cr,Nb,W,Mo,V中的至少一种；且所述金属间化合物中钛、铝的原子比例占金属间化合物的90‑95％。所述粘接剂的应用为：按体积比，粘结剂颗粒：立方氮化硼粉末＝10‑30：70‑90，配取粘结剂颗粒和立方氮化硼粉末；混合均匀后进行真空处理；真空处理后，在高温、高压的环境下进行烧结，得到聚晶立方氮化硼。本发明所开发的粘结剂为低温制备高性能聚晶氮化硼提供了必要条件。本发明粘结剂组分设置合理，应用工艺简单可控、所得产品性能优良，便于大规模的工业化应用。The invention relates to superhard composite material technology, in particular to a binder for synthesizing polycrystalline cubic boron nitride materials and a method for using the same. The binder is an intermetallic compound; the intermetallic compound contains aluminum, titanium and M; the M is selected from at least one of Cr, Nb, W, Mo, and V; and the intermetallic compound is The atomic ratio of titanium and aluminum accounts for 90-95% of the intermetallic compound. The application of the binder is as follows: by volume ratio, binder particles: cubic boron nitride powder = 10-30: 70-90, the binder particles and the cubic boron nitride powder are prepared; after mixing uniformly, vacuum Treatment; after vacuum treatment, sintering is carried out in a high temperature and high pressure environment to obtain polycrystalline cubic boron nitride. The binder developed in the present invention provides necessary conditions for preparing high-performance polycrystalline boron nitride at low temperature. The binder component of the invention is reasonably set, the application process is simple and controllable, the obtained product has excellent performance, and is convenient for large-scale industrial application.
Description
Technical Field
The invention relates to a superhard composite material technology, in particular to a binder for synthesizing a polycrystalline cubic boron nitride material and a using method thereof.
Background
Cubic boron nitride has not only high hardness but also excellent thermal and chemical stability, and does not react with iron-based metals at high temperatures. Because cubic boron nitride is formed by high-strength covalent bonds, the sintering of high-purity cubic boron nitride is quite difficult and is not suitable for industrial production, and therefore, a certain amount of bonding agent is added into cubic boron nitride to prepare polycrystalline cubic boron nitride, so that good cutting performance is obtained. Therefore, the high hardness, thermal stability and chemical inertness of the material are utilized to prepare cutters and grinding tools, and the material can be widely applied to processing various ferrous metal materials and alloys and tough and difficult-to-process materials.
Meanwhile, with the research on high-temperature p-n junctions, the high-temperature semiconductor characteristics of cubic boron nitride attract certain attention, so that the cubic boron nitride becomes a potential functional material. Therefore, the research on a new method, a new theory and new characteristics of cubic boron nitride synthesis has important practical significance.
The high strength covalent bond of cubic boron nitride makes sintering of high purity cubic boron nitride quite difficult, and therefore a certain amount of binder is used to prepare polycrystalline cubic boron nitride. Al, Ti, AlN, SiC and the like are commonly used as a binder. However, the ceramic binder has the problems of poor high-temperature thermal conductivity, difficult sintering densification, weak bending strength and fracture toughness and the like. When the metal binder is used for working at a high temperature, the wear resistance of the tool is greatly reduced due to the softening of the metal, and the red hardness is reduced. The intermetallic compound has the characteristics of metal and ceramic at the same time, and has great potential as a binder.
Disclosure of Invention
Aiming at the defects of the prior art, the invention firstly provides that an intermetallic compound is used as a binder for synthesizing the polycrystalline cubic boron nitride material; meanwhile, an optimized use method of the adhesive is developed.
The invention relates to a binder for synthesizing a polycrystalline cubic boron nitride material; the binder is an intermetallic compound; the intermetallic compound contains aluminum, titanium and M; the M is at least one selected from Cr, Nb, W, Mo and V; and the atomic ratio of titanium and aluminum in the intermetallic compound accounts for 90-95% of the intermetallic compound.
The invention relates to a binder for synthesizing a polycrystalline cubic boron nitride material; the binder is granular before use, and the grain diameter of the binder is less than or equal to 75 microns.
