CN103774022B - Ti (C, N) based ceramic metal and application thereof - Google Patents
Ti (C, N) based ceramic metal and application thereof Download PDFInfo
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Abstract
A kind of Ti (C, N) based ceramic metal and application thereof, being made up of ceramic phase and Binder Phase, does is the atomic percent of each moiety Ti? 48.16 ~ 54.29%, Mo? 7.1 ~ 11.02%, W? 3.52 ~ 6.31%, Ni? 15.56 ~ 19.88%, Y? 0.47 ~ 0.69%, Al? 1.53 ~ 2.43%, C? 9.37 ~ 12.54%, N3.98 ~ 4.99%.In sintering metal preparation, add rare earth element y and AlN, by rare earth element y cleaning action is served to phase interface, the bonding strength of phase interface is enhanced, improves Fracture of Material; And the AlN added makes the Binder Phase of Ti (C, N) based ceramic metal be strengthened, thus improve ceramic-metallic hardness and intensity.The cutting tool be made up of the sintering metal in the present invention has low density, high rigidity, little to the frictional coefficient of steel, during cutting bonding abrasion and diffusive wear little, the advantage that red hardness is good.
Description
Technical field
The present invention relates to the technical field of alloy material, is that one has low density and high rigidity specifically, and Ti (C, the N) based ceramic metal of low production cost and application thereof.
Background technology
Ceramic-metallicly be developed so far main experience three processes: one, TiC-Ni based ceramic metal has been invented by Germany nineteen twenty-nine, although have excellent mechanical behavior under high temperature and low-density feature, but because the wettability of Ni to TiC particle is poor, the easy agglomeration of TiC particle, the strength of materials and toughness poor; Two, TiC-Mo has invented in Ford of the U.S. in 1956
2c-Ni sintering metal, sintering metal intensity is improved; Three, Vienna University of Technology in 1971 has found at TiC-Mo
2tiN is added in C-Ni sintering metal, can refinement hard-phase particles further, high temperature creep-resisting ability, red hardness, room temperature obdurability is all improved.
But along with the introducing of TiN, produce denitrogenation phenomenon in sintering process, increase the porosity of material, the total effect that denitrogenation causes reduces sinterability and intensity.
In the last few years, scientific research personnel has carried out large quantifier elimination, by to material preparation in composition design, the research of reaction mechanism, the optimization of manufacture method and complete processing, wish hardness and the bending strength that can improve material simultaneously, its over-all properties is enable to meet industrial demand, but, by use range and the ratio of domestic cermet product, its industry development is also in initial stage, and performance also needs to improve raising.Along with the progressively understanding to nano material, nano powder is utilized to prepare nanometer Ti (C, N) research of based ceramic metal gets more and more, but the Ti (C of very densification can't be prepared so far, N) based ceramic metal, its preparation process has many problems to need to solve, the preparation cost of nano-ceramic powder is very high in addition, therefore the processing method developing the new sintering method sintering process being suitable for nanometer Ti (C, N) based ceramic metal and preparation nanometer powder mix will become but front research emphasis.
Summary of the invention
The technical problem to be solved in the present invention is to provide one and has low density and high rigidity, and Ti (C, the N) based ceramic metal of low production cost and application thereof.
The technical scheme that the present invention takes for the technical problem existed in solution known technology is:
Ti (C, N) based ceramic metal of the present invention, is made up of ceramic phase and Binder Phase, and in described sintering metal, the mass percent of each component is:
Ti48.16～54.29％，
Mo7.1～11.02％，
W3.52～6.31％，
Ni15.56～19.88％，
Y0.47～0.69％，
Al1.53～2.43％，
C9.37～12.54％，
N3.98～4.99％。
The present invention also comprises the application of Ti (C, N) based ceramic metal in cutting tool.
The advantage that the present invention has and positively effect are:
Ti (C of the present invention, N) based ceramic metal adds rare earth element y and AlN in preparation simultaneously, form insoluble compound by the impurity in rare earth element y and sintered compact and be distributed in Ti (C, N) on/Ni phase interface, serve cleaning action on the one hand to phase interface, the bonding strength of phase interface is enhanced, hard-phase particles is made to obtain refinement, the existence of hole can be reduced on the other hand, improve the density of material, be conducive to the raising of Fracture of Material.And in Ti (C, N) based ceramic metal, add AlN, r' phase and Ni can be formed in Binder Phase
3(Al, Ti), makes the Binder Phase of Ti (C, N) based ceramic metal be strengthened, thus improves ceramic-metallic hardness and intensity.The cutting tool utilizing Ti (C, N) based ceramic metal of the present invention to produce, has low density, high rigidity, little to the frictional coefficient of steel, during cutting bonding abrasion and diffusive wear little, the advantage that red hardness is good.In this Ti (C, N) based ceramic metal, main component is TiC, few to the consumption of national strategy resource W, and not containing Co (Domestic Poor Co, 1% of the reserves deficiency whole world).Little (the 7g/cm of density of Ti (C, N) based ceramic metal
3left and right), the powder market value of main component is low, so material cost is low, in production process, do not need the technical process of high-end devices and complexity, production run cost is far below Hardmetal materials.
