CN110373592A - A kind of Ti (C, N) based metal ceramic cutter material and preparation method thereof - Google Patents
A kind of Ti (C, N) based metal ceramic cutter material and preparation method thereof Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- 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
- B22F3/10—Sintering only
- B22F3/1003—Use of special medium during sintering, e.g. sintering aid
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- 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
- B22F3/10—Sintering only
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- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/04—Making non-ferrous alloys by powder metallurgy
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- 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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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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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- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F2005/001—Cutting tools, earth boring or grinding tool other than table ware
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Abstract
The present invention provides a kind of Ti (C, N) based metal ceramic cutter material and preparation method thereof, material includes the raw material of following mass percent component: Ti (C0.5,N0.5): 31.5~35.5%；(Ti, W) C:20.5~25.5%；TiC:8~12%；Mo2C:10~11%；(Ta, Nb) C:4~9%；VC:0~1.0%；Cr2C3: 0~0.5%；Co:9%；Ni:6%；Er:0~1.0%；C:0.5%.Method includes: that polyethylene glycol and industrial alcohol are added after weighing raw material according to the ratio, ball milling and sieving is carried out after mixing, then carry out mist projection granulating, die forming, the degreasing of positive pressure hydrogen, solid-phase sintering, liquid-phase sintering and fast cold treatment to obtain the final product.Its cutting stability and service life can be improved after cutter is made in gained Ti (C, N) based metal ceramic cutter material.
Description
Technical field
The present invention relates to cermet material field, in particular to a kind of Ti (C, N) based metal ceramic cutter material and its
Preparation method.
Background technique
Cermet has high rigidity, high-wearing feature, red hardness and chemical stabilization as a kind of novel hard material
Property, thus it is widely used as cutter material, mold materials and heat-resisting, wear parts, also obtain more and more researchers'
Concern.Particularly, as cutting tool, Ti (C, N) based ceramic metal has that high temperature resistant, coefficient of friction be small, anti-metal adherence
Can be good the features such as, finishing, semifinishing cutting steel part and in terms of step by step part instead of traditional hard
Matter alloy cutter.However, ceramic tool has the shortcomings that poor toughness and chipping resistance, it is broken that there are abnormal cutters
It splits, if the simple content by improving Binder Phase, then can be improved toughness, but will cause the wear-resisting property of cutter simultaneously significantly
It reduces, anti-plasticity ability can also decline, and final cutter life is also poor.Therefore, by adjusting primitive component, to a certain degree
On can improve the performance of cermet, but its hardness and toughness is often made to be difficult to reach the characteristic of " double height ".And in fact, logical
The specific technology controlling and process of cermet during the preparation process is crossed, can be good at promoting its structure and performance.It is understood that golden
Belong to ceramics to be characterized in being coated with core hard phase with circular phase, and be embedded in Binder Phase, is formed more complicated microcosmic
Structure, wherein the thickness of the interface wellability and circular phase of Binder Phase and circular phase will determine the microstructure of cermet and comprehensive
Close mechanical property, the final cutting effect for influencing cutter.In the preparation process of cermet, sintering condition is largely
Determine the thickness i.e. interface wellability of circular phase.Because nitrogen plays main in Ti (C, N) based ceramic metal
Effect, on the one hand, contain certain nitrogen content in the material, the concentration of nitrogen will affect the thickness of circular phase and the crystalline substance of carbonitride
Grain, while also will affect solid solution degree of other elements in Binder Phase and circular phase；On the other hand, nitrogen is in sintering process
In, volatilization evolution, especially in solid-phase sintering process, not only causes the unbalance of nitrogen concentration and causes material at a higher temperature
Inside leaves stomata, and in liquid sintering process, and due to the influence of nitrogen concentration gradients, surface concentration is low and concentration inside
Height, and Binder Phase can then be migrated to material surface, formed enriched layer, caused the reduction of surface hardness, be formed hard outer soft in one kind
Structure, to substantially reduce the wearability of cutter.Therefore, during the sintering process, for technology controlling and process, especially to the tune of nitrogen
Control is most important to material property is improved.
It is therefore desirable to provide a kind of preparation method of Ti (C, N) based ceramic metal with change of gradient, improve Ti (C,
N) the whole toughness of the surface abrasion resistance of base ceramet tool bit and material.
