CN102400028A - Preparation method of metal matrix composite - Google Patents
Preparation method of metal matrix composite Download PDFInfo
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- CN102400028A CN102400028A CN2011103924718A CN201110392471A CN102400028A CN 102400028 A CN102400028 A CN 102400028A CN 2011103924718 A CN2011103924718 A CN 2011103924718A CN 201110392471 A CN201110392471 A CN 201110392471A CN 102400028 A CN102400028 A CN 102400028A
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Abstract
The invention provides a preparation method of a metal matrix composite and belongs to the field of preparation of structural materials. Compared with a traditional powder metallurgy process, the method provided by the invention has the following advantages: (1) a series of complex process such as pressing, degumming, sintering and the like in traditional powder metallurgy can be omitted; and (2) by virtue of the induction actions of capillary force and Ti-C reaction, the wetting property of molten metal and a ceramic phase can be improved, and phenomena such as sweating, loss of the molten metal and the like caused by poor wetting property of the metal and ceramic phase in a powder metallurgy sintering process do not exist. The method is characterized in that a porous framework is prepared by adopting a gel casting and carbohydrate body pore-forming method, so that the interior of the porous framework is provided with air holes which are totally communicated, and the porosity is 70-80%; in an infiltration process, various C-containing metal powder, comprising iron powder, nickel powder, cobalt powder and other alloy powder, can be adopted; and finally, the metal matrix composite with TiC generated in situ and the ceramic phase dispersed in a metal matrix can be prepared. The preparation method provided by the invention is low in technical cost and simple in process and can be used for preparing large-szie and complex-shape products; and the finished product can maintain the shape of the porous framework and can be subjected to net size molding.
Description
Technical field
The present invention relates to a kind of metal-base composites technology of preparing, belong to the structured material preparation field, being in particular the preparation matrix material provides a kind of cost low, and technology is simple, can realize industrialized new technology.
Background technology
Metal-base composites has advantages such as light weight, intensity is high, antiwear heat resisting property is good, is a kind of advanced person's engineering materials, obtains increasingly extensive application in high-tech sectors such as space flight, automobile, biotechnology.But it is wetting hardly that the difficult point of its production technique is between many metals and alloy and the enhancing body, thereby preparation technology is had relatively high expectations.Through development in recent ten years, mature methods mainly contains powder metallurgic method, squeeze casting method, semi-solid state stirring etc.Powder metallurgic method mainly comprises mixing, compacting and three primary processes of sintering; Powder metallurgy prepares metal-base composites; Adopt liquid phase sintering under the situation mostly; Sintering temperature and melting point metal are more approaching, occur sintered article distortion and the unsound phenomenon of large size goods sintering easily, under the situation of metal and ceramic phase wettability difference, also can occur " sweating " in the sintering process and phenomenon such as molten metal loss.
The present invention adopts stephanoporate framework vacuum reaction in infiltration technique to prepare ceramic-metal composite; The stephanoporate framework that, titanium nickeliferous with carbonaceous alloy powder infiltration and ceramic phase are formed; Wherein stephanoporate framework adopts the preparation of gel injection sugar body port-creating method; The stephanoporate framework that can prepare various complicated shapes, and stephanoporate framework intensity is high, inner complete in being communicated with pore, in molten metal infiltration process, can not cave in; C element in the metallic solution and the Ti reaction in the stephanoporate framework generate TiC, finally form TiC and other ceramic phase metal-base composites that disperse distributes in metallic matrix.This infiltration process can make molten metal evenly fill all holes by capillary force and the reaction induced effect of Ti-C; Thereby make the very poor ceramic phase of script wettability in the wetting skeleton of molten metal; And there is a mutual diffusion of metallic element and Ti element in the molten metal; Reaction in is separated out thin TiC crystal grain, forms ceramic phase and generated in-situ TiC disperse and is distributed in the metallic matrix, and final molten metal is full of whole skeleton; Keep bone porous shape, the disposable metal-base composites of preparing designated shape.
The present invention proposes stephanoporate framework vacuum reaction in infiltration technique; And prepared multiple metal-base composites with this technology; Comparing advantage with the technology that prior powder metallurgy prepares metal_based material is: (1) technology is simple; Cost is low; Saved the wettability of prior powder metallurgy compacting-come unstuck-a series of complicated technologies (2) such as sintering through capillary force and reaction induced improved effect molten metal of Ti-C and ceramic phase, do not have metal and ceramic phase wettability difference in the powder metallurgical sintering process and occur sweating, phenomenon such as molten metal loss.(3) can prepare large size, complex-shaped goods, end article can keep bone porous shape, can accomplish near-net-shape.
