CN102534335A - Rare earth alloy powder-modified Ti(C,N)-based metal ceramic and preparation method thereof - Google Patents
Rare earth alloy powder-modified Ti(C,N)-based metal ceramic and preparation method thereof Download PDFInfo
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- CN102534335A CN102534335A CN2012100138811A CN201210013881A CN102534335A CN 102534335 A CN102534335 A CN 102534335A CN 2012100138811 A CN2012100138811 A CN 2012100138811A CN 201210013881 A CN201210013881 A CN 201210013881A CN 102534335 A CN102534335 A CN 102534335A
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Abstract
The invention discloses a rare earth alloy powder-modified Ti(C,N)-based metal ceramic and a preparation method of the metal ceramic. The metal ceramic comprises Co and Ni or at least two of components selected from Co, Ni as well as Fe as a bonding phase, Ti(C,N) as a basic hard phase and optionally at least one of metallic carbides; and a rare earth alloy powder modifier 0.1-3wt% of the total mass of the metal ceramic. The preparation method comprises treating a raw material through a wet-grinding and mixing process, a die-forming process, a vacuum-degreasing process and a low-pressure sintering process to prepare the rare earth alloy powder-modified Ti(C,N)-based metal ceramic. On the premise of keeping high hardness and high wear resistance, the Ti(C,N)-based metal ceramic prepared according to the invention has excellent comprehensive performance, can be greatly improved in strength and tenacity and can also be widely applied to various cutting tools and wear-resistant parts.
Description
Technical field
The invention belongs to the cermet material preparing technical field, particularly a kind of Ti of rare earth alloy powder modification (C, N) based ceramic metal and preparation method thereof.
Background technology
Ti (C; N) based ceramic metal is because it has higher hardness and wear resistance, excellent chemical stability, red hardness and creep-resistant property; And extremely low a series of feature performance benefits such as rubbing factor; Thereby receive common concern both domestic and external, and shown its great potential as traditional WC-Co wimet equivalent material.But with regard to use properties, and Ti (C, N) based ceramic metal remains in intensity and the insufficient weakness of toughness, and this weakness not only influences its work-ing life, and its use range is restricted.Therefore (C, N) obdurability of based ceramic metal just becomes the problem that material supplier author pays close attention to, and is exactly a kind of valid approach to its interpolation REE wherein how to improve Ti.At Ti (C; N) adding a small amount of REE in the based ceramic metal can refinement hard phase constitution, improve metallographic phase to the wettability of ceramic phase, improve interface Impurity Distribution situation, purify crystal boundary, strengthen the bonding phase, thereby improve ceramic-metallic mechanical property effectively.But because REE is active high; Oxidized extremely easily, and the addition of REE genus trace, must cause REE at Ti (C; N) homogeneity in the based ceramic metal distributes and is difficult to control; (C, N) stability of base metal-ceramic material is relatively poor, thereby has greatly influenced further developing of this technology to cause rare earth Ti.Chinese patent CN 101487094A has announced " containing carbon nitridation titanium ceramet powder of rare earth and preparation method thereof ".This patent provides two kinds of methods that prepare the carbon nitridation titanium ceramet powder that contains rare earth, and what can effectively solve the rare earth phase gathers problem partially.But this method technical process is complicated and wayward, and the suitability for industrialized production that causes related prods is difficulty, and for rare earth Ti (C, N) production of based ceramic metal compact block material preparation and fail to propose reasonable plan.
Summary of the invention
The objective of the invention is to weak point, propose a kind of Ti (C, N) based ceramic metal of rare earth alloy powder modification to prior art.This new Ti (C; N) based ceramic metal can improve its intensity and toughness greatly under the prerequisite that keeps high firmness, high-wearing feature, makes it possess excellent comprehensive performances; And solve REE preferably at Ti (C, the homogeneity question that N) distributes in the based ceramic metal.
Another object of the present invention also is to combine through reasonable component design and optimal preparation technology; A kind of over-all properties that can further improve material is provided; Production technique is easy, the Ti that contains REE that production cost is low relatively (C, N) preparation method of based ceramic metal.
