CN113201676B - Preparation method of high-temperature oxidation-resistant low-bonding-phase metal ceramic - Google Patents
Preparation method of high-temperature oxidation-resistant low-bonding-phase metal ceramic Download PDFInfo
- Publication number
- CN113201676B CN113201676B CN202110357878.0A CN202110357878A CN113201676B CN 113201676 B CN113201676 B CN 113201676B CN 202110357878 A CN202110357878 A CN 202110357878A CN 113201676 B CN113201676 B CN 113201676B
- Authority
- CN
- China
- Prior art keywords
- partial pressure
- pressure sintering
- temperature
- powder
- bonding
- 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
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/04—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbonitrides
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- 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
- B22F3/16—Both compacting and sintering in successive or repeated steps
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—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
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
-
- 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
- B22F2302/00—Metal Compound, non-Metallic compound or non-metal composition of the powder or its coating
- B22F2302/35—Complex boride, carbide, carbonitride, nitride, oxide or oxynitride
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention discloses a preparation method of a high-temperature oxidation resistant low-bonding-phase Ti (C, N) -based composite metal ceramic, belonging to the technical field of metal ceramic materials and powder metallurgy. The preparation method of the Ti (C, N) -based composite metal ceramic comprises the steps of raw material proportioning, wet grinding, material drying, pressing, partial pressure sintering and the like, and Mo is adjusted2The contents of C and Co form a Ti (C, N) -based cermet with higher oxidation resistance by a partial pressure sintering mode. The invention relates to a high-temperature oxidation-resistant low-bonding-phase Ti (C, N) -based composite metal ceramic which comprises the following components in percentage by weight: ti (C) 0.5 N 0.5):35～65％，WC:15～35％，Mo210-15% of C, 10-15% of Co, 10-20% of Ni and 0.8-1.0% of graphite. The Ti (C, N) -based composite metal ceramic prepared by the method has better compactness. Meanwhile, the high-temperature oxidation resistance is excellent, and the high-temperature oxidation resistance has positive significance in the aspect of semi-finishing cutting tool materials of special steel.
Description
Technical Field
The invention belongs to the preparation of Ti (C, N) -based metal ceramic materials, and particularly relates to a high-temperature oxidation-resistant low-bonding-phase Ti (C, N) -based metal ceramic and a preparation method thereof.
Background
In recent years, with the improvement of machine tool performance, the cutting speed is faster and the cutting temperature is increased, and the temperature near the cutting edge can reach about 1000 ℃. Under the condition, the cutter material is very easy to oxidize, so that the tissue change is caused, the performance of the cutter is reduced, even the cutting edge of the cutter is broken and loses efficacy, and the high-speed cutting requires that the cutting cutter material has good high-temperature oxidation resistance and high-temperature mechanical property. The existing hard alloy tool is difficult to meet the requirements of working under the conditions of higher cutting speed and larger feed amount. Ti (C, N) -based cermet has excellent high temperature stability, and is gradually replacing hard alloy for high speed cutting. Therefore, the high temperature oxidation resistance of Ti (C, N) -based cermet has become an important factor in determining its commercial application.
The Ti (C, N) -based cermet is a functional structural material with intermetallic compound as hard phase and Ni and Co as binding phase. The excellent mechanical property of the alloy makes the alloy more prominent in comparison of hard alloys, and the alloy has high hardness, high bending strength and good wear resistance in the aspect of mechanical property. The high-temperature characteristics have high oxidation resistance and heat resistance; but also is not easy to generate accumulated chips when used as a cutter for cutting; the cermet material is superior to hard alloy in comprehensive performance.
In recent years, cermet, especially Ti (C, N) -based cermet, has made a significant breakthrough in cutting tool materials, and has become the most promising tool material to replace WC — Co. The excellent wear resistance and high-temperature stability not only prolong the service life of the cutter, but also achieve the effect of improving the quality of the cutting surface of the cutter. The cermet with low binder phase (less than or equal to 20%) has high hardness, high strength and high fracture toughness, and may be used widely in turning tool and milling cutter. However, the sintering process of the cermet also plays a crucial role in its overall mechanical properties.