Summary of the invention
In view of the deficiencies of the prior art, the present invention provides a kind of Ti (C, N) based metal ceramic cutter material and its preparations
Method, its purpose is to improve Ti (C, N) base ceramet tool bit wearability and toughness, so that Ti (C, N) Base Metal be made to make pottery
The cutting stability and service life of porcelain cutter get a promotion.
In order to achieve the above object, the invention provides the following technical scheme:
A kind of Ti (C, N) based metal ceramic cutter material, the raw material including following mass percent component: Ti (C0.5,
N0.5): 31.5~35.5%；(Ti,W) C:20.5~25.5%；TiC:8~12%；Mo2C:10~11%；(Ta, Nb) C:4~
9%；VC:0~1.0%；Cr2C3: 0~0.5%；Co:9%；Ni:6%；Er:0~1.0%；C:0.5%.
Preferably, above-mentioned Ti (C, N) based metal ceramic cutter material, the raw material including following mass percent component: Ti
(C0.5,N0.5): 31.5%；(Ti,W) C:25.5%；TiC:9.0%；Mo2C:10.5%；(Ta, Nb) C:6.5%；VC:0.6%；
Cr2C3: 0.4%；Co:9%；Ni:6%；Er:0.5%；C:0.5%.
Preferably, the ceramic tool is in the change of gradient of interior tough and outer hard.
The present invention also provides a kind of preparation methods of above-mentioned Ti (C, N) based metal ceramic cutter material, include the following steps:
(1) each raw material is weighed according to the ratio, polyethylene glycol and industrial alcohol are added into raw material, and ball milling and mistake are carried out after mixing
Sieve, obtains slurry；Wherein, the additional amount of polyethylene glycol accounts for the 3~4% of total mass of raw material；Industrial alcohol is according to 0.78~0.80
The amount of liter/kilogram raw material is added；
(2) slurry obtained by step (1) is subjected to mist projection granulating, obtains mixture；
(3) mixture obtained by step (2) is subjected under the pressure of 80~120MPa die forming, obtains green compact；
(4) green compact obtained by step (3) is subjected to positive pressure hydrogen degreasing at 25~450 DEG C；
(5) green compact after degreasing is subjected to solid-phase sintering and liquid-phase sintering；
Solid-phase sintering specifically: 910 DEG C are warming up to from 450 DEG C with the speed of 7 DEG C/min under vacuum first, at 910 DEG C
Keep the temperature 30~60min；Then 1280 DEG C are warming up to from 910 DEG C with the speed of 5 DEG C/min under vacuum, are passed through nitrogen at 1280 DEG C
Gas keeps the temperature 60~90min；
Liquid-phase sintering specifically: be warming up to 1480 DEG C from 1280 DEG C with the speed of 3 DEG C/min, be passed through nitrogen at 1480 DEG C
Keep the temperature 60~90min；
(6) green compact after sintering is subjected to fast cold treatment under an argon atmosphere, obtains Ti (C, N) base ceramet tool bit material
Material.
Preferably, ball milling condition in step (1): drum's speed of rotation is 35~40r/min, and Ball-milling Time is 30~54h.
Preferably, positive pressure hydrogen degreasing described in step (4) be specially under the hydrogen of flowing, with the speed of 10 DEG C/min from
25 DEG C are warming up to 320 DEG C, then are warming up to 370 DEG C from 320 DEG C with the speed of 2 DEG C/min, in 370 DEG C of 30~60min of heat preservation, finally
450 DEG C are warming up to from 370 DEG C with the speed of 2 DEG C/min, in 450 DEG C of 60~90min of heat preservation.
Preferably, the vacuum degree of solid-phase sintering is lower than 5Pa in step (5).
Preferably, in step (5) solid-phase sintering nitrogen pressure size be absolute pressure 5~50mbar.
Preferably, in step (5) liquid-phase sintering nitrogen pressure size be relatively large air pressure 10~100mbar.
Preferably, in step (6) fast cold treatment be specially under the argon atmosphere of 100~200mabr, with 20~40 DEG C/
The speed of min is cooled to 800 DEG C from 1480 DEG C.
The high temperature red hardness and thermal-shock resistance of cutter are improved by optimizing the content of the second phase carbide in the present invention,
Improve the interrupted cut performance of cutter.As (Ta, Nb) C can inhibit to a certain degree growing up for crystal grain, Cr2C3Bonding can be dissolved into
Mutually and on phase interface, inhibits the extension of crackle, improve the fracture toughness and bending strength of material；VC fusing point with higher,
It is not easy to be dissolved in material, its main effect is the inhibitor of grain growth, improves the hardness and wear-resisting property of material.Cause
This, the two is added simultaneously to improve the wearability and toughness of material in certain degree.