For solving the problems of the technologies described above, technical scheme provided by the invention is Ti (C, N) based ceramic metal of said rare earth alloy powder modification; Comprise with Co, Ni or be selected among Co, Ni and the Fe at least two kinds of components as the bonding mutually, (C N) is basic hard phase with Ti; At least a optional metallic carbide; With rare earth alloy powder properties-correcting agent, Ti (C, N) the composition component of base metal-ceramic material is by weight percentage:
In technique scheme; Said bonding can select for use Co or two kinds of metal-powders of Ni as the bonding phase mutually respectively; Also can select for use among Co, Ni and the Fe two kinds of metal-powders as bonding mutually, preferred Co, three kinds of metal-powders of Ni and Fe as bonding mutually, two or three metal-powder in selecting Co, Ni and Fe for use is as the bonding phase time; Can be arbitrarily than mixing, but the weight fraction of total content must satisfy 8%～30% requirement.
In technique scheme; Preferably a kind of rare earth of said rare earth alloy powder properties-correcting agent-bonding phase alloy; Wherein bonding can be made up of metallic element Co and M mutually; Said M can be at least a among Ni, Fe, Cr, V, Cu and the Al etc., and said rare earth can be at least a among Ce, La, Sm, Pr, Nd, Y, Er, Eu, Gd, Tb, Dy, Ho, Tm, Yb, Lu and the Pm etc.
In technique scheme, said metallic carbide can be selected from WC, Mo
2C, TaC, NbC, Cr
3C
2With VC etc.
The Ti of above-mentioned rare earth alloy powder modification (C, N) the based ceramic metal method that can take to comprise following process step prepares:
(1) press Ti (C, N) the composition component of based ceramic metal batching is inserted ball mill with the raw materials mix powder for preparing; Add grinding medium and carry out the wet-milling dispersion; After fully wet-milling disperses, take out and grind spheroid, will be able to that abundant wet-milling dispersive mixed slurry precipitates, drying;
(2) 1～2wt% by compound weight mixes forming agent, and thorough mixing carries out granulation, drying after evenly, obtain the mixing pellet of good fluidity;
(3) above-mentioned dried mixing pellet is packed into carry out mechanical compression molding in the mould, the compression moulding blank is inserted in the vacuum oven, under 250～350 ℃ and 450～600 ℃, respectively is incubated 40～120min and deviates from forming agent, and the vacuum tightness in the vacuum oven is 1 * 10
-1Pa～1 * 10
-3Pa;
(4) shaping blank that will deviate from forming agent places the low pressure sintering stove, and at 1430～1500 ℃ of following sintering 90～120min, sintering is accomplished back feeding inert atmosphere cool to room temperature and come out of the stove, and promptly makes Ti (C, N) based ceramic metal.
(C N) on the basis of based ceramic metal technical scheme, can further take following technical measures at the Ti of above-mentioned preparation rare earth alloy powder modification.Following each item technical measures can be implemented separately, enforcement also capable of being combined, even implement in the lump.
Said grinding medium is preferentially selected absolute ethyl alcohol or methyl alcohol for use; Said forming agent is a kind of in polyoxyethylene glycol, paraffin, buna and the SD glue; Said wet-milling disperses to pay the utmost attention in the roller milling machine to carry out, and grinds spheroid and preferentially selects the WC-8wt%Co sintered carbide ball for use, and ball-to-powder weight ratio can be controlled in (15～8): 1 scope; The controllable rotation speed of roller milling machine is built in 20～40 rev/mins scope, and the wet-milling dispersive time was generally 60～90 hours; Mixed slurry after fully wet-milling disperses is paid the utmost attention to employing vacuum-drying through the compound that precipitate and separate obtains, and the vacuum-drying Controllable Temperature is built in 60～80 ℃ scope; Shaping blank places low pressure sintering stove agglomerating pressure, pays the utmost attention to 1～6MPa scope that is controlled at, and inert atmosphere is paid the utmost attention to and is argon gas or nitrogen.
The present invention has also taked some other technical measures.