Summary of the invention
The present invention proposes stephanoporate framework vacuum reaction in infiltration technique, and adopts this technology to prepare large size, complex-shaped metal-base composite-material product.
The stephanoporate framework that this technology adopts that the metal alloy powder vacuum reaction in infiltration that contains C is nickeliferous, titanium and ceramic phase are formed is finally prepared in-situ formation of TiC and the ceramic phase disperse is distributed in the metal-base composites in the metallic matrix.
At first adopt gel injection sugar body port-creating method to prepare the stephanoporate framework preform blank of designated shape, then stephanoporate framework preform blank and metal alloy powder are put into ceramic crucible, the vacuum infiltration is carried out in heating in vacuum oven.Bone porous formation and vacuum infiltration can disposablely be accomplished.The finished product keep bone porous shape, to the effect to near-net-shape.
Concrete technical matters is following:
1, porous material preform blank preparation: is raw material in ceramics powder and the granularity of 1 ~ 10 μ m at 10 ~ 50 μ m nickel powders in 10 ~ 50 μ m titanium valves, granularity with granularity; Massfraction is respectively 5 ~ 55wt%, 40 ~ 90wt%, 5 ~ 20wt%, and adopting common rolling ball milling is medium with toluene, ball milling 5 ~ 10h; Compound is dry 5 ~ 8h in vacuum drying oven; Compound adopts gel injection toluene-Rocryl 400 gelling system moulding, does pore-forming material with the sucrose of granularity 100 ~ 300 μ m, and add-on is the 10 ~ 90vol.% that accounts for the base substrate volume(tric)fraction; Base substrate is dry 5 ~ 10h in vacuum drying oven, prepares the porous material preform blank;
2, the preparation of alloy powder: is raw material in Graphite Powder 99 and the granularity of 5 ~ 10 μ m at 10 ~ 50 μ m chromium powders in metal powder, the granularity of 10 ~ 50 μ m with granularity; Massfraction is respectively 70 ~ 98wt%, 0.1 ~ 10wt%, 1 ~ 29.9wt%, and to adopt high energy vibrations ball milling be medium ball milling 6 ~ 8h with the absolute ethyl alcohol; Compound is dry 5 ~ 8h in vacuum drying oven, prepares alloy powder;
3, vacuum reaction infiltration: the porous material preform blank is put into crucible, pour alloy powder into, 1350 ~ 1450 ℃ of vacuum sinterings are incubated 1 ~ 2 hour.
Described ceramics powder is TiC, WC, Al
2O
3, TiB
2, TiCN or several kinds of ceramic phases powder mix.
Described metal powder can adopt iron powder, nickel powder or cobalt powder.
The present invention proposes stephanoporate framework vacuum reaction in infiltration technique, compare with the traditional preparation process powder metallurgical technique, its advantage is:
1, saved prior powder metallurgy compacting-come unstuck-a series of complicated technologies such as sintering.
2, through the wettability of capillary force and reaction induced improved effect molten metal of Ti-C and ceramic phase, do not have metal and ceramic phase wettability difference in the powder metallurgical sintering process and occur sweating, phenomenon such as molten metal loss.
Embodiment
Embodiment 1:Fe-Cr-C alloy powder infiltration Ni-Ti-TiC stephanoporate framework
1, takes by weighing 100g TiC-10Ni-50Ti powder mix (mean particle size 50 μ m, granularity is less than 100 μ m), add 60g sucrose powder (mean particle size 150 μ m, granularity is less than 300 μ m), uniform mixing, preparation compound;
2, adopt gel injection toluene-HEMA gelling system that compound is molded the base substrate of designated shape, dry then 6 ~ 8h prepares the stephanoporate framework preform blank.
3, take by weighing the 370g electrolytic iron powder, the 12.5g Graphite Powder 99,10 g chromium powder high energy vibrations ball milling 8h uses absolute ethyl alcohol to be medium, and drying and screening is prepared alloy powder then.
4, alloy powder and stephanoporate framework preform blank are put into ceramic crucible, in vacuum oven, heat infiltration, 1400 ℃ of insulation 2h finally prepare the TiC metal-base composites that disperse distributes in iron alloy.