Rare earth element er is added in cermet, is allowed to the gas in conjunction with interface impurity and purifies interface, it can be significantly
Improve the wellability of Binder Phase and hard phase interface.Meanwhile the addition of Er can reduce the temperature that the liquid phase of cermet occurs,
Make the entrance liquid-phase sintering stage of cermet earlier, reduces the denitrogenation amount of nitrogen, improve the densification of material, to improve gold
Belong to the comprehensive performance of ceramics.
During the sintering process, especially in solid-phase sintering, liquid-phase sintering, the microcosmic knot of material is adjusted by nitrogen atmosphere
Structure and performance with significant importance.In solid-phase sintering process, in the lower temperature stage, mainly foreign gas is a large amount of
Discharge, such as O2, CO etc..And the volatilization in higher temperature stage (in the period of especially before liquid phase appearance) nitrogen escapes,
So that material internal leaves hole, more metal elements Ws, Mo, Ta, Nb etc. are enriched to core by solution modeling mechanism at this time
Surface causes the exception of circular phase to thicken.Circular phase is a kind of brittlement phase, blocked up to be easy to cause cutter easily broken.Meanwhile it is above-mentioned
Excessive being dissolved into Binder Phase of metallic element will cause the reduction of hard phase volume fraction, and material hardness is caused to substantially reduce.Cause
This, in the solid-phase sintering stage, being passed through certain nitrogen point partial pressure sintering can inhibit the volatilization of nitrogen to escape well, reduce residual
The generation for gap of boxing out, can also inhibit circular phase transition thicken and the reduction of hard phase volume fraction.
Under the hot conditions of liquid-phase sintering, the fusing point of material Binder Phase is lower, be easy to cause the volatilization of part adhesive phase,
Toughness of material is caused to reduce.Meanwhile nitrogen can also volatilize in the solid-phase sintering stage, cause Binder Phase can to surface aggregation, from
And increase the volatilization of Binder Phase.Therefore, in the liquid-phase sintering stage, being passed through certain micro-positive pressure nitrogen static state sintering can be very
Inhibit the volatilization of Binder Phase in big degree, in addition, the concentration inside that nitrogen gas concn is higher than material can be such that Binder Phase internally migrates
Diffusion forms a kind of Binder Phase by the structure of surface internally stepped change.That is hard phase of the surface with high-content, and it is internal
Binder Phase continuously varying gradient structure with high-content, so that the existing preferable toughness of material and higher surface abrasion resistance
Property.
On the one hand growing up for crystal grain can be inhibited using argon gas fast-cooling technology, refine crystal grain；On the other hand due in Binder Phase
Co phase have two kinds of crystal forms of α-Co and ε-Co, α-Co is face-centered cubic (fcc) structure, there is 12 slide surfaces, good toughness；ε-Co is
Close-packed hexagonal (hcp) structure, only 3 slide surfaces absorb strain energy and relaxed stress and coordinate two-phase adaptability to changes ratio
α-Co is poor, and toughness is also poor, and fast cold treatment can make the α-Co of high temperature state is minimal amount of to be changed into ε-Co, improves toughness, on the other hand,
Rapid cooling process will not to bond opposite surface migration diffusion, equally be retained in state when high-temperature liquid-phase sintering.
In conclusion by the second phase carbide and addition rare earth element er in optimization primitive component, and adjustment exists
The technology controlling and process of sintering process, the cutting stability and service life for capableing of ceramic tool get a promotion.
Above scheme of the invention have it is following the utility model has the advantages that
1. the present invention by adjusting optimization primitive component in the second phase carbide and addition rare earth element er, make Ti (C,
N) hardness, wearability, toughness and high-temperature behavior of based ceramic metal get a promotion, and improve the stability that cutter uses, and extend
The whole service life of cutter, ensure that the surface quality of workpieces processing, to effectively improve the cutting ability of cutter.
2. the cross that (C, the N) base ceramet tool bit of Ti made from sintering preparation method provided by the invention passes through scalpel blade
Section surface layer, subsurface stratum, central area Vickers hardness, test obtain tool surface hardness highest, can reach 1695MPa with
On, sub-surface is taken second place, and inner hardness is then lower than 1600MPa, in the change of gradient of interior tough and outer hard；Bending strength is greater than
1800MPa, fracture toughness are greater than 9.20MPam1/2。
Specific embodiment
To keep the technical problem to be solved in the present invention, technical solution and advantage clearer, below in conjunction with specific implementation
Example is described in detail.
Each hard phase and binding metal are weighed by following proportion: Ti (C, N), (Ti, W) C, TiC, Mo2C,(Ta,Nb)
C,VC,Cr2C3, Er, Co, Ni and carbon black, Examples 1 to 3 and each material content of comparative example 1~3 are as shown in table 1.
The material composition table of 1 Examples 1 to 3 of table
Prepared mixed raw material is poured into ball mill, and accounts for 3~4% polyethylene glycol that raw material gross weight is added, ball
Grinding process are as follows: ratio of grinding media to material 10:1, abrading-ball are the YG8 sintered carbide ball of φ 8；Ball-milling medium be industrial alcohol (alcohol/pure water be 9:
1), alcohol dosage be 0.75~0.80L/kg (according to 0.78~0.80 liter/kilogram raw material amount add), Ball-milling Time be 30~
54h, drum's speed of rotation is 35~40r/min, after the completion of ball milling, by slurry through 325 mesh net filtrations.
C, mist projection granulating
Sieved slurry is subjected to mist projection granulating, the technique of mist projection granulating are as follows: the speed of slurry stirring is done in 12~14Hz
Use nitrogen stream in dry tower is dry, and nitrogen pressure is 2.6~3kPa, and spray tower outlet temperature is maintained at 95~100 DEG C, sprays piece
Diameter carries out mist projection granulating, atomizing pressure 1.2kPa using 1.0mm.
D, compacting, sintering
By mixed raw material after pressing pressure is pressed into the blade of certain size and shape for 80~120MPa, it is put into de-
Rouge-sintering integrated furnace is sintered, and sintering process is as shown in table 2:
Positive pressure degreasing process: 320 DEG C are risen to from room temperature with the heating rate of 10 DEG C/min, then with the heating speed of 2 DEG C/min
Rate is from 320 DEG C of continuous warmings to 370 DEG C, in the process, H2Flow be 50L/min carry out H2Positive pressure degreasing, because of H2's
It is strong to permeate degreasing power, the organic forming agent of material internal can be removed clean；After 370 DEG C of heat preservation 60min, with 2 DEG C/
The heating rate of min is warming up to 450 DEG C, 450 DEG C of heat preservation 90min from 370 DEG C, removes the forming agent of material internal with thoroughly dry
Only, then TORVAC processing is carried out, time 50min is passed through the Ar of 80L/min, and internal residual hydrogen is discharged；
The solid-phase sintering first stage: 450~910 DEG C are the vacuum solid-phase sintering stage, in TORVAC after treatment, with 7
DEG C/heating rate of min is warming up to 910 DEG C from 450 DEG C, high vacuum state is in furnace, vacuum degree is lower than 5Pa hereinafter, 910
DEG C when keep the temperature 30min, in this process, using vacuum-sintering, dominant powder oxide on surface reduction, intergranular contact is answered
Power gradually eliminates, and escapes its internal impurity, gas adequately, avoids the intervention of other gases, and protects at 910 DEG C
Wen Ze is the diffusion of subsequent particle, causes so that oxidation-reduction process, contact stress and foreign gas are adequately discharged
Densification etc. is prepared；
Solid-phase sintering second stage: 910~1280 DEG C are vacuum+atmosphere solid-phase sintering stage, are terminated with 910 DEG C of heat preservations
Afterwards, 1280 DEG C are warming up to from 910 DEG C with the speed of 5 DEG C/min, this process according to use vacuum-sintering, in this temperature-rise period,
It is so that remaining stress, foreign gas etc. is discharged completely, in addition, the ring of cermet using lower heating rate
Shape is mutually grown, and the growth of especially annular is more abundant, and complete inner ring can mutually reduce hard phase and the lattice of Binder Phase loses
With degree, interface can be reduced, and phase interface is made to have high binding force；At 1280 DEG C, 60min is kept the temperature, is led to during incubation
Enter certain nitrogen partial pressure, on the one hand, the easy material denitrogenation phenomenon of material itself at relatively high temperatures is easy to form gas in the material
Hole, and denitrogenation will cause circular phase abnormal growth, and material property is caused to reduce, and it is passed through certain nitrogen point at this temperature
Pressure, can inhibit the abnormal growth of stomata caused by the denitrogenation of material and circular phase.
The liquid-phase sintering stage: 1280~1480 DEG C are micro-positive pressure liquid-phase sintering stage, in this process, mainly particle
The processes such as rearrangement, crystallization of the dissolution and precipitation, be warming up to 1480 DEG C from 1280 DEG C with the speed of 3 DEG C/min, in this temperature-rise period,
It is after there is liquid phase using lower heating rate, under the action of surface tension, the frictional force between hard phase is reduced,
So that intergranular gap reduces, the aggravation of material structure densification process, and in this process, hard-phase particles occur molten
Solution-precipitation process forms " core-ring " structure, and Binder Phase also sufficiently spreads and migrates, and keeps its heterogeneous microstructure more uniform,
Form " black core/Bai Xin ", the institutional framework that white inner ring/ash outer ring and Binder Phase coexists；In 1480 DEG C of heat preservation 60min, keeping the temperature
Period is passed through the sintering of 50mbar nitrogen gas micro-positive pressure static state, and in this process, nitrogen forms the high nitrogen concentration in surface and internal low nitrogen
Concentration, i.e. progress surface carburization processing, and nitrogen is low with Binder Phase affinity, it is suppressed that the chance to external migration of Binder Phase makes
Material has outer hard interior tough change of gradient microstructure, in addition, the sintering of micro-positive pressure static state also can inhibit Binder Phase in high temperature item
Volatilization under part, to increase the toughness of material.
The cooling down stage: after sintering, carrying out fast cold treatment, with the speed of 20~40 DEG C/min, in 30min from
1480 DEG C drop to 800 DEG C hereinafter, to retain the performance of the condition of high temperature, and crystal grain are inhibited to grow up.
The experiment condition of 2 Examples 1 to 3 of table and comparative example 1~3
The test that mechanical property is carried out to Examples 1 to 3 and 1~3 gained ceramic cutting tool material of comparative example, as a result such as table 3
It is shown.
As shown in Table 3, the solid-phase sintering stage be passed through 20~40mbar nitrogen and the liquid-phase sintering stage be passed through 40~
60mbar nitrogen the hardness of material can be made to present internal lower and surface is high, sub-surface is taken second place, the toughness of material is maintained at one
A higher level, the comprehensive performance of material obtain higher promotion, thus cutter wearability promoted and chipping resistance,
Plasticity_resistant deformation ability is preferably promoted.
In order to verify cutting effect of the invention, the cutter of the WNMG080404-FG with iso standard, counter blade have been manufactured
Mouth circular arc carries out blasting treatment ER:0.035mm, and it is continuous to carry out dry type to embodiment 2 and 1 gained ceramic tool of comparative example
High-speed cutting test.Technological parameter is as follows: being cut material: 40Cr bar, HRC35, it is desirable that precision is lower than Ra < 1.6 μm, cutting
Speed Vc:240m/min, cutting-in ap:0.40mm feed f:0.15mm/rev.The results are shown in Table 4 for Tool in Cutting.
4 Tool in Cutting experimental result of table
| Number | Process time (min) | Workpiece surface roughness Ra (μm) | Tool flank wear Vb (mm) |
| Embodiment 3 | 35 | 1.21 | 0.091 |
| Comparative example 1 | 30 | 1.55 | 0.141 |
As shown in Table 4, certain nitrogen is passed through in solid-phase sintering and liquid-phase sintering stage to can reduce material surface coarse
Degree, improves the wearability of material.
The above is a preferred embodiment of the present invention, it is noted that for those skilled in the art
For, without departing from the principles of the present invention, it can also make several improvements and retouch, these improvements and modifications
It should be regarded as protection scope of the present invention.
Claims (10)
1. a kind of Ti (C, N) based metal ceramic cutter material, which is characterized in that the raw material including following mass percent component:
Ti(C0.5,N0.5): 31.5~35.5%；(Ti,W) C:20.5~25.5%；TiC:8~12%；Mo2C:10~11%；(Ta,
Nb) C:4~9%；VC:0~1.0%；Cr2C3: 0~0.5%；Co:9%；Ni:6%；Er:0~1.0%；C:0.5%.
2. Ti (C, N) based metal ceramic cutter material according to claim 1, which is characterized in that including following quality percentage
Than the raw material of component: Ti (C0.5,N0.5): 31.5%；(Ti,W) C:25.5%；TiC:9.0%；Mo2C:10.5%；(Ta, Nb) C:
6.5%；VC:0.6%；Cr2C3: 0.4%；Co:9%；Ni:6%；Er:0.5%；C:0.5%.
3. Ti (C, N) based metal ceramic cutter material according to claim 1, which is characterized in that the ceramic tool
In the change of gradient of interior tough and outer hard.
4. a kind of preparation method of Ti (C, N) based metal ceramic cutter material as described in claims 1 to 3 any one,
It is characterized in that, includes the following steps:
(1) each raw material is weighed according to the ratio, polyethylene glycol and industrial alcohol are added into raw material, and ball milling and sieving are carried out after mixing,
Obtain slurry；Wherein, the additional amount of polyethylene glycol accounts for the 3~4% of total mass of raw material；Industrial alcohol according to 0.78~0.80 liter/
The amount addition of kilogram raw material；
(2) slurry obtained by step (1) is subjected to mist projection granulating, obtains mixture；
(3) mixture obtained by step (2) is subjected under the pressure of 80~120MPa die forming, obtains green compact；
(4) green compact obtained by step (3) is subjected to positive pressure hydrogen degreasing at 25~450 DEG C；
(5) green compact after degreasing is subjected to solid-phase sintering and liquid-phase sintering；
Solid-phase sintering specifically: be warming up to 910 DEG C from 450 DEG C with the speed of 7 DEG C/min under vacuum first, kept the temperature at 910 DEG C
30~60min；Then 1280 DEG C are warming up to from 910 DEG C with the speed of 5 DEG C/min under vacuum, nitrogen guarantor is passed through at 1280 DEG C
60~90min of temperature；
Liquid-phase sintering specifically: be warming up to 1480 DEG C from 1280 DEG C with the speed of 3 DEG C/min, nitrogen heat preservation is passed through at 1480 DEG C
60~90min；
(6) green compact after sintering is subjected to fast cold treatment under an argon atmosphere, obtains Ti (C, N) based metal ceramic cutter material.
5. the preparation method according to claim 4, which is characterized in that ball milling condition in step (1): drum's speed of rotation 35
~40r/min, Ball-milling Time are 30~54h.
6. the preparation method according to claim 4, which is characterized in that positive pressure hydrogen degreasing described in step (4) specially exists
Under the hydrogen of flowing, 320 DEG C are warming up to from 25 DEG C with the speed of 10 DEG C/min, then be warming up to from 320 DEG C with the speed of 2 DEG C/min
370 DEG C, in 370 DEG C of 30~60min of heat preservation, 450 DEG C finally are warming up to from 370 DEG C with the speed of 2 DEG C/min, is kept the temperature at 450 DEG C
60~90min.
7. the preparation method according to claim 4, which is characterized in that the vacuum degree of solid-phase sintering is lower than in step (5)
5Pa。
8. the preparation method according to claim 4, which is characterized in that the nitrogen pressure size of solid-phase sintering is in step (5)
5~50mbar of absolute pressure.
9. the preparation method according to claim 4, which is characterized in that the nitrogen pressure size of liquid-phase sintering is in step (5)
30~100mbar of relatively large air pressure.
10. the preparation method according to claim 4, which is characterized in that in step (6) fast cold treatment be specially 100~
Under the argon atmosphere of 200mabr, 800 DEG C are cooled to from 1480 DEG C with the speed of 20~40 DEG C/min.
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| CN111647787A (en) * | 2020-06-16 | 2020-09-11 | 四川神工钨钢刀具有限公司 | TiCN-based particle metal ceramic cutter and preparation method thereof |
| CN112357896A (en) * | 2020-11-23 | 2021-02-12 | 株洲昊坤硬质材料有限公司 | Preparation method and device of superfine titanium carbonitride |
| CN112853187A (en) * | 2021-01-07 | 2021-05-28 | 中南大学 | Weak core ring structure fine-grain homogeneous TiCN-based metal ceramic and preparation method thereof |
| CN112962008A (en) * | 2021-01-29 | 2021-06-15 | 嘉兴鸷锐新材料科技有限公司 | Ti (C, N) -based metal ceramic tool and preparation method thereof |
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