(C is N) under the condition of preparation technology's flow process of based ceramic metal, through adding rare earth alloy powder properties-correcting agent not changing conventional Ti in the present invention; Suppressed Ti (C in the sintered compact alloy effectively; N) growing up of hard phase crystal grain can obtain crystal grain is tiny, be evenly distributed Ti (C, N) hard phase.In sintering process, reaction such as the impurity element O that brings in REE and the raw material powder, S generates rare earth compound, has purified the interface, has improved interface bond strength, and has improved the wettability of metallographic phase to ceramic phase simultaneously.In addition; The adding of rare earth alloy powder makes that the ratio of white core phase increases in the microtexture; This helps reducing the structural stress that black core and annular exist between mutually, and has further strengthened W, Mo, Ta, Cr or V etc. and strengthened the effect of Co, Ni and/or Fe bonding phase, thereby has improved Ti (C; N) fracture toughness property of based ceramic metal, bending strength and hardness make it demonstrate better wear resistance and excellent impact resistance.
(amount that adds REE is all fewer for C, N) based ceramic metal through adding rare-earth element modified Ti.Ti (the C of rare earth alloy powder modification provided by the invention; N) based ceramic metal; The REE that is added is taked to add with rare earth-bonding phase alloy form, makes the prior solid solution of REE in the bonding phase component, and then makes an addition in the sintering metal with the rare earth alloy form; Guaranteed that REE distribution disperse in sintering metal is even, overcome because the few REE difficult problem pockety that is caused of rare earth adding quantity.REE adds with the alloy form of rare earth-bonding phase; Introduced Ni, Fe, Cr, V, Cu, Al and multiple REE, rare earth addition is formed relative diversification, produces the complex effect of multicomponent; And the distribution disperse evenly helps the carrying out of physical-chemical reaction in the sintering process; Thereby it is single effectively to have overcome the interpolation of traditional rare earth additive preparation middle-weight rare earths element, skewness, the difficult problem that oxygen level is high.
The present invention does not change conventional Ti basically, and (production cost is low for C, N) preparation technology's flow process of based ceramic metal; Alloy property is stable to be improved, and implements easily and suitability for industrialized production.Through the Ti of rare earth alloy powder modification (C; N) based ceramic metal can be applicable to all kinds of cutting tools and wear part; Not only can improve the surface quality of mechanical workout benefit and processing work after the application, and the work-ing life that can improve Impact mould and wear part.
(C, N) (C, N) based ceramic metal have improved fracture toughness property, bending strength and hardness to based ceramic metal to Ti provided by the invention significantly, the see after embodiment of face of concrete mechanical performance index than the Ti of prior art.
Description of drawings
Fig. 1 is the SEM back scattering photo (5000 *) of Comparative Examples 1 said goods.
Fig. 2 is microstructure and component Ti, W, Mo, Ta, Ni, the Co of embodiment 1 said goods, the distribution diagram of element of Ce; Wherein Fig. 2-1 is a SEM back scattering photo (5000 *), and Fig. 2-2-1 to Fig. 2-2-7 is respectively the distribution diagram of element of Ti, W, Mo, Ta, Ni, Co, Ce.
Fig. 3 is the SEM back scattering photo (5000 *) of embodiment 3 said goods
Embodiment
Below in conjunction with embodiment and accompanying drawing the present invention is described further, but the invention is not restricted to following examples.
Among each embodiment, involved component concentration per-cent and umber except that specifying, all are weight percentage and parts by weight below.