Embodiment
The present invention will be described in detail by the following examples.
Ti (C, N) based ceramic metal of the present invention, is made up of ceramic phase and Binder Phase.
As shown in table 1, in different embodiment, in sintering metal, the mass percent of each component is:
The mass percent (wt%) of each component in table 1 sintering metal
| Sequence number | Ti | Mo | W | Ni | Y | Al | C | N |
| 1 | 48.16 | 9.88 | 4.27 | 19.32 | 0.63 | 1.86 | 11.86 | 4.02 |
| 2 | 54.15 | 7.1 | 3.52 | 19.88 | 0.47 | 1.53 | 9.37 | 3.98 |
| 3 | 54.29 | 11.02 | 3.52 | 15.56 | 0.47 | 1.53 | 9.63 | 3.98 |
| 4 | 50.38 | 7.1 | 6.31 | 15.56 | 0.69 | 2.43 | 12.54 | 4.99 |
| 5 | 51.26 | 9 | 4.69 | 17 | 0.6 | 1.97 | 11.06 | 4.42 |
The present invention also comprises the application of Ti (C, N) based ceramic metal in cutting tool.Use the milling cutter of sintering metal production specification 4160511 described in the present invention, in order to process 30CrMo steel alloy, above-mentioned milling cutter carries out high speed cutting with the rotating speed alloy steel of 350m/min.Contrast with the hart metal product of same model, the milling cutter be made up of Ti described in the present invention (C, N) based ceramic metal improves 3-6 doubly its work-ing life, and the surface smoothness of steel alloy finished surface is greatly improved, and cutwork efficiency is improved.
Ti (C, N) based ceramic metal of the present invention can be prepared by following steps:
A, carry out raw material assembly, in raw material, the mass percent of each component is: TiC49.6%, TiN15%, WC5%, Ni17%, Mo9%, C0.8%, Y0.6%, AlN3%;
B, add the proportioning of 850 milliliters of dehydrated alcohols by every kg feed material, in above-mentioned raw materials, add dehydrated alcohol, by material wet mixing on planetary ball mill of mixing, ratio of grinding media to material is 8:1, and drum's speed of rotation is 300r/min, batch mixing 72 hours in ball mill;
C, the batch mixing slip obtained in above-mentioned steps is carried out drying in electrically heated drying cabinet, drying temperature is 78 ± 5 DEG C, 12 hours time of drying;
D, configuration quality per-cent are the polyvinyl alcohol solution of 8%, and join in mixture by polyvinyl alcohol solution, and the polyvinyl alcohol solution quality added is 6% of dry mixed material quality, drying-granulating after Homogeneous phase mixing, cross 200 mesh sieves;
E, the powder compression molding will obtained in D step, pressing force 215MPa, pressed compact is of a size of 5.6mm × 5.6mm × 40mm, pressed compact surface flawless;
F, pressed compact is inserted degreasing in vacuum degreasing stove, the vacuum tightness of vacuum degreasing stove is not less than 10Pa, and furnace temperature is warmed up to 800 DEG C with the heat-up rate of 2 DEG C/min from 200 DEG C, and keeps the temperature 2 hours of 800 DEG C;
G, sinter in vacuum sintering furnace, the vacuum tightness in solid state sintering stage is between 1-10Pa, and liquid phase sintering stage vacuum degree is at 1-10
-2between Pa.
Add rare earth element y can with powder stock band people's 0, the impurity such as S react, such as: react with impurity element S and generate the complex chemical compound of S and other elements (Ti, Mo, W, Ni),---ceramic phase interface and ceramic phase---the metallographic phase interface that purified ceramic phase, the bonding strength of phase interface is strengthened, improve the wettability of metallographic phase to ceramic phase simultaneously, decrease the existence of hole, improve the density of material.But the add-on of Y is too much, then after reaction remaining Y also can with Ni reacting generating compound, thus reduce bending strength and hardness.
The volume fraction of Binder Phase increases, ceramic-metallic hardness declines, and bending strength increases gradually, and Binder Phase volume fraction close to 1/4 time reach maximum, volume fraction continue increase, bending strength declines on the contrary, improve hardness and bending strength if think simultaneously, must Binder Phase be strengthened, according to Ni based high-temperature alloy strengthening mechanism, by adding appropriate AlN in Binder Phase, then likely utilize the solution strengthening effect of Al in Ni and Ni simultaneously
3the strengthening effect of Al (r' phase) disperse educt phase, strengthening Binder Phase, improves material property.But Ni
3the fragility of Al (r' phase) is comparatively large, Ni
3al (r' phase) too high levels, reduces the bending strength of material, Ni on the contrary
3al (r' phase) content needs to control in a rational scope, thus needs the add-on of control AlN.According to combination that is theoretical and test, determine rational addition: Y account for that about 0.6%, AlN of oeverall quality per-cent accounts for oeverall quality per-cent about 3%.