Therefore, research on sintering atmosphere is more important, partial pressure sintering of Ti (C, N) -based cermet is mainly carried out in argon atmosphere sintering at the solid phase sintering stage, and a fast cooling mode is adopted during cooling, so that the method is beneficial to generation of a core-ring phase, and has certain positive significance on control of mechanical property stability. This patent carries out the atmosphere sintering experiment at the solid phase sintering stage that the alloy has not accomplished densification, adopts vacuum, argon atmosphere to experiment respectively at the solid phase sintering stage, and the nitrogen atmosphere is built with nitrogen partial pressure sintering in the liquid phase stage for restraining the volatilization of nitrogen, improves its compactness, has certain positive meaning to Ti (C, N) base cermet quality stability control, has still studied the influence of the ratio proportion of Mo element and Co to its oxidation resistance simultaneously.
Disclosure of Invention
The invention provides a pressure-division sintered Ti (C, N) -based metal ceramic, and also provides a raw material proportion and a preparation method thereof, aiming at ensuring that the Ti (C, N) -based metal ceramic not only has good mechanical property, but also has excellent oxidation resistance.
The invention aims to overcome the defects of the existing low-fracture toughness metal ceramic through partial pressure sintering, and provides a preparation method of a high-temperature oxidation-resistant low-bonding-phase Ti (C, N) -based composite metal ceramic.
In order to achieve the above purpose, the invention provides a preparation method of a high-temperature oxidation-resistant low-bonding-phase Ti (C, N) -based composite cermet, which comprises the following steps:
(1) powder preparation: weighing Ti (C)0.5N0.5) Powder, WC powder, Mo2Ball-milling C powder, Co powder, Ni powder, graphite and hard alloy balls in absolute ethyl alcohol to obtain slurry, drying, and sieving by at least 80 meshes to obtain powder; the weight percentage of the raw materials is as follows: ti (C)0.5N0.5):35～65％，WC:15～35％，Mo210-15% of C, 10-15% of Co, 10-20% of Ni and 0.8-1.0% of graphite. Adding hard alloy balls according to a material ball ratio of 1: 5-1: 7 in the step (1), wherein the ratio of the large hard alloy balls to the small hard alloy balls is 1: 1, wet grinding the mixed material on a planetary ball mill at a rotating speed of 220r/min and setting forward and reverse rotation, wherein the interval time between the forward and reverse rotation is 25min, and wet grinding the mixed material on a ball mill for 24-36 h.
(2) Pressing: putting the dried powder into a pressing blank, and pressing and forming; in the process of press forming, firstly, the pressure is kept at 2000-2800N, and then the pressure is kept at 200-220 MPa for 45-60 s.
(3) Partial pressure sintering: and (3) placing the pressed compact in a pressure sintering furnace for partial pressure sintering, wherein the vacuum degree is less than 5Pa, heating the furnace from room temperature to 1200 ℃, then heating to 1200-1260 ℃ for low argon partial pressure sintering, then heating to 1260-1350 ℃ for vacuum or low argon partial pressure sintering, further heating to 1350-1490 ℃ for nitrogen partial pressure sintering, heating to 1490 ℃ for nitrogen partial pressure sintering, preserving heat for 1-2 h, and cooling to room temperature to obtain the high-temperature oxidation-resistant low-bonding-phase cermet.
The heating rate of each stage in the step (3) is as follows: 3-8 ℃/min at the normal temperature of 1200 ℃, 1-3 ℃/min at the temperature of 1200-1260 ℃, 1-3 ℃/min at the temperature of 1260-1350 ℃ and 2-3 ℃/min at the temperature of 1350-1490 ℃. Wherein, when the low argon partial pressure sintering is carried out at the stage of 1200-1260 ℃ and 1260-1350 ℃, the pressure is 300-400 mbar. And when partial pressure sintering of nitrogen is carried out at 1350-1490 ℃, the pressure is 15-20 mbar; and (3) sintering at 1490 ℃ under the condition of nitrogen partial pressure, wherein the pressure is 15-20 mbar.