Embodiment 1:
The Ti of present embodiment (C, N) based ceramic metal raw material (powder) prescription: rare earth alloy powder properties-correcting agent 0.6wt%, Ti (C, N) 53.4wt%, WC 20wt%, Mo
2C 8wt%, TaC 5wt%, Ni 8wt%, Co 5wt%, wherein the feed composition of rare earth alloy powder properties-correcting agent is: rare earth element ce 27.32wt%, bonding phase raw material Co56.28wt%, Ni16.4wt%.The above-mentioned raw materials powder is put into the roller milling machine carry out the wet-milling dispersion; Rotational speed of ball-mill is 30 rev/mins, and milling time is 72 hours, and grinding spheroid employing diameter is the WC-8wt%Co sintered carbide ball of φ 10mm; Ball-to-powder weight ratio is 10: 1, and wet grinding media is an absolute ethyl alcohol.Mixed slurry after grinding sieved to take out grinds spheroid, mixed slurry under 80 ℃ of conditions after the precipitate and separate dry 4 hours compound.1wt% by compound weight mixes polyoxyethylene glycol as forming agent, granulates after mixing, drying, obtains the mixing pellet of good fluidity.Pack in the mould with the pressure compression moulding of 220MPa mixing pellet, again pressed compact is put into vacuum oven and deviate from forming agent, vacuum tightness is 1 * 10 in the vacuum oven
-1Pa is being warming up to 260 ℃ of insulation 40min, 550 ℃ of insulation 40min; Then qualified powder compact is put into the low pressure sintering stove and carry out sintering, use argon gas to make transmission medium, atmosphere pressures is 2MPa, and sintering temperature is 1465 ℃, and soaking time is 105min, feeds big flow argon gas behind the sintering and cools off fast.According to the new Ti of mentioned component and processing condition preparation (C, N) based ceramic metal homogeneous microstructure, its mean grain size are 0.3～1.0 μ m, its microscopic appearance is shown in Fig. 2-1.Measuring above-mentioned ceramic-metallic mechanical performance index is: bending strength 2191MPa, Vickers' hardness 1560MPa, fracture toughness property 11.01MPam
1/2
Comparative Examples 1: with same sample ingredient, the raw material powder that does not add rare earth alloy powder properties-correcting agent mixes by following quality proportioning: and Ti (C, N): 54, WC:20, Mo
2C:8, TaC:5, Ni:8; Co:5 is prepared into sintering metal with existing PM technique again, and its microscopic appearance is as shown in Figure 1; Measuring above-mentioned ceramic-metallic performance index is: bending strength 1639MPa, Vickers' hardness 1479MPa, fracture toughness property 9.21MPam
1/2
This shows that (C, N) hardness of based ceramic metal, bending strength and fracture toughness property have all obtained significant raising, make it possess excellent comprehensive performances through a kind of Ti of rare earth alloy powder modification.The contrast heterogeneous microstructure (seeing Fig. 1 and Fig. 2-1) can find out, under identical preparation process condition, cermet of the present invention Comparatively speaking, Ti (C, N) crystal grain of hard phase more tiny, be more evenly distributed.
Embodiment 2:
The Ti of present embodiment (C, N) based ceramic metal raw material (powder) prescription: rare earth alloy powder properties-correcting agent 1.0wt%, Ti (C, N) 40wt%, WC 26wt%, Mo
2C 10wt%, TaC 8wt%, NbC 6wt%; Ni5wt%, Co 4wt%, wherein the feed composition of rare earth alloy powder properties-correcting agent is: REE Sm 16.87wt%, Dy1.2wt%; Bonding phase raw material Co36.85wt%, Ni36.97wt%, Cu 6.19wt%, Al 1.92wt%.The above-mentioned raw materials powder is put into the roller milling machine carry out the wet-milling dispersion; Rotational speed of ball-mill is 20 rev/mins, and milling time is 82 hours, and grinding spheroid employing diameter is the WC-8wt%Co sintered carbide ball of φ 10mm; Ball-to-powder weight ratio is 8: 1, and wet grinding media is an absolute ethyl alcohol.Mixed slurry after grinding sieved to take out grinds spheroid, mixed slurry through precipitate and separate, under 60 ℃ of conditions dry 6 hours compound.1.2wt% by compound weight mixes paraffin as forming agent, granulates after mixing, drying, obtains the mixing pellet of good fluidity.Pack in the mould with the pressure compression moulding of 200MPa mixing pellet, again pressed compact is put into vacuum oven and deviate from forming agent, vacuum tightness 1 * 10 in the vacuum oven