As a preferred scheme, the invention relates to a binder for synthesizing a polycrystalline cubic boron nitride material; the intermetallic compound is composed of Ti, Al, Cr and Nb in molar ratio; ti: 40-50 of Al, 40-50 of Al: 40-50:2-5 of Cr, Al: nb is 40-50: 2-7. As a further preferable scheme, the invention provides a binder for synthesizing a polycrystalline cubic boron nitride material; the intermetallic compound is formed by Ti, Al, Cr and Nb according to molar ratio; ti: al: cr: nb 48-50: 48-50: 2: 2. as a further preferable mode, the intermetallic compound is formed by mixing Ti, Al, Cr, Nb in a molar ratio; ti: al: cr: nb 48: 48: 2: 2.
preferably, the inventionThe invention relates to a binder for synthesizing a polycrystalline cubic boron nitride material; the loose packed density is 3.9-4.2g/cm3。
The invention relates to an application of a binder for synthesizing a polycrystalline cubic boron nitride material, wherein the binder comprises the following particles in percentage by volume: cubic boron nitride powder 10-30: 70-90, preferably 20-30:70:80, and further preferably 1:4, and preparing binder particles and cubic boron nitride powder; after being uniformly mixed, the mixture is subjected to vacuum treatment; and after vacuum treatment, sintering the polycrystalline cubic boron nitride in a high-temperature and high-pressure environment to obtain the polycrystalline cubic boron nitride.
The cubic boron nitride powder has a particle size of less than 10 microns.
Preferably, the application of the binder for synthesizing the polycrystalline cubic boron nitride material comprises the following components in percentage by volume: cubic boron nitride powder 10-30: 70-90, preferably 20-30:70:80, and further preferably 1:4, and preparing binder particles and cubic boron nitride powder; firstly, carrying out cold air ball milling treatment on the prepared binder particles; after ball milling treatment, adding cubic boron nitride powder for mixing; to obtain uniformly mixed powder. During the cold air ball milling treatment, the ball milling rotation speed is controlled to be 250-350 r/min, preferably 280-320 r/min; the time is 10 to 20 hours; the mass ratio of the ball material is 10-15: 1. preferably 10: 1; the cold air temperature is-30 to-10 ℃. During the cold air ball milling treatment, protective gas is filled in a ball milling cavity; and cold air is used as a cooling medium of the ball milling cavity.
According to the application of the binder for synthesizing the polycrystalline cubic boron nitride material, the grinding balls used for ball milling are made of stainless steel or agate balls. The cold air is air.
The uniformly mixed powder is firstly subjected to vacuum treatment for at least 8 hours under 1000 Pa; and after vacuum treatment, sintering the polycrystalline cubic boron nitride in a high-temperature and high-pressure environment to obtain the polycrystalline cubic boron nitride. The high temperature is greater than or equal to 1150 ℃, and certainly comprises the temperature of more than 1150-1195 ℃ and 1195 ℃. Of course, the temperatures of the prior art can also be used in the present invention. The adhesive provided by the invention realizes that the high-performance polycrystalline cubic boron nitride is prepared at the temperature lower than 1200 ℃ (such as 1150 ℃ -1195 ℃) for the first time. The high voltage of the present invention is that of the prior art.
The binder designed by the invention is optimized and combined with an application process, the hardness of the obtained product can be 37-43GPa, and the fracture toughness can be 5.6-6.7 MPa.m1/2. Is far higher than the similar products on the market.
Principles and advantages
The metal binder widely used at present is melted at high temperature to fill gaps of CBN, and simultaneously can react with the CBN to generate corresponding boride and nitride, the CBN is combined through bonding of a metal element-B/N formed by the products, sintering conditions are improved, but the hardness and the high-temperature performance of the PCBN can be reduced, the ceramic binder has high melting point and basically does not react with the CBN in a solid phase manner, so that the obtained PCBN has better hardness, thermal stability and wear resistance, but lacks of filling gaps, and the toughness and compactness are not as good as those of the PCBN using the metal binder.