Embodiment 2:Fe-Cr-C alloy powder infiltration Ni-Ti-WC stephanoporate framework
1, takes by weighing 100g WC-10Ni-50Ti powder mix (mean particle size 50 μ m, granularity is less than 100 μ m), add 55g sucrose powder (mean particle size 150 μ m, granularity is less than 300 μ m), uniform mixing, preparation compound;
2, adopt gel injection toluene-HEMA gelling system that compound is molded the base substrate of designated shape, dry then 6 ~ 8h prepares the stephanoporate framework preform blank.
3, take by weighing the 450g electrolytic iron powder, the 12.5g Graphite Powder 99,13g chromium powder high energy vibrations ball milling 8h uses absolute ethyl alcohol to be medium, and drying and screening is prepared alloy powder then.
4, alloy powder and stephanoporate framework preform blank are put into ceramic crucible, in vacuum oven, heat infiltration, 1370 ℃ of insulation 2h finally prepare TiC and the WC metal-base composites that disperse distributes in iron alloy.
Embodiment 3:Fe-Cr-C alloy powder infiltration Ni-Ti-Al
2O
3Stephanoporate framework
1, takes by weighing 100g Al
2O
3-10Ni-50Ti powder mix (mean particle size 50 μ m, granularity is less than 100 μ m) adds 42g sucrose powder (mean particle size 150 μ m, granularity is less than 300 μ m), uniform mixing, preparation compound;
2, adopt gel injection toluene-HEMA gelling system that compound is molded the base substrate of designated shape, dry then 6 ~ 8h prepares the stephanoporate framework preform blank.
3, take by weighing the 410g electrolytic iron powder, the 12.5g Graphite Powder 99,11g chromium powder high energy vibrations ball milling 8h uses absolute ethyl alcohol to be medium, and drying and screening is prepared alloy powder then.
4, alloy powder and stephanoporate framework preform blank are put into ceramic crucible, in vacuum oven, heat infiltration, 1410 ℃ of insulation 2h finally prepare TiC and Al
2O
3The metal-base composites that disperse distributes in iron alloy.
Claims (3)
1. metal-base composites preparation method is characterized in that:
Step 1, the preparation of porous material preform blank: is raw material in ceramics powder and the granularity of 1 ~ 10 μ m at 10 ~ 50 μ m nickel powders in 10 ~ 50 μ m titanium valves, granularity with granularity; Massfraction is respectively 5 ~ 55wt%, 40 ~ 90wt%, 5 ~ 20wt%, and adopting common rolling ball milling is medium with toluene, ball milling 5 ~ 10h; Compound is dry 5 ~ 8h in vacuum drying oven; Compound adopts gel injection toluene-Rocryl 400 gelling system moulding, does pore-forming material with the sucrose of granularity 100 ~ 300 μ m, and add-on is the 10 ~ 90vol.% that accounts for the base substrate volume(tric)fraction; Base substrate is dry 5 ~ 10h in vacuum drying oven, prepares the porous material preform blank;
The preparation of step 2, alloy powder: is raw material in Graphite Powder 99 and the granularity of 5 ~ 10 μ m at 10 ~ 50 μ m chromium powders in metal powder, the granularity of 10 ~ 50 μ m with granularity; Massfraction is respectively 70 ~ 98wt%, 0.1 ~ 10wt%, 1 ~ 29.9wt%; Adopting high energy vibrations ball milling is medium ball milling 6 ~ 8h with the absolute ethyl alcohol; Compound is dry 5 ~ 8h in vacuum drying oven, prepares alloy powder;
Step 3, vacuum reaction infiltration: the porous material preform blank is put into crucible, pour alloy powder into, the mass ratio of alloy powder and preform blank is 0.5 ~ 2, and 1350 ~ 1450 ℃ of vacuum sinterings are incubated 1 ~ 2 hour, prepare matrix material.
2. metal-base composites preparation method as claimed in claim 1 is characterized in that: described ceramics powder is TiC, WC, Al
2O
3, TiB
2Or the mixing of one or more materials among the TiCN.