-2Pa is being warming up to 300 ℃ of insulation 90min, insulation 90min in the time of 500 ℃; Sintering in the low pressure sintering stove uses argon gas to make transmission medium then, and atmosphere pressures is 4MPa, and sintering temperature is 1480 ℃, and soaking time is 90min, feeds big flow argon gas behind the sintering and cools off fast.Measuring above-mentioned ceramic-metallic mechanical performance index is: bending strength 1809MPa, Vickers' hardness 1506MP, fracture toughness property 8.73MPam
1/2
Embodiment 3:
The Ti of present embodiment (C, N) based ceramic metal raw material (powder) prescription: rare earth alloy powder properties-correcting agent 0.4wt%, Ti (C, N) 63.6wt%, WC 8wt%, Mo
2C 5wt%, TaC 5wt%, Ni9wt%, Co 4wt%; Fe 5wt%, wherein the feed composition of rare earth alloy powder properties-correcting agent is: REE Pr 16.95wt%, La10.2wt%, Yb 1.05wt%; Bonding phase raw material Co 51.87wt%, Ni14.65wt%, Fe 5.28wt%.The above-mentioned raw materials powder is put into the roller milling machine carry out the wet-milling dispersion, rotational speed of ball-mill is 26r/min, and milling time is 80 hours, and grinding spheroid employing diameter is the WC-8wt%Co sintered carbide ball of φ 10mm, and ball-to-powder weight ratio is 15: 1, and wet grinding media is a methyl alcohol.Mixed slurry after grinding sieved to take out grinds spheroid, mixed slurry under 80 ℃ of conditions after the precipitate and separate dry 4 hours compound.1.4wt% by compound weight mixes polyoxyethylene glycol as forming agent, granulates after mixing, drying, obtains the mixing pellet of good fluidity.Pack in the mould with the pressure compression moulding of 300MPa mixing pellet, again pressed compact is put into vacuum oven and deviate from forming agent, vacuum tightness 1 * 10 in the vacuum oven
-3Pa is being warming up to 280 ℃ of insulation 60min, insulation 60min in the time of 560 ℃; Then qualified powder compact is put into the low pressure sintering stove and carry out sintering, use argon gas to make transmission medium, atmosphere pressures is 4MPa, and sintering temperature is 1450 ℃, and soaking time is 120min, feeds big flow argon gas behind the sintering and cools off fast.(C, N) the microtexture photo of based ceramic metal is as shown in Figure 3 according to the new Ti of mentioned component and processing condition preparation.Measuring above-mentioned ceramic-metallic mechanical performance index is: bending strength 1987MPa, Vickers' hardness 1654MP, fracture toughness property 10.43MPam
1/2
Embodiment 4:
The Ti of present embodiment (C, N) based ceramic metal raw material (powder) prescription: rare earth alloy powder properties-correcting agent 0.2wt%, Ti (C, N) 53.8wt%, WC 10wt%, Mo
2C 7wt%, Ni 12wt%, Co 8wt%, Fe 9wt%; Wherein the feed composition of rare earth alloy powder properties-correcting agent is: rare earth element nd 35.43wt%, Er 2.3wt%, Eu2.3wt%, Gd 4.6wt%; Bonding phase raw material Co 26.64wt%, Ni 2.19wt%, Fe 26.54wt%.The above-mentioned raw materials powder is put into the roller milling machine carry out the wet-milling dispersion; Rotational speed of ball-mill is 25 rev/mins, and milling time is 75 hours, and grinding spheroid employing diameter is the WC-8wt%Co sintered carbide ball of φ 10mm; Ball-to-powder weight ratio is 10: 1, and wet grinding media is an absolute ethyl alcohol.Mixed slurry after grinding sieved to take out grinds spheroid, mixed slurry under 80 ℃ of conditions after the precipitate and separate dry 5 hours compound.1wt% by compound weight mixes buna as forming agent, granulates after mixing, drying, obtains the mixing pellet of good fluidity.Pack in the mould with the pressure compression moulding of 200MPa mixing pellet, again pressed compact is put into vacuum oven and deviate from forming agent, vacuum tightness 1 * 10 in the vacuum oven
-2Pa is being warming up to 350 ℃ of insulation 40min, insulation 40min in the time of 600 ℃; Sintering in the low pressure sintering stove uses argon gas to make transmission medium then, and atmosphere pressures is 4MPa, and sintering temperature is 1465 ℃, and soaking time is 90min, feeds big flow argon gas behind the sintering and cools off fast.Measuring above-mentioned ceramic-metallic mechanical performance index is: bending strength 1809MPa, Vickers' hardness 1506MP, fracture toughness property 10.18MPam
1/2
Embodiment 5:
The Ti of present embodiment (C, N) based ceramic metal raw material (powder) prescription: rare earth alloy powder properties-correcting agent 0.4wt%, Ti (C, N) 53.6wt%, WC 20wt%, Mo
2C 7wt%, TaC 5wt%, Cr
3C
20.6wt%, VC 0.4wt%, Ni8wt%, Co 5wt%; Wherein the feed composition of rare earth alloy powder properties-correcting agent is: rare earth element y 3.43wt%, Tm 0.95wt%, Ho 2wt%, bonding phase raw material Co 23.79wt%; Ni 56.81wt%, Cr11.57wt%, V 1.45wt%.The above-mentioned raw materials powder is put into the roller milling machine carry out the wet-milling dispersion; Rotational speed of ball-mill is 40 rev/mins, and milling time is 60 hours, and grinding spheroid employing diameter is the WC-8wt%Co sintered carbide ball of φ 10mm; Ball-to-powder weight ratio is 10: 1, and wet grinding media is an absolute ethyl alcohol.Mixed slurry after grinding sieved to take out grinds spheroid, mixed slurry under 80 ℃ of conditions after the precipitate and separate dry 5 hours compound.1wt% by compound weight mixes SD glue as forming agent, granulates after mixing, drying, obtains the mixing pellet of good fluidity.Pack in the mould with the pressure compression moulding of 280MPa mixing pellet, again pressed compact is put into vacuum oven and deviate from forming agent, vacuum tightness 1 * 10 in the vacuum oven
-1Pa is being warming up to 260 ℃ of insulation 60min, 550 ℃ of insulation 60min; Sintering in the low pressure sintering stove uses argon gas to make transmission medium then, and atmosphere pressures is 4MPa, and sintering temperature is 1435 ℃, and soaking time is 105min, feeds big flow argon gas behind the sintering and cools off fast.Measuring above-mentioned ceramic-metallic mechanical performance index is: bending strength 1925MPa, Vickers' hardness 1618, fracture toughness property 10.45MPam
1/2
Embodiment 6:
The Ti of present embodiment (C, N) based ceramic metal raw material (powder) prescription: rare earth alloy powder properties-correcting agent 2.4wt%, Ti (C, N) 51.6wt%, WC 20wt%, Mo
2C 8wt%, TaC 5wt%, Ni6wt%, Co 5wt%,, Fe 2wt%.Wherein the feed composition of rare earth alloy powder properties-correcting agent is: rare earth element nd 13.15wt%, Pm0.35wt%, Tb 0.3wt%, Lu 0.2wt%, bonding phase raw material Co 50.79wt%, Ni16.65wt%, Fe 18.56wt%.The above-mentioned raw materials powder is put into the roller milling machine carry out the wet-milling dispersion; Rotational speed of ball-mill is 29 rev/mins, and milling time is 70 hours, and grinding spheroid employing diameter is the WC-8wt%Co sintered carbide ball of φ 10mm; Ball-to-powder weight ratio is 10: 1, and wet grinding media is an absolute ethyl alcohol.Mixed slurry after grinding sieved to take out grinds spheroid, mixed slurry under 70 ℃ of conditions after the precipitate and separate dry 4.5 hours compound.1.8wt% by compound weight mixes polyoxyethylene glycol as forming agent, granulates after mixing, drying, obtains the mixing pellet of good fluidity.Pack in the mould with the pressure compression moulding of 240MPa mixing pellet, again pressed compact is put into vacuum oven and deviate from forming agent, vacuum tightness 1 * 10 in the vacuum oven
-3Pa is being warming up to 270 ℃ of insulation 100min, 570 ℃ of insulation 100min; Sintering in the low pressure sintering stove uses argon gas to make transmission medium then, and atmosphere pressures is 4MPa, and sintering temperature is 1500 ℃, and soaking time is 90min, feeds big flow argon gas behind the sintering and cools off fast.Measuring above-mentioned ceramic-metallic mechanical performance index is: bending strength 1763MPa, Vickers' hardness 1533, fracture toughness property 10.77MPam
1/2
Claims (10)
- The Ti of a rare earth alloy powder modification (C, N) based ceramic metal, comprise with Co, Ni or be selected among Co, Ni and the Fe at least two kinds of components as the bonding mutually; With Ti (C; N) be basic hard phase, at least a optional metallic carbide is characterized in that being added with rare earth alloy powder properties-correcting agent; Ti (C, N) the composition component of base metal-ceramic material is by weight percentage:
- 2. Ti (the C of rare earth alloy powder modification according to claim 1; N) based ceramic metal; It is characterized in that said rare earth alloy powder properties-correcting agent is a kind of rare earth-bonding phase alloy; Wherein bonding is made up of metallic element Co and M, and said M is at least a among Ni, Fe, Cr, V, Cu and the Al, and said rare earth is at least a among Ce, La, Sm, Pr, Nd, Y, Er, Eu, Gd, Tb, Dy, Ho, Tm, Yb, Lu and the Pm.