In the step (3), in the process of rapidly cooling to room temperature, cooling to 1350 ℃ at a speed of 8-10 ℃/min, and cooling to 1350 ℃ at a speed of 5-7 ℃/min to 1000 ℃; cooling to room temperature at a rate of 1-2 deg.C/min.
In the step (5), the pressure-dividing sintering process is mainly characterized in that the cermet material gradually becomes compact in a longer time through the added inert gas and given energy, and meanwhile, a higher vacuum degree can be kept through continuous ventilation in the pressure-dividing process, so that gas in tiny pores in the material can be discharged, and the effect of controlling crystal growth is achieved, and the Ti (C, N) -based composite cermet material with good compactness is further obtained.
Compared with the prior art, the technical scheme provided by the invention has the following remarkable effects:
(1) the preparation method of the high-temperature oxidation-resistant low-bonding-phase Ti (C, N) -based composite cermet material can prepare the Ti (C, N) -based composite cermet material with uniform structure and good compactness; scanning Electron Microscopy (SEM) analysis and porosity evaluation are carried out on the material, and the material obtained by the invention can be found to have a Ti (C, N) -based ring core structure, is complete and has uniform structural distribution.
(2) According to the preparation method of the high-temperature oxidation-resistant low-bonding-phase Ti (C, N) -based composite cermet, the prepared material has HV hardness of 1337-1564 and fracture toughness of 9.7-11.7 MPa.m1/2The bending strength reaches 1672-1864 MPa, and the high strength and toughness can be seen. (ii) a
(3) Meanwhile, the cermet with stronger high-temperature oxidation resistance can be prepared by adopting a slow pressure-dividing sintering mode.
Drawings
Fig. 1 is a Scanning Electron Microscope (SEM) backscattered electron imaging (SEM) picture of Ti (C, N) -based cermet microstructure No. 10.
FIG. 2 is a gold phase diagram of a sample of example 2, wherein (a) is reference numeral 1, (b) is reference numeral 3, (c) is reference numeral 5, (d) is reference numeral 9, and (e) is reference numeral 11.
Fig. 3 is a Scanning Electron Microscope (SEM) photograph of the Ti (C, N) -based composite cermet material prepared in example 1 of the present invention, wherein (a) is number 1, (b) is number 3, (C) is number 5, (d) is number 9, and (e) is number 11.
Detailed Description
For further understanding of the present invention, the present invention is further described below with reference to examples, which are provided for illustration only and are not intended to limit the scope of the present invention.
Example 1
Weighing raw material powder according to the components in the proportion in the table to prepare Ti (C, N) -based metal ceramics with different components, mixing the Ti (C, N) -based metal ceramics in a ball milling tank, and adding 500g of hard alloy balls and 72ml of absolute ethyl alcohol; ball-milling for 36h on a pot-type ball mill at the rotation speed of 220r/min, sieving the mixed material slurry with a 325-mesh sieve, pouring out, drying in a 75-DEG C oven, and sieving the dried powder with a 60-mesh sieve for later use. And (3) taking the proper amount of powder according to the shape of a cutter, placing the powder into an alloy grinding tool, performing dry pressing at 100MPa, then placing the powder into a vacuum sintering furnace for sintering under the sintering condition shown in Table II, and then cooling, wherein the temperature is reduced from 1490 ℃ to 1350 ℃ at the cooling speed of 10 ℃/min, is reduced from 1350 ℃ to 1000 ℃ at the cooling speed of 7 ℃/min, and is reduced from 1000 ℃ to room temperature at the cooling speed of 1 ℃/min, so that the high-temperature oxidation-resistant low-bonding-phase metal ceramic is obtained. The solid-phase sintering and liquid-phase sintering processes are shown in table two:
TABLE-Ti (C, N) -based cermet compositions
Epi-di Ti (C, N) -based metal ceramic partial pressure sintering process