The chemical bond between atoms in the intermetallic compound used by the invention has the properties of both an ionic bond and a covalent bond, so that the intermetallic compound has the characteristics of metal and ceramic at the same time and has certain strength and toughness at room temperature and high temperature. In the development process of the present invention, it is found that at a certain temperature and pressure, the intermetallic compound of a specific composition reacts with CBN, taking TiAl as an example, and the reaction occurs as follows:
TiAl+BN→TiB2+AlN
the invention provides a method for synthesizing polycrystalline cubic boron nitride material, which generates a corresponding metal element-B/N bonded ceramic phase, can reduce the sintering temperature, increase the sintering degree and improve the sintering performance, and provides the method for synthesizing polycrystalline cubic boron nitride material by using an intermetallic compound as a binder for synthesizing the polycrystalline cubic boron nitride material for the first time; meanwhile, an optimized use method of the adhesive is developed. The developed binder can also avoid metal residues left in the sintering process, so that the high-temperature softening of the product is avoided to a certain extent, and the purpose of prolonging the service life is further achieved.
The binder developed by the invention provides necessary conditions for preparing high-performance polycrystalline cubic boron nitride at low temperature. The invention realizes the preparation of the high-performance polycrystalline cubic boron nitride at the temperature lower than 1200 ℃ (such as 1150 ℃ -1195 ℃) for the first time.
The binder developed by the invention is used as the binder for synthesizing the polycrystalline cubic boron nitride material, and when the volume ratio of the intermetallic compound powder: when the cubic boron nitride powder and the intermetallic compound powder are mixed in a ratio of 20:80, the hardness of the obtained product is 40-42GPa, and the fracture toughness is 6.3-6.5 MPa.m1/2Bending strength 623-. Is far higher than similar products on the market.
Drawings
FIG. 1 is a schematic diagram of a cubic boron nitride superhard material prepared in example 1 of the present invention
FIG. 2 is a phase composition diagram of a cubic boron nitride superhard material prepared in example 1 of the present invention
Fig. 3 is a scanning electron microscope image of the cubic boron nitride superhard material prepared in example 1 of the present invention: (a)2.5k times; (b)5k times; (c)10k times.
FIG. 4 is a diagram of a cutter made of cubic boron nitride superhard material prepared in example 1 of the present invention after grinding: (a)200 times of the total weight of the powder; (b)500 times; (c)1000 times.
Detailed Description
Example 1
Taking a molar ratio; ti: al: cr: nb 48: 48: 2: 2, preparing intermetallic compound powder.
Preparing a grinding ball and an intermetallic compound according to a ball milling mass ratio of 10: 1; intermetallic compound powder by volume ratio: preparing cubic boron nitride powder at a ratio of 20: 80; the grinding balls are made of stainless steel;
adding the grinding balls and the intermetallic compound into a ball mill for cold air ball milling; the rotating speed of cold air ball milling is 300 r/min, the time is 20 hours, and the temperature of the cold air is-30 ℃; then adding the prepared cubic boron nitride powder; ball milling is carried out for 8 hours at 250 revolutions per minute, and powder which is evenly mixed is obtained.
The uniformly mixed powder is firstly subjected to vacuum treatment for 8 hours under 1000 Pa; and after vacuum treatment, sintering the polycrystalline cubic boron nitride in a high-temperature and high-pressure environment to obtain the polycrystalline cubic boron nitride, wherein the high temperature is 1190 ℃, and the high pressure is 5.0GPa.
The hardness of the obtained product is 42GPa, and the fracture toughness is 6.5 MPa.m1/2Bending strength 627MPa, abrasion ratio 4437.
As shown in FIG. 1, the PcBN product prepared was very dense;
as shown in FIG. 2, the phase composition of the prepared PcBN product forms AlN and TiB2 ceramic phases in the sintering process after the intermetallic compound binder is added;
as shown in fig. 3, in the PcBN sample, a ceramic phase formed by sintering after adding an intermetallic compound was distributed at the cBN grain boundary, filling the gap, forming a covalent bond compound mainly composed of AlN and TiB2 and bonding the cBN grains;
as shown in FIG. 4, the PcBN sample obtained by sintering is made into a cutter and ground, the situation of the edge after grinding is shown in the figure, and the manufactured cutter has good performance and considerable service life.
Example 2
Taking a molar ratio; ti: al: cr: nb 43: 48: 2: 7 preparing intermetallic compound powder.