- 3. (C, N) based ceramic metal is characterized in that said metallic carbide are selected from WC, Mo to the Ti of rare earth alloy powder modification according to claim 1 2C, TaC, NbC, Cr 3C 2And VC.
- The Ti of each described rare earth alloy powder modification in the claim 1 to 3 (C, N) based ceramic metal preparation method comprises following process step:(1) press Ti (C, N) the composition component of based ceramic metal batching is inserted ball mill with the raw materials mix powder for preparing; Add grinding medium and carry out the wet-milling dispersion; After fully wet-milling disperses, take out and grind spheroid, will be able to that abundant wet-milling dispersive mixed slurry precipitates, drying;(2) 1～2wt% by compound weight mixes forming agent, carries out granulation, drying after thorough mixing is even, obtains the mixing pellet of good fluidity;(3) above-mentioned dried mixing pellet is packed into carry out mechanical compression molding in the mould, the compression moulding blank is inserted in the vacuum oven, under 250～350 ℃ and 450～600 ℃, respectively is incubated 40～120min and deviates from forming agent, and the vacuum tightness in the vacuum oven is 1 * 10 -1Pa～1 * 10 -3Pa;(4) shaping blank that will deviate from forming agent places the low pressure sintering stove, and at 1430～1500 ℃ of following sintering 90～120min, sintering is accomplished back feeding inert atmosphere cool to room temperature and come out of the stove, and promptly makes Ti (C, N) based ceramic metal.
- 5. (C, N) based ceramic metal preparation method is characterized in that said grinding medium is absolute ethyl alcohol or methyl alcohol to the Ti of rare earth alloy powder modification according to claim 4.
- 6. (C, N) based ceramic metal preparation method is characterized in that said forming agent is a kind of in polyoxyethylene glycol, paraffin, buna and the SD glue to the Ti of rare earth alloy powder modification according to claim 4.
- 7. (it is characterized in that said wet-milling is scattered in the roller milling machine carries out the Ti of rare earth alloy powder modification according to claim 4 for C, N) based ceramic metal preparation method, and grinding spheroid is the WC-8wt%Co sintered carbide ball, and ball-to-powder weight ratio is (15～8): 1.
- 8. (rotating speed that it is characterized in that the roller milling machine is 20～40 rev/mins to the Ti of rare earth alloy powder modification according to claim 7 for C, N) based ceramic metal preparation method, and the wet-milling dispersive time is 60～90 hours.
- 9. (C, N) based ceramic metal preparation method is characterized in that the compound that obtains through deposition adopts vacuum-drying to the Ti of rare earth alloy powder modification according to claim 7, and drying temperature is 60～80 ℃.
- 10. (air pressure that it is characterized in that said low pressure sintering is 1～6MPa for C, N) based ceramic metal preparation method, and inert atmosphere is argon gas or nitrogen according to the Ti of the described rare earth alloy powder modification of one of claim 4 to 9.
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