The Transverse Rupture Strength (TRS) of a sintered sample is determined according to GB/T3851-1983 hard alloy transverse rupture strength determination method, the Vickers Hardness (HV) is determined according to GB7997-1987 hard alloy Vickers hardness test method, and the rupture toughness (K)1C) The determination is referred to BS ISO 28079-2009 Hardmetals-Palmqvist Toughress test. And (3) carrying out mechanical property test on a sample prepared by partial pressure sintering: as shown in the third table
TABLE TRI Ti (C, N) -based cermet mechanical Properties and volume fraction of binder phase in the microstructure
Mo can be seen from the mechanical properties of numbers 1, 5 and 14 in Table III2The addition of C and Co has an effect of improving fracture toughness; from the numbers 3, 8, 9, 10 and 11 in the third table, it can be seen that the fracture toughness is greatly improved by partial pressure sintering, wherein the properties of the numbers 10 and 11 are more excellent, and it is seen that the nitrogen atmosphere sintering in the liquid phase stage is beneficial to improving the mechanical properties. In addition, the improvement of the mechanical property by matching with the nitrogen partial pressure in the liquid phase stage is more obvious, and the partial pressure sintering has great guiding significance for improving the mechanical property of the metal ceramic. It can be seen from the graphs (d) and (e) in fig. 3 that the partial pressure sintering makes the microstructure more uniform and the ring phase more complete, and provides a strong evidence for the improvement of mechanical properties. FIG. 1 is a Scanning Electron Microscope (SEM) back-scattered electron image of the above Ti (C, N) -based cermet microstructure of accession No. 10, in which several structures of a black core phase, an inner ring phase, an outer ring phase, a white core phase, a ring phase and a binder phase are observed. The volume fraction of the binder phase is basically 12-15% and the volume fraction of the binder phase is 25% of the common volume fractionFor the above high binder phase, the volume fraction of the binder phase is low.
Example 2
And selecting samples numbered 1, 3, 5, 9 and 11 in the fourth table to perform a high-temperature oxidation experiment, measuring the density of the samples by using the Archimedes principle, and photographing the polished surface under a microscope under a 40-time lens for evaluating the porosity. The specific experimental steps are as follows: polishing the surface of a sample, placing the polished sample on a platinum wire mesh, placing the sample in a resistance furnace for high-temperature oxidation at 1000 ℃, oxidizing for 10 hours, weighing the sample on an analytical balance with the precision of 0.0001g after the sample is cooled after the oxidation is finished, simultaneously recording the measurement, and measuring the oxidation weight gain of the sample after the experiment is finished, wherein the measurement is shown in the following table four:
table four density and oxidative weight gain of samples
After the sample is sintered, the sample is roughly ground on a grinding wheel and finely ground on a diamond grinding disc, and then polished, and the porosity of the sample is observed under an optical microscope according to the ISO4505 standard. The samples with high porosity can cause crack sources to be formed during the fracture of the metal ceramic material, and the bending strength and the fracture toughness of the metal ceramic are reduced. From the fourth table and the metallographic image (b) in fig. 2, it can be seen that the addition of Mo and Co improves the porosity to some extent, and also plays a role in oxidation resistance; as can be seen from Table IV and the metallographic photographs (d) (e), the samples prepared by partial pressure sintering had smooth surfaces and few pores, and it was found that the density was greatly improved and the oxidation resistance was also remarkably excellent.
The invention and its embodiments have been described above schematically, without limitation, and the actual method is not limited thereto. Although the present invention has been described in detail and with reference to specific embodiments thereof, it will be apparent to one skilled in the art that various changes and modifications can be made therein without departing from the spirit and scope thereof.
Claims (3)
1. The preparation method of the high-temperature oxidation-resistant low-bonding-phase cermet is characterized by comprising the following steps of:
(1) powder preparation: weighing Ti (C)0.5N0.5) Powder, WC powder, Mo2Ball-milling C powder, Co powder, Ni powder, graphite and hard alloy balls in absolute ethyl alcohol to obtain slurry, drying, and sieving by at least 80 meshes to obtain powder; the weight percentage of each raw material is as follows: ti (C)0.5N0.5):46%，WC:19%，Mo212 percent of C, 12 percent of Co, 10 percent of Ni and 1.0 percent of graphite;
(2) pressing: putting the dried powder into a pressing blank, and pressing and forming;
(3) and (3) vacuum sintering: placing the pressed compact in a pressure sintering furnace for partial pressure sintering, wherein the vacuum degree is less than 5Pa, heating the furnace temperature from room temperature to 1200 ℃ at the speed of 3-8 ℃/min, then heating to 1200-1260 ℃ at the speed of 1 ℃/min for low argon partial pressure sintering, heating to 1260-1350 ℃ at the speed of 1 ℃/min for low argon partial pressure sintering, heating to 1350-;
when low argon partial pressure sintering is carried out at the stage of 1200-1260 ℃ and 1260-1350 ℃, the pressure is 350mbar, the temperature is further increased to 1350-1490 ℃ for nitrogen partial pressure sintering, the nitrogen partial pressure sintering is carried out at 1490 ℃, and when the nitrogen partial pressure sintering is carried out at 1350-1490 ℃, the pressure is 15 mbar; and (3) performing nitrogen partial pressure sintering at 1490 ℃, keeping the temperature for 1h, and cooling to room temperature to obtain the high-temperature oxidation-resistant low-bonding-phase cermet.
2. The method for preparing the high-temperature oxidation-resistant low-bonding-phase cermet according to claim 1, wherein the cermet is prepared by pressing at a pre-pressure of 2000-2800N and then at a pressure of 200-220 MPa for 45-60 s.
3. The method for preparing the high-temperature oxidation-resistant low-bonding-phase cermet according to claim 1, wherein in the step (3), the temperature is reduced to 1350 ℃ at a rate of 8-10 ℃/min and is reduced to 1000 ℃ at a rate of 5-7 ℃/min during the cooling to the room temperature; cooling to room temperature at 1-2 deg.C/min.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110357878.0A CN113201676B (en) | 2021-04-01 | 2021-04-01 | Preparation method of high-temperature oxidation-resistant low-bonding-phase metal ceramic |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110357878.0A CN113201676B (en) | 2021-04-01 | 2021-04-01 | Preparation method of high-temperature oxidation-resistant low-bonding-phase metal ceramic |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN113201676A CN113201676A (en) | 2021-08-03 |
| CN113201676B true CN113201676B (en) | 2022-06-03 |
Family
ID=77026049
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202110357878.0A Active CN113201676B (en) | 2021-04-01 | 2021-04-01 | Preparation method of high-temperature oxidation-resistant low-bonding-phase metal ceramic |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN113201676B (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115418542B (en) * | 2022-07-12 | 2023-05-23 | 杭州巨星科技股份有限公司 | Nano modified metal ceramic cutter material and preparation method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0374358A1 (en) * | 1988-11-29 | 1990-06-27 | Toshiba Tungaloy Co. Ltd. | High strength nitrogen-containing cermet and process for preparation thereof |
| 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 |
| CN107099722A (en) * | 2017-05-02 | 2017-08-29 | 四川大学 | Surface self-lubricating Ti (C, N) based ceramic metal preparation method based on carbon diffusion |
| CN107523710A (en) * | 2017-08-24 | 2017-12-29 | 台州学院 | A kind of whisker modified Ti (C, N) based composite metal ceramic preparation of resistance to high temperature oxidation |
| CN109182874A (en) * | 2018-10-24 | 2019-01-11 | 四川大学 | A kind of preparation method of Ti (C, the N) based ceramic metal for adding graphene |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103820692B (en) * | 2014-03-07 | 2015-03-04 | 华中科技大学 | Ti (C, N) base cermet using Ni3Al and Ni as binder and its prepn |