Preparing a grinding ball and an intermetallic compound according to a ball milling mass ratio of 10: 1; intermetallic compound powder by volume ratio: preparing cubic boron nitride powder at a ratio of 20: 80; the grinding balls are made of stainless steel;
adding the grinding balls and the intermetallic compound into a ball mill for cold air ball milling; the rotating speed of cold air ball milling is 300 r/min, the time is 20 hours, and the temperature of the cold air is-30 ℃; then adding the prepared cubic boron nitride powder; ball milling is carried out for 8 hours at 250 revolutions per minute, and uniformly mixed powder is obtained;
the uniformly mixed powder is firstly subjected to vacuum treatment for 8 hours under 1000 Pa; and after vacuum treatment, sintering the polycrystalline cubic boron nitride in a high-temperature and high-pressure environment to obtain the polycrystalline cubic boron nitride, wherein the high temperature is 1200 ℃, and the high pressure is 5.0GPa.
The hardness of the obtained product is 40GPa, and the fracture toughness is 6.3 MPa.m1/2Bending strength 623MPa, and abrasion ratio 4378.
Comparative example 1
The other conditions were the same as in example 1 except that:
according to the molar ratio; ti: al: cr: nb 35: 48: 15: 2, preparing Ti powder, Al powder, Cr powder and Nb powder.
Preparing a grinding ball and metal powder according to a ball milling mass ratio of 10: 1; metal powder by volume ratio: 20:80 of cubic boron nitride powder; the grinding balls are made of stainless steel; ball milling without cold air, and mixing;
the hardness of the obtained product is only 36.5GPa, and the fracture toughness is only 6.0 MPa.m1/2Bending strength 580MPa, wear ratio 4038.
Comparative example 2
The other conditions were the same as in example 1 except that:
according to the molar ratio; ti: al: cr: nb 48: 48: 2: 2, preparing Ti powder, Al powder, Cr powder and Nb powder.
Preparing a grinding ball and metal powder according to a ball milling mass ratio of 10: 1; metal powder by volume ratio: 20:80 of cubic boron nitride powder; the grinding balls are made of stainless steel; ball-milling the mixture by non-cold air,
the hardness of the obtained product is only 35.5GPa, and the fracture toughness is only 5.7 MPa.m1/2Bending strength 520MPa, and abrasion ratio 3898.
Claims (8)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910564429.6A CN112142481B (en) | 2019-06-27 | 2019-06-27 | A kind of binder for synthesizing polycrystalline cubic boron nitride material and using method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910564429.6A CN112142481B (en) | 2019-06-27 | 2019-06-27 | A kind of binder for synthesizing polycrystalline cubic boron nitride material and using method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112142481A CN112142481A (en) | 2020-12-29 |
| CN112142481B true CN112142481B (en) | 2021-09-24 |
Family
ID=73870028
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201910564429.6A Active CN112142481B (en) | 2019-06-27 | 2019-06-27 | A kind of binder for synthesizing polycrystalline cubic boron nitride material and using method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112142481B (en) |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20010062076A (en) * | 1999-12-03 | 2001-07-07 | 오카야마 노리오 | Coated pcbn cutting tools |
| CN106660888A (en) * | 2014-07-08 | 2017-05-10 | 六号元素(英国)有限公司 | Cubic boron nitride composite material, method of using it, method of making it and tool comprising it |
| CN107098704A (en) * | 2017-05-08 | 2017-08-29 | 中原工学院 | A kind of preparation method of polycrystalline cubic boron nitride sintered material |
| CN107973606A (en) * | 2017-10-23 | 2018-05-01 | 富耐克超硬材料股份有限公司 | Polycrystalline cubic boron nitride, preparation method and applications, the cutter comprising the polycrystalline cubic boron nitride |
| CN108165855A (en) * | 2017-12-15 | 2018-06-15 | 富耐克超硬材料股份有限公司 | A kind of bonding agent, polycrystalline cubic boron nitride compound sheets and preparation method thereof |