The above, it is only preferred embodiment of the present invention, not any pro forma restriction is done to the present invention, although the present invention with preferred embodiment openly as above, but, and be not used to limit the present invention, any those skilled in the art, do not departing within the scope of technical solution of the present invention, certainly the technology contents of announcement can be utilized to make a little change or modification, become the Equivalent embodiments of equivalent variations, in every case be the content not departing from technical solution of the present invention, according to any simple modification that technical spirit of the present invention is done above embodiment, equivalent variations and modification, all belong in the scope of technical solution of the present invention.
Claims (2)
1. Ti (C, a N) based ceramic metal, is made up of ceramic phase and Binder Phase, it is characterized in that: in described sintering metal, the mass percent of each component is as follows:
Ti48.16～54.29％，Mo7.1～11.02％，W3.52～6.31％，Ni15.56～19.88％，Y0.47～0.69％，Al1.53～2.43％，C9.37～12.54％，N3.98～4.99％；
Described Ti (C, N) based ceramic metal is prepared according to following steps:
A, carry out raw material assembly, raw material is made up of TiC, TiN, WC, Ni, Mo, C, Y and AlN, and in raw material, each element carries out proportioning according to required cermet composition;
B, add the proportioning of 850 milliliters of dehydrated alcohols by every kg feed material, in described raw material, add dehydrated alcohol, by material wet mixing on planetary ball mill of mixing, ratio of grinding media to material is 8:1, drum's speed of rotation is 300r/min, batch mixing 72 hours in ball mill, obtains batch mixing slip;
C, the batch mixing slip obtained in step B is carried out drying in electrically heated drying cabinet, drying temperature is 78 ± 5 DEG C, 12 hours time of drying, obtains mixture after drying;
D, configuration quality per-cent are the polyvinyl alcohol solution of 8%, and join in mixture by polyvinyl alcohol solution, and the polyvinyl alcohol solution quality added is 6% of dry mixed material quality, drying-granulating after Homogeneous phase mixing, cross 200 mesh sieves;
E, the powder compression molding will obtained in step D, pressing force 215MPa, pressed compact is of a size of 5.6mm × 5.6mm × 40mm, pressed compact surface flawless;
F, pressed compact is inserted degreasing in vacuum degreasing stove, the vacuum tightness of vacuum degreasing stove is not less than 10Pa, and furnace temperature is warmed up to 800 DEG C with the heat-up rate of 2 DEG C/min from 200 DEG C, and keeps the temperature 2 hours of 800 DEG C;
G, sinter in vacuum sintering furnace, the vacuum tightness in solid state sintering stage is between 1-10Pa, and liquid phase sintering stage vacuum degree is at 1-10
-2between Pa;
In prepared Ti (C, N) based ceramic metal, main component is TiC ceramic phase, and rare earth element y is distributed in Ti (C, N)/Ni phase interface, containing Ni in Binder Phase
3(Al, Ti).
2. the application of Ti (C, N) based ceramic metal in cutting tool described in a claim 1.
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| CN108517449B (en) * | 2018-03-26 | 2021-01-19 | 西安交通大学 | Ti (C, N) -304 stainless steel cermet and preparation process thereof |
| CN108642361B (en) * | 2018-06-11 | 2020-04-17 | 潮安县联兴源陶瓷有限公司 | High-strength high-hardness ceramic material and production process thereof |
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|---|---|---|---|---|
| CN1772701A (en) * | 2005-09-28 | 2006-05-17 | 郑勇 | Functional gradient nanometer composite Ti(C, N)-base cermet and its prepn |
| 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 |
| CN101307406A (en) * | 2008-07-04 | 2008-11-19 | 华中科技大学 | Molybdenum free Ti(C, N)-based cermet and method for preparing same |
| CN101879670A (en) * | 2010-06-03 | 2010-11-10 | 辽宁工程技术大学 | High wear resistance surfacing alloy material containing multiphase metal ceramics |
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1772701A (en) * | 2005-09-28 | 2006-05-17 | 郑勇 | Functional gradient nanometer composite Ti(C, N)-base cermet and its prepn |
| CN101307406A (en) * | 2008-07-04 | 2008-11-19 | 华中科技大学 | Molybdenum free Ti(C, N)-based cermet and method for preparing same |
| 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 |
| CN101879670A (en) * | 2010-06-03 | 2010-11-10 | 辽宁工程技术大学 | High wear resistance surfacing alloy material containing multiphase metal ceramics |
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Effective date of registration: 20230105 Address after: 300240 reservoir area 15, yard, No. 1199, Yuejin Road, Jinzhong street, Dongli District, Tianjin Patentee after: Tianjin Ertong Driers Equipment Manufacturing Co.,Ltd. Address before: No. 12, Gate 54, Block 127, Gangdu Garden, Qingshan District, Wuhan Patentee before: Zheng Handong |