-
2021
- 2021-04-01 CN CN202110357878.0A patent/CN113201676B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0374358A1 (en) * | 1988-11-29 | 1990-06-27 | Toshiba Tungaloy Co. Ltd. | High strength nitrogen-containing cermet and process for preparation thereof |
| US4985070A (en) * | 1988-11-29 | 1991-01-15 | Toshiba Tungaloy Co., Ltd. | High strength nitrogen-containing cermet and process for preparation thereof |
| 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 |
| CN107099722A (en) * | 2017-05-02 | 2017-08-29 | 四川大学 | Surface self-lubricating Ti (C, N) based ceramic metal preparation method based on carbon diffusion |
| CN107523710A (en) * | 2017-08-24 | 2017-12-29 | 台州学院 | A kind of whisker modified Ti (C, N) based composite metal ceramic preparation of resistance to high temperature oxidation |
| CN109182874A (en) * | 2018-10-24 | 2019-01-11 | 四川大学 | A kind of preparation method of Ti (C, the N) based ceramic metal for adding graphene |
Non-Patent Citations (1)
| Title |
|---|
| 《高韧性Ti(C,N)基金属陶瓷制备及组织结构特征研究》;龚琳;《万方学位论文》;20191219;第8、10-11、14页 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN113201676A (en) | 2021-08-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109371307A (en) | It is a kind of using high-entropy alloy powder as the preparation method of the WC base cemented carbide of binder | |
| CN108060322A (en) | The preparation method of hard high-entropy alloy composite material | |
| CN113234950B (en) | Preparation method of Ti (C, N) -based metal ceramic | |
| CN102828096B (en) | Metal ceramic cutting tool material and preparation method thereof | |
| CN113201676B (en) | Preparation method of high-temperature oxidation-resistant low-bonding-phase metal ceramic | |
| US8173561B2 (en) | Inert high hardness material for tool lens production in imaging applications | |
| CN114774754A (en) | Novel FeCrMnVSix high-entropy alloy coating and preparation method thereof | |
| CN101695822A (en) | Formula of diamond super-thin cutting disc for cutting of magnetic materials and production technology thereof | |
| JP6922110B1 (en) | Crushing / stirring / mixing / kneading machine parts | |
| JP4713119B2 (en) | Cutting tool insert and manufacturing method thereof | |
| CN101758465A (en) | Prescription and production process of diamond ultrathin slice for sapphire and crystal cutting | |
| JP2005281084A (en) | Sintered compact and manufacturing method therefor | |
| JP6049978B1 (en) | Oxidation-resistant low-binder hard alloy with a large thermal expansion coefficient or lens mold made of this material | |
| CN114318163B (en) | Superfine multi-element prealloy powder for diamond tool and preparation method thereof | |
| CN116727671A (en) | Pulverizing, stirring, mixing and pugging machine component | |
| CN101758212A (en) | Prescription and production process of diamond ultrathin slice for hard alloy cutting | |
| CN101758442A (en) | Formula of diamond ultrathin blade for cutting QFN baseplate and manufacturing technique thereof | |
| CN101698290A (en) | Diamond ultrathin section formula used for sectioning ceramics and production process | |
| JP6888294B2 (en) | Manufacturing method of Cu-Ga alloy sputtering target and Cu-Ga alloy sputtering target | |
| CN101758443A (en) | Prescription and production process of diamond ultrathin slice for ceramic substrate cutting | |
| JP2009209022A (en) | WC-SiC-Mo2C-BASED SINTERED BODY AND ITS MANUFACTURING METHOD | |
| CN115786758B (en) | Mo (molybdenum)2FeB2Preparation method of-TiN-based composite material | |
| CN109763054A (en) | A kind of multi-element mixed Cutanit and its preparation method and application | |
| CN113278848B (en) | SPS sintered particle reinforced Ti-Al-Sn-Zr series high-temperature-resistant titanium-based composite material and preparation method thereof | |
| CN101758217A (en) | Formula and production process of diamond ultrathin slice for crystal glass cutting |
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 |