-
2019
- 2019-06-27 CN CN201910564429.6A patent/CN112142481B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20010062076A (en) * | 1999-12-03 | 2001-07-07 | 오카야마 노리오 | Coated pcbn cutting tools |
| CN106660888A (en) * | 2014-07-08 | 2017-05-10 | 六号元素(英国)有限公司 | Cubic boron nitride composite material, method of using it, method of making it and tool comprising it |
| CN107098704A (en) * | 2017-05-08 | 2017-08-29 | 中原工学院 | A kind of preparation method of polycrystalline cubic boron nitride sintered material |
| CN107973606A (en) * | 2017-10-23 | 2018-05-01 | 富耐克超硬材料股份有限公司 | Polycrystalline cubic boron nitride, preparation method and applications, the cutter comprising the polycrystalline cubic boron nitride |
| CN108165855A (en) * | 2017-12-15 | 2018-06-15 | 富耐克超硬材料股份有限公司 | A kind of bonding agent, polycrystalline cubic boron nitride compound sheets and preparation method thereof |
Non-Patent Citations (2)
| Title |
|---|
| 不同聚晶立方氮化硼复合刀具加工等温淬火球墨铸铁的切削性能对比;张弘等;《机械工程材料》;20080831;第32卷(第08期);第43-46页 * |
| 张弘等.不同聚晶立方氮化硼复合刀具加工等温淬火球墨铸铁的切削性能对比.《机械工程材料》.2008,第32卷(第08期),第43-46页. * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN112142481A (en) | 2020-12-29 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP2907315B2 (en) | Production of polycrystalline cubic boron nitride | |
| JP3309897B2 (en) | Ultra-hard composite member and method of manufacturing the same | |
| CN112500178B (en) | ZrB generated in situ 2 -SiC toughened PcBN cutter and preparation method thereof | |
| CN110903091B (en) | SiC-Ti3SiC2Composite material and preparation method thereof | |
| CN103030396A (en) | Boron carbide silicon carbide composite ceramic and preparation method thereof | |
| CN105728734B (en) | High-strength superfine ultra-fine（TixBy‑TiC）/ 7075Al composites and preparation method thereof | |
| CN106587088A (en) | Novel ternary osmium-ruthenium-boron compound hard material and preparation method thereof | |
| CN111979462A (en) | A kind of WC-MoC-Co-Y2O3 cemented carbide with high hardness and preparation method thereof | |
| CN103243252B (en) | Binder-phase wolfram-carbide (WC) hard alloy and preparation method thereof | |
| CN105755304B (en) | A kind of AlMgB14The preparation method of ultra hard ceramic powder body material | |
| JP6344975B2 (en) | Diamond composite sintered body and manufacturing method thereof | |
| CN112142481B (en) | A kind of binder for synthesizing polycrystalline cubic boron nitride material and using method thereof | |
| CN104775046A (en) | A kind of TiC-Ni3Al composite material and preparation method thereof | |
| JPS6132275B2 (en) | ||
| CN111979463A (en) | A kind of WC-Co-Y2O3-Zr cemented carbide with excellent comprehensive mechanical properties and preparation method thereof | |
| JPH10310838A (en) | Ultra-hard composite member and method of manufacturing the same | |
| CN107043260A (en) | A kind of novel tertiary osmium rhenium diboride (Os1 xRexB2) hard material and preparation method thereof | |
| Li et al. | Fabrication and performance evaluation of metal bond diamond tools based on aluminothermic reaction | |
| CN110241351B (en) | A kind of high-hardness and high-strength polycrystalline cubic boron nitride and its manufacturing method | |
| CN105624513A (en) | Dedicated carbide-based high-entropy alloy ceramic bond for PCBN (Polycrystalline Cubic Boron Nitride) | |
| Liang et al. | Self-propagation high-temperature sintering of the Ti–Al–C-diamond/BN system | |
| CN104907564B (en) | Preparation method for Ti3SiC2-Co based diamond ultra-thin saw blade materials | |
| JP2006001829A (en) | Titanium carbide sintered body or titanium silicon carbide sintered body, manufacturing method, processing method or coating method, and substrate for same | |
| CN112239360A (en) | A Tungsten Carbide Composite Material Synergistically Toughened by Boron Oxide and Magnesium Oxide and Their Reaction Products and Its Preparation | |
| JPH0215515B2 (en) |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |