CN108642361B - High-strength high-hardness ceramic material and production process thereof - Google Patents
High-strength high-hardness ceramic material and production process thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
Abstract
A high-strength high-hardness ceramic material comprises the following components in percentage by weight: a high-strength high-hardness ceramic material comprises the following components in percentage by weight: 50-52 parts of TiC, 13-14 parts of TiN and Cr3C21‑2、WC 7‑8、HfC 5‑6、TaC 3‑4、La2O31-2 parts of titanium, 5-6 parts of Co, 3-4 parts of Mn, 5-6 parts of Ni, 4-5 parts of Fe, and the balance of Al and inevitable impurities, wherein the ratio of TiC/TiN is 3.6-4; after component proportioning, ball milling, molding and vacuum hot pressing sintering, the final ceramic material has the hardness of HRA94-100, the bending strength of 2400-2600MPa and the fracture toughness of 12-13 MPa-m1/2The coefficient of thermal conductivity is 95-105W/(m.K), and the coefficient of linear expansion is 2.8 multiplied by 10‑6/℃‑3.8×10‑6/℃。
Description
Technical Field
The invention belongs to the technical field of ceramic materials, and particularly relates to a high-strength high-hardness ceramic material and a production process thereof.
Background
Cermet is composed of hard phase such as TiC and TiN and binder phase such as cobalt and nickel, and has attracted general attention at home and abroad due to its high hardness, wear resistance, red hardness, excellent chemical stability and low friction coefficient, and has been widely used in cutting tools in countries such as japan. The binding phase in the metal ceramic is mainly used for improving the toughness of the ceramic, but the metal binding phase is seriously softened at high temperature in the cutting process, so that the performance of the metal ceramic is reduced. There is an increasing research and application in this area to further improve the properties and extend the service life of cermet materials. The long-range ordered arrangement of atoms in the intermetallic compound and the coexistence of metal bonds and covalent bonds enable the intermetallic compound to simultaneously have the plasticity of metal and the high-temperature strength of ceramic, thereby becoming a high-temperature material with relatively high potential, and the performance of the cermet is improved by using the intermetallic compound as the binding phase of the cermet. However, the uniform dispersion of the hard phase, the reinforcing phase and the binding phase has problems all the time, and the service life of the product is influenced.
However, Ti (C, N) -based ceramics have the weakness of insufficient strength and toughness in terms of service performance, which not only affects the service life thereof, but also limits the range of use thereof. Therefore, how to improve the toughness of Ti (C, N) -based cermets is a concern for materials workers. The wear resistance and the toughness of the Ti (C, N) -based cermet are mutually contradictory, but a non-uniform structure material can be considered, so that the components and the microstructure of the material are distributed in a step manner, a hard phase enrichment area is formed on the surface layer, and a bonding phase enrichment area is formed in the structure. The method of physical coating or chemical coating is one of the common methods for generating wear-resistant coating on the surface of substrate material, but the surface of the material prepared by the method and the substrate have obvious interfaces in components, microstructures and the like, and the thermal expansion coefficients of the surface and the substrate are different, so that the surface hardening layer is easy to crack and even fall off. In addition, due to the fact that a large amount of friction heat exists near the cutting surface in the specific using process of the cutter, the heat conduction rate of the cutter surface is inconsistent with that of the inner portion of the core, the temperature difference between the inner portion and the outer portion is increased continuously in long-term operation, and considering that the Ti (C, N) -based metal ceramic hard phase structure is a typical core-ring structure, namely, the hard phase structure is divided into an inner core, an inner ring and an outer ring, the ceramic material divided from the structure is prone to thermal fracture caused by thermal stress due to the temperature difference.
Disclosure of Invention
Therefore, it is desirable to provide a high-strength and high-hardness ceramic material for cutting tools, which has a long service life, high strength, high hardness, and strong heat conductivity. In order to achieve the above object, the present invention requires, on the one hand, control of the composition of the ceramic material and, on the other hand, strict control of the production process of the ceramic material.
The technical scheme is as follows:
a high-strength high-hardness ceramic material comprises the following components in percentage by weight: the hard phase is TiC + TiN, the reinforcing phase is at least 2 of Cr3C2, WC, HfC, TaC and La2O3, and the binder phase is at least 2 of Co, Mn, Ni, Fe and Al.
A high-strength high-hardness ceramic material comprises the following components in percentage by weight: 50-52 parts of TiC, 13-14 parts of TiN, 3C21-2 parts of Cr, 7-8 parts of WC, 5-6 parts of HfC, 3-4 parts of TaC, 3-2 parts of La2O31-2 parts of Co, 5-6 parts of Mn, 5-6 parts of Ni, 4-5 parts of Fe, and the balance of Al and inevitable impurities, wherein the ratio of TiC to TiN is 3.6-4.
Further: a high-strength high-hardness ceramic material comprises the following components in percentage by weight: TiC50, TiN 13, Cr3C21, WC7, HfC 5, TaC 3, La2O31, Co 5, Mn 3, Ni 5, Fe 4, and the balance of Al and inevitable impurities, wherein the TiC/TiN ratio is 3.85.
Further: a high-strength high-hardness ceramic material comprises the following components in percentage by weight: TiC 50.5, TiN 13.5, Cr3C21.5, WC 7.5, HfC 5, TaC 3, La2O31, Co 5, Mn 3, Ni 5, Fe 4, the balance being Al and unavoidable impurities, the TiC/TiN ratio being 3.74.
Further: a high-strength high-hardness ceramic material comprises the following components in percentage by weight: TiC 51, TiN 14, Cr3C21, WC7, HfC 5, TaC 3, La2O31, Co 5, Mn 3, Ni 5, Fe 4, and the balance of Al and inevitable impurities, wherein the TiC/TiN ratio is 3.64.
The specific preparation steps of the high-strength and high-hardness ceramic material are as follows:
(1) preparing the following components: the preparation method comprises the following steps of proportioning according to target components, wherein the size of TiC and TiN is 300-800 nanometers, the size of Cr3C2, WC, HfC, TaC and La2O3 is 1-3 micrometers, Co, Mn, Ni, Fe and Al are added in the form of Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder, the size is 10-20 micrometers, the production of the Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder comprises the steps of firstly selecting raw materials with the purity of more than or equal to 99.9% for smelting, removing impurities to obtain an alloy solution with high purity, and then carrying out atomization for milling, wherein the specific technological parameters of the atomization for milling are as follows: the liquid flow rate is 10 kg/min-15 kg/min, the atomizing medium is nitrogen, the atomizing airflow pressure is 10 MPa-15 MPa, and the diameter of an atomizing nozzle of the atomizing rapid condensing device is 5 mm-6 mm; after the atomization is finished, completely cooling the powder, and screening in a nitrogen protective atmosphere to obtain Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder with the particle size of 10-20 microns;
(2) ball milling: putting the raw materials prepared in the step (1) into a vacuum ball milling tank, weighing anhydrous ethanol with the weight accounting for 30-40% of the weight of the raw materials prepared in the step (1) and paraffin with the weight accounting for 10-20% of the weight of the raw materials prepared in the step (1) to mix to serve as a medium, wherein the ball-material ratio is 10: 1, in order to prevent powder from being oxidized in the ball milling process, argon is used as protective gas, ball milling is carried out for 48 hours, and vacuum drying and sieving are carried out;
(3) molding: putting the ceramic powder obtained in the step (2) into a die, performing compression molding by adopting a two-way press, pressurizing two ends, pressurizing for two times, heating to 800 ℃ at a heating rate of 30-40 ℃/min in a first pressurizing state, and keeping for 2-3 hours at 20MPa, heating to 1200 ℃ at a heating rate of 20-30 ℃/min in a second pressurizing state, and keeping for 2-3 hours at 20MPa, completing the dewaxing step at this stage, finishing a pressed blank after molding, and checking the appearance quality;
(4) vacuum hot-pressing sintering: putting the pressed compact obtained in the step (3) into a vacuum hot-pressing sintering furnace, keeping the sintering temperature at 1550 ℃ and the sintering pressure at 30MPa for 1 hour, and filling argon gas 20min before the final sintering is completed until the sintering is completed, thus obtaining a metal ceramic sample; through detection, the hardness of the final ceramic material is HRA94-100, the bending strength is 2400-2600MPa, and the fracture toughness is 12-13 MPa.m1/2The coefficient of thermal conductivity is 95-105W/(m.K), and the coefficient of linear expansion is 2.8 multiplied by 10-6/℃-3.8×10-6/℃。
Further: ball milling: putting the raw materials prepared in the step (1) into a vacuum ball milling tank, weighing anhydrous ethanol accounting for 35% of the weight of the raw materials prepared in the step (1), weighing paraffin accounting for 15% of the weight of the raw materials prepared in the step (1), mixing the anhydrous ethanol and the paraffin as a medium, wherein the ball-material ratio is 10: 1, ball-milling for 48 hours by taking argon as protective gas in order to avoid powder from being oxidized in the ball milling process, and carrying out vacuum drying and sieving.
Further: step (3) forming: and (3) putting the ceramic powder obtained in the step (2) into a die, performing compression molding by adopting a two-way press, pressurizing two ends, pressurizing for two times, heating to 800 ℃ at a heating rate of 35 ℃/min in the first pressurizing state, keeping the temperature for 2.5 hours under 20MPa, heating to 1200 ℃ at a heating rate of 25 ℃/min in the second pressurizing state, keeping the temperature for 2.5 hours under 20MPa, completing the dewaxing step at this stage, trimming the pressed blank after molding, and checking the appearance quality.
Next, the reason for limiting the chemical components of the present invention will be described. Here, the% of the component means mass%.
TiC and TiN are important basic hard phases of the metal ceramic material, belong to a face-centered cubic structure, and can form solid solution with various transition metal carbides. The proportion of TiC and TiN greatly influences the performance of the final metal ceramic. Compared with the common metal ceramic material with wider ratio of TiC and TiN materials, the invention discovers that the TiC/TiN ratio is 3.6-4, and the system has good long service life, high strength, high hardness and heat conductivity. Therefore, the ratio of TiC 50-52%, TiN 13-14% and TiC/TiN is 3.6-4.
High melting point carbides such as Cr3C2, WC, HfC, TaC also have important effects on the cermet material. The vickers hardness of the Ti (C, N) -based cermet is affected by the amount of WC added as well as the flexural strength, and the vickers hardness of the Ti (C, N) -based cermet increases and then decreases as the amount of WC added increases. This is mainly because WC enhances the wettability of the hard phase, refines the grains, reduces the porosity, and thus increases the hardness of the cermet. However, when the amount of WC added exceeds 8%, the solubility of WC in the solid solution is close to saturation, so that the hard phase crystal grains become large, the ring phase becomes thick, and the hardness of WC is inherently lower than that of TiC, so that the hardness of the Ti (C, N) -based metal is drastically lowered. Therefore, WC is 7-8%.
Because Cr and W are elements of the same group, carbide of Cr and W can be well dissolved in TiC and TiN, and when the content of Cr3C2 is excessive, crystal grains on a fracture of the cermet material are pulled out to leave more dimples, the structure is compact, and the bending strength is highest; the fracture toughness is just opposite, so that the suitable Cr3C2 is determined to be 1-2% after the comprehensive measurement of the bending strength and the fracture toughness.
The crystal structures of HfC and TaC are face-centered cubic structures, the melting point is high and close to (4000 ℃), the hardness is high, the binding force of Hf, Ta and C, N is strong, and a compound with high thermal stability can be formed, so that the high-temperature cutting performance of the Ti (C, N) -based metal ceramic cutter can be improved by adding HfC and TaC. And the content is not more and better, and the HfC is determined to be 5-6% and the TaC is determined to be 3-4% through experiments.
Co exhibits a close-packed hexagonal structure or a mixed face-centered cubic structure at normal temperature. Co has better toughness, can effectively block cracks, reduce grain boundary fracture and improve the ductility of the material. Therefore, the cermet having Co as a binder phase of the present invention has more excellent toughness than other binder phase cermets. The metal Ni is a main binding phase material of general Ti (C, N) -based metal ceramics due to excellent toughness and good interface matching degree; co has toughness superior to that of Ni, can obviously wet the interface between hard phase and binding phase, and when the Ni content is high, the toughness of Ti (C, N) -based metal ceramic can be improved. The binder phase of Ti (C, N) -based cermet is usually Ni-Mn, Ni-Co, and from the viewpoint of resources and production costs, attempts have been made to partially or totally replace Ni-Mn, Ni-Co with readily available Cr, Fe, Al, Cu, Ti, rare earth, etc. The high-entropy alloy is a direction which is very concerned in the field of materials at present, has the excellent characteristics of high hardness, high strength, high-temperature oxidation resistance, corrosion resistance and the like, and based on the advantages of the high-entropy alloy, the high-entropy alloy is prepared by smelting at first and then atomized to prepare powder, and the prepared powder is uniform in degree, very little in segregation, good in appearance, convenient to sinter, and good in high hardness, high strength and high heat conduction effect. In the invention, Co is 5-6%, Mn is 3-4%, Ni is 5-6%, Fe is 4-5%, and Al is 1-5%.
The ball milling process, the forming process and the sintering process all have important influence on the performance of the Ti (C, N) -based metal ceramic. The invention ensures that the Ti (C, N) -based metal ceramic has a high compact state by carrying out heat preservation and pressure maintaining at a plurality of stages, thereby ensuring that the Ti (C, N) -based metal ceramic has high-standard comprehensive mechanical properties.
Effect of sintering temperature on grain size of sintered body it was found through experiments that the grains of Ti (C, N) -based cermet grow as the sintering temperature increases. According to the invention, fine La2O3 is added as an inhibitor, so that the growth of crystal grains can be well inhibited. Generally, when sintering is carried out at a lower temperature, the growth of Ti (C, N) -based cermet grains can be inhibited by adding a small amount of inhibitor; as the sintering temperature increases, Ti (C, N) -based cermet crystal grains tend to grow, discontinuous growth of the crystal grains cannot be inhibited even if a sintering grain inhibitor is added, but fine Ti (C, N) -based cermet crystal grains can be obtained by sintering at 1550 ℃ and a sintering pressure of 30MPa for 1 hour.
Generally, the density of a sintered body increases as the sintering temperature increases, because the content of a liquid phase in the sintered body increases as the temperature increases, facilitating diffusion and migration of a substance. As the sintering temperature increases, the density of the sintered body does not increase but gradually decreases. By performing a weight loss test on the sintered sample, it was found that the weight loss of the sintered body at high temperature sintering was always larger than that at low temperature sintering, and therefore, the reason for the decrease in density of the sintered body with the increase in sintering temperature was the evaporation of a small amount of binder phase. The sintering time determines whether the binder phase can sufficiently penetrate into the gaps between the particles, and analysis of the density of the sintered body shows that sintering at 1550 ℃ for 1 hour at a sintering pressure of 30MPa is sufficient to fully densify the Ti (C, N) -based cermet.
Compared with the prior art, the invention has the technical effects that:
1. the invention ensures the uniformity of the mechanical property of the Ti (C, N) -based metal ceramic by accurately controlling the components and the production process of the product, has high strength, high toughness, wear resistance, high hardness, high thermal conductivity coefficient and low linear expansion coefficient, and prolongs the service life.
2. According to the invention, through the accurate control of the binder phase alloy elements, compared with common alloy elements with large proportion in the metal ceramic material, the process cost is saved, and the product competitiveness is improved.
3. The invention combines reasonable chemical component design with specific production process, the hardness of the final ceramic material is HRA94-100, the bending strength is 2400-2600MPa, and the fracture toughness is 12-13 MPa.m1/2The coefficient of thermal conductivity is 95-105W/(m.K), and the coefficient of linear expansion is 2.8 multiplied by 10-6/℃-3.8×10-6/℃。
Detailed Description
The technical solution of the present invention will be described in detail with reference to exemplary embodiments. Example embodiments may, however, be embodied in many different forms and should not be construed as limited to the embodiments set forth herein; rather, these embodiments are provided so that this disclosure will be thorough and complete, and will fully convey the concept of example embodiments to those skilled in the art.
Example 1
A high-strength high-hardness ceramic material comprises the following components in percentage by weight: 50-52 parts of TiC, 13-14 parts of TiN, 3C21-2 parts of Cr, 7-8 parts of WC, 5-6 parts of HfC, 3-4 parts of TaC, 3-2 parts of La2O31-2 parts of Co, 5-6 parts of Mn, 5-6 parts of Ni, 4-5 parts of Fe, and the balance of Al and inevitable impurities, wherein the ratio of TiC to TiN is 3.6-4; the preparation method comprises the following specific steps:
(1) preparing the following components: the preparation method comprises the following steps of proportioning according to target components, wherein the size of TiC and TiN is 300-800 nanometers, the size of Cr3C2, WC, HfC, TaC and La2O3 is 1-3 micrometers, Co, Mn, Ni, Fe and Al are added in the form of Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder, the size is 10-20 micrometers, the production of the Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder comprises the steps of firstly selecting raw materials with the purity of more than or equal to 99.9% for smelting, removing impurities to obtain an alloy solution with high purity, and then carrying out atomization for milling, wherein the specific technological parameters of the atomization for milling are as follows: the liquid flow rate is 10 kg/min-15 kg/min, the atomizing medium is nitrogen, the atomizing airflow pressure is 10 MPa-15 MPa, and the diameter of an atomizing nozzle of the atomizing rapid condensing device is 5 mm-6 mm; after the atomization is finished, completely cooling the powder, and screening in a nitrogen protective atmosphere to obtain Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder with the particle size of 10-20 microns;
(2) ball milling: putting the raw materials prepared in the step (1) into a vacuum ball milling tank, weighing anhydrous ethanol with the weight accounting for 30-40% of the weight of the raw materials prepared in the step (1) and paraffin with the weight accounting for 10-20% of the weight of the raw materials prepared in the step (1) to mix to serve as a medium, wherein the ball-material ratio is 10: 1, in order to prevent powder from being oxidized in the ball milling process, argon is used as protective gas, ball milling is carried out for 48 hours, and vacuum drying and sieving are carried out;
(3) molding: putting the ceramic powder obtained in the step (2) into a die, performing compression molding by adopting a two-way press, pressurizing two ends, pressurizing for two times, heating to 800 ℃ at a heating rate of 30-40 ℃/min in a first pressurizing state, and keeping for 2-3 hours at 20MPa, heating to 1200 ℃ at a heating rate of 20-30 ℃/min in a second pressurizing state, and keeping for 2-3 hours at 20MPa, completing the dewaxing step at this stage, finishing a pressed blank after molding, and checking the appearance quality;
(4) vacuum hot-pressing sintering: putting the pressed compact obtained in the step (3) into a vacuum hot-pressing sintering furnace, keeping the sintering temperature at 1550 ℃ and the sintering pressure at 30MPa for 1 hour, and filling argon gas 20min before the final sintering is completed until the sintering is completed, thus obtaining a metal ceramic sample;
through detection, the hardness of the final ceramic material is HRA94-100, the bending strength is 2400-2600MPa, and the fracture toughness is 12-13 MPa.m1/2The coefficient of thermal conductivity is 95-105W/(m.K), and the coefficient of linear expansion is 2.8 multiplied by 10-6/℃-3.8×10-6/℃。
Comparative example 1
A high-strength high-hardness ceramic material comprises the following components in percentage by weight: 40-42 parts of TiC, 23-24 parts of TiN, 7-8 parts of Cr3C21-2 parts of WC, 5-6 parts of HfC, 3-4 parts of TaC, 3-2 parts of La2O31-2 parts of Co, 5-6 parts of Mn, 5-6 parts of Ni, 4-5 parts of Fe, and the balance of Al and inevitable impurities; the preparation method comprises the following specific steps:
(1) preparing the following components: the preparation method comprises the following steps of proportioning according to target components, wherein the size of TiC and TiN is 300-800 nanometers, the size of Cr3C2, WC, HfC, TaC and La2O3 is 1-3 micrometers, Co, Mn, Ni, Fe and Al are added in the form of Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder, the size is 10-20 micrometers, the production of the Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder comprises the steps of firstly selecting raw materials with the purity of more than or equal to 99.9% for smelting, removing impurities to obtain an alloy solution with high purity, and then carrying out atomization for milling, wherein the specific technological parameters of the atomization for milling are as follows: the liquid flow rate is 10 kg/min-15 kg/min, the atomizing medium is nitrogen, the atomizing airflow pressure is 10 MPa-15 MPa, and the diameter of an atomizing nozzle of the atomizing rapid condensing device is 5 mm-6 mm; after the atomization is finished, completely cooling the powder, and screening in a nitrogen protective atmosphere to obtain Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder with the particle size of 10-20 microns;
(2) ball milling: putting the raw materials prepared in the step (1) into a vacuum ball milling tank, weighing anhydrous ethanol with the weight accounting for 30-40% of the weight of the raw materials prepared in the step (1) and paraffin with the weight accounting for 10-20% of the weight of the raw materials prepared in the step (1) to mix to serve as a medium, wherein the ball-material ratio is 10: 1, in order to prevent powder from being oxidized in the ball milling process, argon is used as protective gas, ball milling is carried out for 48 hours, and vacuum drying and sieving are carried out;
(3) molding: putting the ceramic powder obtained in the step (2) into a die, performing compression molding by adopting a two-way press, pressurizing two ends, pressurizing for two times, heating to 800 ℃ at a heating rate of 30-40 ℃/min in a first pressurizing state, and keeping for 2-3 hours at 20MPa, heating to 1200 ℃ at a heating rate of 20-30 ℃/min in a second pressurizing state, and keeping for 2-3 hours at 20MPa, completing the dewaxing step at this stage, finishing a pressed blank after molding, and checking the appearance quality;
(4) vacuum hot-pressing sintering: putting the pressed compact obtained in the step (3) into a vacuum hot-pressing sintering furnace, keeping the sintering temperature at 1550 ℃ and the sintering pressure at 30MPa for 1 hour, and filling argon gas 20min before the final sintering is completed until the sintering is completed, thus obtaining a metal ceramic sample;
through detection, the hardness of the final ceramic material is HRA 70-82, the bending strength is 1800-2000MPa, and the fracture toughness is 7-8 MPa.m1/2The coefficient of thermal conductivity is 80-83W/(m.K), and the coefficient of linear expansion is 4 multiplied by 10-6/℃-5×10-6/℃。
Comparative example 2
A high-strength high-hardness ceramic material comprises the following components in percentage by weight: 50-52 parts of TiC, 13-14 parts of TiN, 8-10 parts of WC, 5-6 parts of HfC, 3-4 parts of TaC, 5-6 parts of Co, 3-4 parts of Mn, 5-6 parts of Ni, 4-5 parts of Fe, and the balance of Al and inevitable impurities, wherein the ratio of TiC to TiN is 3.6-4; the preparation method comprises the following specific steps:
(1) preparing the following components: the preparation method comprises the following steps of proportioning according to target components, wherein the size of TiC and TiN is 300-800 nanometers, the size of WC, HfC and TaC is 1-3 micrometers, Co, Mn, Ni, Fe and Al are added in the form of Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder, the size is 10-20 micrometers, and the production of the Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder comprises the steps of firstly selecting raw materials with the purity of more than or equal to 99.9% for smelting, removing impurities to obtain an alloy solution with high purity, and then carrying out atomization powder preparation, wherein the specific technological parameters of the atomization powder preparation are as follows: the liquid flow rate is 10 kg/min-15 kg/min, the atomizing medium is nitrogen, the atomizing airflow pressure is 10 MPa-15 MPa, and the diameter of an atomizing nozzle of the atomizing rapid condensing device is 5 mm-6 mm; after the atomization is finished, completely cooling the powder, and screening in a nitrogen protective atmosphere to obtain Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder with the particle size of 10-20 microns;
(2) ball milling: putting the raw materials prepared in the step (1) into a vacuum ball milling tank, weighing anhydrous ethanol with the weight accounting for 30-40% of the weight of the raw materials prepared in the step (1) and paraffin with the weight accounting for 10-20% of the weight of the raw materials prepared in the step (1) to mix to serve as a medium, wherein the ball-material ratio is 10: 1, in order to prevent powder from being oxidized in the ball milling process, argon is used as protective gas, ball milling is carried out for 48 hours, and vacuum drying and sieving are carried out;
(3) molding: putting the ceramic powder obtained in the step (2) into a die, performing compression molding by adopting a two-way press, pressurizing two ends, pressurizing for two times, heating to 800 ℃ at a heating rate of 30-40 ℃/min in a first pressurizing state, and keeping for 2-3 hours at 20MPa, heating to 1200 ℃ at a heating rate of 20-30 ℃/min in a second pressurizing state, and keeping for 2-3 hours at 20MPa, completing the dewaxing step at this stage, finishing a pressed blank after molding, and checking the appearance quality;
(4) vacuum hot-pressing sintering: putting the pressed compact obtained in the step (3) into a vacuum hot-pressing sintering furnace, keeping the sintering temperature at 1550 ℃ and the sintering pressure at 30MPa for 1 hour, and filling argon gas 20min before the final sintering is completed until the sintering is completed, thus obtaining a metal ceramic sample; through detection, the hardness of the final ceramic material is HRA75-80, the bending strength is 1700-2000MPa, and the fracture toughness is 7-9 MPa.m1/2The coefficient of thermal conductivity is 82-86W/(m.K), and the coefficient of linear expansion is 4 multiplied by 10-6/℃-4.8×10-6/℃。
Comparative example 3
A high-strength high-hardness ceramic material comprises the following components in percentage by weight: TiC50, TiN 14, Cr3C21-2, WC7-8, HfC 5-6, TaC 3-4, La2O31-2, Co 1-2, Mn 2-3, Ni 2-3, Fe 4-5, and the balance of Al and inevitable impurities; the preparation method comprises the following specific steps:
(1) preparing the following components: the preparation method comprises the following steps of proportioning according to target components, wherein the size of TiC and TiN is 300-800 nanometers, the size of Cr3C2, WC, HfC, TaC and La2O3 is 1-3 micrometers, Co, Mn, Ni, Fe and Al are added in the form of Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder, the size is 10-20 micrometers, the production of the Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder comprises the steps of firstly selecting raw materials with the purity of more than or equal to 99.9% for smelting, removing impurities to obtain an alloy solution with high purity, and then carrying out atomization for milling, wherein the specific technological parameters of the atomization for milling are as follows: the liquid flow rate is 10 kg/min-15 kg/min, the atomizing medium is nitrogen, the atomizing airflow pressure is 10 MPa-15 MPa, and the diameter of an atomizing nozzle of the atomizing rapid condensing device is 5 mm-6 mm; after the atomization is finished, completely cooling the powder, and screening in a nitrogen protective atmosphere to obtain Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder with the particle size of 10-20 microns;
(2) ball milling: putting the raw materials prepared in the step (1) into a vacuum ball milling tank, weighing anhydrous ethanol with the weight accounting for 30-40% of the weight of the raw materials prepared in the step (1) and paraffin with the weight accounting for 10-20% of the weight of the raw materials prepared in the step (1) to mix to serve as a medium, wherein the ball-material ratio is 10: 1, in order to prevent powder from being oxidized in the ball milling process, argon is used as protective gas, ball milling is carried out for 48 hours, and vacuum drying and sieving are carried out;
(3) molding: putting the ceramic powder obtained in the step (2) into a die, performing compression molding by adopting a two-way press, pressurizing two ends, pressurizing for two times, heating to 800 ℃ at a heating rate of 30-40 ℃/min in a first pressurizing state, and keeping for 2-3 hours at 20MPa, heating to 1200 ℃ at a heating rate of 20-30 ℃/min in a second pressurizing state, and keeping for 2-3 hours at 20MPa, completing the dewaxing step at this stage, finishing a pressed blank after molding, and checking the appearance quality;
(4) vacuum hot-pressing sintering: putting the pressed compact obtained in the step (3) into a vacuum hot-pressing sintering furnace, keeping the sintering temperature at 1550 ℃ and the sintering pressure at 30MPa for 1 hour, and filling argon gas 20min before the final sintering is completed until the sintering is completed, thus obtaining a metal ceramic sample;
through detection, the hardness of the final ceramic material is HRA 84-88, the bending strength is 1900-2100MPa, and the fracture toughness is 8-9 MPa.m1/2The coefficient of thermal conductivity is 80-87W/(m.K), and the coefficient of linear expansion is 3.8 multiplied by 10-6/℃-4.5×10-6/℃。
Comparative example 4
A high-strength high-hardness ceramic material comprises the following components in percentage by weight: TiC50, TiN 14, Cr3C21-2, WC7-8, HfC 5-6, TaC 3-4, La2O31-2, Co 5-6, Mn 3-4, Ni 5-6, Fe 4-5, and the balance of Al and inevitable impurities; the preparation method comprises the following specific steps:
(1) preparing the following components: the preparation method comprises the following steps of proportioning according to target components, wherein the size of TiC and TiN is 300-800 nanometers, the size of Cr3C2, WC, HfC, TaC and La2O3 is 1-3 micrometers, Co, Mn, Ni, Fe and Al are added in the form of Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder, the size is 10-20 micrometers, the production of the Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder comprises the steps of firstly selecting raw materials with the purity of more than or equal to 99.9% for smelting, removing impurities to obtain an alloy solution with high purity, and then carrying out atomization for milling, wherein the specific technological parameters of the atomization for milling are as follows: the liquid flow rate is 10 kg/min-15 kg/min, the atomizing medium is nitrogen, the atomizing airflow pressure is 10 MPa-15 MPa, and the diameter of an atomizing nozzle of the atomizing rapid condensing device is 5 mm-6 mm; after the atomization is finished, completely cooling the powder, and screening in a nitrogen protective atmosphere to obtain Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder with the particle size of 10-20 microns;
(2) ball milling: putting the raw materials prepared in the step (1) into a vacuum ball milling tank, weighing anhydrous ethanol with the weight accounting for 30-40% of the weight of the raw materials prepared in the step (1) and paraffin with the weight accounting for 10-20% of the weight of the raw materials prepared in the step (1) to mix to serve as a medium, wherein the ball-material ratio is 10: 1, in order to prevent powder from being oxidized in the ball milling process, argon is used as protective gas, ball milling is carried out for 48 hours, and vacuum drying and sieving are carried out;
(3) molding: putting the ceramic powder obtained in the step (2) into a die, performing compression molding by adopting a two-way press, pressurizing two ends, pressurizing for two times, heating to 800 ℃ at a heating rate of 30-40 ℃/min in a first pressurizing state, and keeping for 2-3 hours at 20MPa, heating to 1200 ℃ at a heating rate of 20-30 ℃/min in a second pressurizing state, and keeping for 2-3 hours at 20MPa, completing the dewaxing step at this stage, finishing a pressed blank after molding, and checking the appearance quality;
(4) vacuum hot-pressing sintering: putting the pressed compact obtained in the step (3) into a vacuum hot-pressing sintering furnace, keeping the sintering temperature at 1550 ℃ and the sintering pressure at 30MPa for 1 hour, and filling argon gas 20min before the final sintering is completed until the sintering is completed, thus obtaining a metal ceramic sample; through detection, the hardness of the final ceramic material is HRA85-90, the bending strength is 1900-2200MPa, and the fracture toughness is 10-11 MPa.m1/2The coefficient of thermal conductivity is 88-92W/(m.K), and the coefficient of linear expansion is 4 multiplied by 10-6/℃-4.4×10-6/℃。
Comparative example 5
A high-strength high-hardness ceramic material comprises the following components in percentage by weight: 50-52 parts of TiC, 13-14 parts of TiN, 3C21-2 parts of Cr, 7-8 parts of WC, 5-6 parts of HfC, 3-4 parts of TaC, 3-2 parts of La2O31-2 parts of Co, 5-6 parts of Mn, 5-6 parts of Ni, 4-5 parts of Fe, and the balance of Al and inevitable impurities, wherein the ratio of TiC to TiN is 3.6-4; the preparation method comprises the following specific steps:
(1) preparing the following components: mixing according to target components, wherein the size of TiC and TiN is 300-800 nm, the size of Cr3C2, WC, HfC, TaC and La2O3 is 1-3 microns, and the size of Co, Mn, Ni, Fe and Al is 10-20 microns in the form of elemental powder;
(2) ball milling: putting the raw materials prepared in the step (1) into a vacuum ball milling tank, weighing anhydrous ethanol with the weight accounting for 30-40% of the weight of the raw materials prepared in the step (1) and paraffin with the weight accounting for 10-20% of the weight of the raw materials prepared in the step (1) to mix to serve as a medium, wherein the ball-material ratio is 10: 1, in order to prevent powder from being oxidized in the ball milling process, argon is used as protective gas, ball milling is carried out for 48 hours, and vacuum drying and sieving are carried out;
(3) molding: putting the ceramic powder obtained in the step (2) into a die, performing compression molding by adopting a two-way press, pressurizing two ends, pressurizing for two times, heating the pressurized ceramic powder to 1000 ℃ at a heating rate of 20-30 ℃/min, and keeping the heated ceramic powder at 20MPa for 2-3 hours, completing the dewaxing step at the stage, finishing a pressed blank after molding, and checking the appearance quality;
(4) vacuum hot-pressing sintering: putting the pressed compact obtained in the step (3) into a vacuum hot-pressing sintering furnace, keeping the sintering temperature at 1480 ℃ and the sintering pressure at 30MPa for 1.3 hours, and filling argon gas 20min before the final sintering is completed until the sintering is completed to obtain a metal ceramic sample;
through detection, the hardness of the final ceramic material is HRA 88-95, the bending strength is 2000-2300MPa, and the fracture toughness is 10.5-11.8 MPa.m1/2The coefficient of thermal conductivity is 84-92W/(m.K), and the coefficient of linear expansion is 3.5 multiplied by 10-6/℃-4.5×10-6/℃。
The terminology used herein is for the purpose of description and illustration, rather than of limitation. As the present invention may be embodied in several forms without departing from the spirit or essential characteristics thereof, it should also be understood that the above-described embodiments are not limited by any of the details of the foregoing description, but rather should be construed broadly within its spirit and scope as defined in the appended claims, and therefore all changes and modifications that fall within the meets and bounds of the claims, or equivalences of such meets and bounds are therefore intended to be embraced by the appended claims.
Claims (6)
1. A high-strength high-hardness ceramic material comprises the following components in percentage by weight: 50-52 parts of TiC, 13-14 parts of TiN and Cr3C21-2、WC 7-8、HfC 5-6、TaC 3-4、La2O31-2 parts of titanium, 5-6 parts of Co, 3-4 parts of Mn, 5-6 parts of Ni, 4-5 parts of Fe, and the balance of Al and inevitable impurities, wherein the ratio of TiC/TiN is 3.6-4; the preparation method comprises the following specific steps:
(1) preparing the following components: the materials are mixed according to target components, wherein the size of TiC and TiN is 300-800 nm, and the size of Cr is3C2、WC、HfC、TaC、La2O3The size of the alloy powder is 1-3 microns, wherein Co, Mn, Ni, Fe and Al are added in the form of Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder, the size of the alloy powder is 10-20 microns, the production of the Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder comprises the steps of firstly, selecting raw materials with the purity of more than or equal to 99.9% for smelting, removing impurities to obtain an alloy solution with high purity, and then carrying out atomization powder preparation, wherein the specific technological parameters of the atomization powder preparation are as follows: the liquid flow rate is 10 kg/min-15 kg/min, the atomizing medium is nitrogen, the atomizing airflow pressure is 10 MPa-15 MPa, and the diameter of an atomizing nozzle of the atomizing rapid condensing device is 5 mm-6 mm; after the atomization is finished, completely cooling the powder, and screening in a nitrogen protective atmosphere to obtain Co-Mn-Ni-Fe-Al quinary high-entropy alloy powder with the particle size of 10-20 microns;
(2) ball milling: putting the raw materials prepared in the step (1) into a vacuum ball milling tank, weighing anhydrous ethanol with the weight accounting for 30-40% of the weight of the raw materials prepared in the step (1) and paraffin with the weight accounting for 10-20% of the weight of the raw materials prepared in the step (1) to mix to serve as a medium, wherein the ball-material ratio is 10: 1, in order to prevent powder from being oxidized in the ball milling process, argon is used as protective gas, ball milling is carried out for 48 hours, and vacuum drying and sieving are carried out;
(3) molding: putting the ceramic powder obtained in the step (2) into a die, performing compression molding by adopting a two-way press, pressurizing two ends, pressurizing for two times, heating to 800 ℃ at a heating rate of 30-40 ℃/min in a first pressurizing state, and keeping for 2-3 hours at 20MPa, heating to 1200 ℃ at a heating rate of 20-30 ℃/min in a second pressurizing state, and keeping for 2-3 hours at 20MPa, completing the dewaxing step at this stage, finishing a pressed blank after molding, and checking the appearance quality;
(4) vacuum hot-pressing sintering: putting the pressed compact obtained in the step (3) into a vacuum hot-pressing sintering furnace, keeping the sintering temperature at 1550 ℃ and the sintering pressure at 30MPa for 1 hour, and filling argon gas 20min before the final sintering is completed until the sintering is completed, thus obtaining a metal ceramic sample; through detection, the hardness of the final ceramic material is HRA94-100, the bending strength is 2400-2600MPa, and the fracture toughness is 12-13 MPa.m1/2The coefficient of thermal conductivity is 95-105W/(m.K), and the coefficient of linear expansion is 2.8 multiplied by 10-6/℃-3.8×10-6/℃。
2. The high-strength high-hardness ceramic material according to claim 1, characterized in that: ball milling: putting the raw materials prepared in the step (1) into a vacuum ball milling tank, weighing anhydrous ethanol accounting for 35% of the weight of the raw materials prepared in the step (1), weighing paraffin accounting for 15% of the weight of the raw materials prepared in the step (1), mixing the anhydrous ethanol and the paraffin as a medium, wherein the ball-material ratio is 10: 1, ball-milling for 48 hours by taking argon as protective gas in order to avoid powder from being oxidized in the ball milling process, and carrying out vacuum drying and sieving.
3. The high-strength high-hardness ceramic material according to claim 1, characterized in that: step (3) forming: and (3) putting the ceramic powder obtained in the step (2) into a die, performing compression molding by adopting a two-way press, pressurizing two ends, pressurizing for two times, heating to 800 ℃ at a heating rate of 35 ℃/min in the first pressurizing state, keeping the temperature for 2.5 hours under 20MPa, heating to 1200 ℃ at a heating rate of 25 ℃/min in the second pressurizing state, keeping the temperature for 2.5 hours under 20MPa, completing the dewaxing step at this stage, trimming the pressed blank after molding, and checking the appearance quality.
4. The high-strength high-hardness ceramic material according to claim 1, characterized in that: the weight percentages of the components are as follows: TiC50, TiN 13, Cr3C21、WC 7、HfC 5、TaC 3、La2O31. Co 5, Mn 3, Ni 5, Fe 4, the balance being Al and unavoidable impurities, the TiC/TiN ratio being 3.85.
5. The high-strength high-hardness ceramic material according to claim 1, characterized in that: the weight percentages of the components are as follows: TiC 50.5, TiN 13.5, Cr3C21.5、WC 7.5、HfC 5、TaC 3、La2O31. Co 5, Mn 3, Ni 5, Fe 4, the balance being Al and unavoidable impurities, the TiC/TiN ratio being 3.74.
6. The high-strength high-hardness ceramic material according to claim 1, characterized in that: the weight percentages of the components are as follows: TiC 51, TiN 14, Cr3C21、WC 7、HfC 5、TaC 3、La2O31. Co 5, Mn 3, Ni 5, Fe 4, the balance being Al and unavoidable impurities, the TiC/TiN ratio being 3.64.
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Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101255520A (en) * | 2008-04-07 | 2008-09-03 | 株洲钻石切削刀具股份有限公司 | Nano WC-Co composite powder modified Ti(CN) based metal ceramic and preparation thereof |
| CN101302595A (en) * | 2008-07-08 | 2008-11-12 | 湖南科技大学 | High-wear resistant Ti (C, N)-base ceramet tool bit and preparation thereof |
| CN103556086A (en) * | 2013-10-21 | 2014-02-05 | 西安科技大学 | Preparation method of anti-high temperature wear-resistant Ti(C, N) metal ceramic composite material |
| CN103589929A (en) * | 2013-10-17 | 2014-02-19 | 株洲钻石切削刀具股份有限公司 | Metal ceramic alloy preparation method and product thereof |
| CN103710603A (en) * | 2013-12-27 | 2014-04-09 | 华中科技大学 | Non-magnetic Ti(C, N) base cermet with gradient structure and preparation method thereof |
| CN103774022A (en) * | 2012-10-19 | 2014-05-07 | 郑汉东 | Ti(C,N)-based metal ceramic and its application |
| CN107385303A (en) * | 2016-01-29 | 2017-11-24 | 重庆文理学院 | A kind of high fine and close and high tenacity metal material and preparation method thereof |
| CN107794430A (en) * | 2017-10-24 | 2018-03-13 | 株洲金锐美新材料有限公司 | A kind of ultra-fine crystal particle cermet and preparation method thereof |
| CN107881389A (en) * | 2017-11-06 | 2018-04-06 | 株洲科力特新材料有限公司 | Ti (C, N) based ceramic metals and for preparing its preparation method |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0726173B2 (en) * | 1991-02-13 | 1995-03-22 | 東芝タンガロイ株式会社 | High toughness cermet and method for producing the same |
| CN1172168A (en) * | 1996-07-30 | 1998-02-04 | 大韩重石株式会社 | Ultra-hard alloy for wrist watch and decoration |
| JPH1046282A (en) * | 1996-07-31 | 1998-02-17 | Korea Tungsten Co Ltd | Cemented carbide for wristwatch and ornament |
| CN106119655A (en) * | 2016-08-11 | 2016-11-16 | 宁波市鄞州亚大汽车管件有限公司 | A kind of oil pipe plug |
-
2018
- 2018-06-11 CN CN201810595951.6A patent/CN108642361B/en active Active
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101255520A (en) * | 2008-04-07 | 2008-09-03 | 株洲钻石切削刀具股份有限公司 | Nano WC-Co composite powder modified Ti(CN) based metal ceramic and preparation thereof |
| CN101302595A (en) * | 2008-07-08 | 2008-11-12 | 湖南科技大学 | High-wear resistant Ti (C, N)-base ceramet tool bit and preparation thereof |
| CN103774022A (en) * | 2012-10-19 | 2014-05-07 | 郑汉东 | Ti(C,N)-based metal ceramic and its application |
| CN103589929A (en) * | 2013-10-17 | 2014-02-19 | 株洲钻石切削刀具股份有限公司 | Metal ceramic alloy preparation method and product thereof |
| CN103556086A (en) * | 2013-10-21 | 2014-02-05 | 西安科技大学 | Preparation method of anti-high temperature wear-resistant Ti(C, N) metal ceramic composite material |
| CN103710603A (en) * | 2013-12-27 | 2014-04-09 | 华中科技大学 | Non-magnetic Ti(C, N) base cermet with gradient structure and preparation method thereof |
| CN107385303A (en) * | 2016-01-29 | 2017-11-24 | 重庆文理学院 | A kind of high fine and close and high tenacity metal material and preparation method thereof |
| CN107794430A (en) * | 2017-10-24 | 2018-03-13 | 株洲金锐美新材料有限公司 | A kind of ultra-fine crystal particle cermet and preparation method thereof |
| CN107881389A (en) * | 2017-11-06 | 2018-04-06 | 株洲科力特新材料有限公司 | Ti (C, N) based ceramic metals and for preparing its preparation method |
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