3. metal-base composites preparation method as claimed in claim 1 is characterized in that: described metal powder is the powder mix of one or more materials in iron powder, nickel powder or the cobalt powder.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103302268A (en) * | 2013-06-27 | 2013-09-18 | 重庆罗曼耐磨材料有限公司 | Preparation method of ceramic-metal compound wear-resistant material |
| CN104141063A (en) * | 2014-07-31 | 2014-11-12 | 重庆大学 | Preparing method of in-situ synthesis titanium carbide enhanced titanium-based multi-hole materials |
| CN104311116A (en) * | 2014-10-21 | 2015-01-28 | 武汉科技大学 | Magnesium aluminate spinel foam ceramic and preparation method thereof |
| CN107406927A (en) * | 2015-03-20 | 2017-11-28 | 哈利伯顿能源服务公司 | The metal-matrix composite strengthened using refractory metal |
| CN108044091A (en) * | 2017-12-07 | 2018-05-18 | 北京科技大学 | A kind of preparation of high-Nb Ti-Al base porous compound material filtration membrane and application process |
| CN111334696A (en) * | 2020-04-13 | 2020-06-26 | 山东交通学院 | TiC-based porous composite material and preparation method thereof |
| CN113174542A (en) * | 2021-04-20 | 2021-07-27 | 天泽思创(武汉)智能交通科技有限公司 | Multiphase ceramic particle dispersion reinforced iron-based composite material and preparation method thereof |
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| CN101168805A (en) * | 2007-11-09 | 2008-04-30 | 西安交通大学 | Method for preparing ceramic reinforced metal-based porous composite material |
| CN101899586A (en) * | 2010-07-23 | 2010-12-01 | 西安交通大学 | Preparation process of composite preform |
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Patent Citations (2)
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| CN101168805A (en) * | 2007-11-09 | 2008-04-30 | 西安交通大学 | Method for preparing ceramic reinforced metal-based porous composite material |
| CN101899586A (en) * | 2010-07-23 | 2010-12-01 | 西安交通大学 | Preparation process of composite preform |
Non-Patent Citations (3)
| Title |
|---|
| K. LEMSTER ET AL.: "Activation of alumina foams for fabricating MMCs by pressureless infiltration", 《CERAMICS INTERNATIONAL》, vol. 33, 11 September 2006 (2006-09-11), pages 1179 - 1185 * |
| K. LEMSTER ET AL.: "Processing and microstructure of metal matrix composites prepared by pressureless Ti-activated infiltration using Fe-base and Ni-base alloys", 《MATERIALS SCIENCE AND ENGINEERING A》, vol. 393, 31 December 2005 (2005-12-31), pages 229 - 238 * |
| 高明霞等: "自发熔渗法制备TiC/NiAl复合材料和其微观组织特征", 《复合材料学报》, vol. 21, no. 5, 31 October 2004 (2004-10-31), pages 11 - 15 * |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103302268A (en) * | 2013-06-27 | 2013-09-18 | 重庆罗曼耐磨材料有限公司 | Preparation method of ceramic-metal compound wear-resistant material |
| CN104141063A (en) * | 2014-07-31 | 2014-11-12 | 重庆大学 | Preparing method of in-situ synthesis titanium carbide enhanced titanium-based multi-hole materials |
| CN104141063B (en) * | 2014-07-31 | 2015-12-09 | 重庆大学 | A kind of fabricated in situ titanium carbide strengthens the preparation method of titanium based porous materials |
| CN104311116A (en) * | 2014-10-21 | 2015-01-28 | 武汉科技大学 | Magnesium aluminate spinel foam ceramic and preparation method thereof |
| CN104311116B (en) * | 2014-10-21 | 2016-07-13 | 武汉科技大学 | A kind of magnesium aluminate spinel foamed ceramics and preparation method thereof |
| CN107406927B (en) * | 2015-03-20 | 2019-04-26 | 哈利伯顿能源服务公司 | The metal-matrix composite reinforced using refractory metal |
| CN107406927A (en) * | 2015-03-20 | 2017-11-28 | 哈利伯顿能源服务公司 | The metal-matrix composite strengthened using refractory metal |
| US10208366B2 (en) | 2015-03-20 | 2019-02-19 | Halliburton Energy Service, Inc. | Metal-matrix composites reinforced with a refractory metal |
| CN108044091A (en) * | 2017-12-07 | 2018-05-18 | 北京科技大学 | A kind of preparation of high-Nb Ti-Al base porous compound material filtration membrane and application process |
| CN108044091B (en) * | 2017-12-07 | 2019-12-31 | 北京科技大学 | Preparation and application methods of high-niobium titanium-aluminum-based porous composite material filter membrane |
| CN111334696A (en) * | 2020-04-13 | 2020-06-26 | 山东交通学院 | TiC-based porous composite material and preparation method thereof |
| CN113174542A (en) * | 2021-04-20 | 2021-07-27 | 天泽思创(武汉)智能交通科技有限公司 | Multiphase ceramic particle dispersion reinforced iron-based composite material and preparation method thereof |
| CN113174542B (en) * | 2021-04-20 | 2023-10-27 | 天泽思创(武汉)智能交通科技有限公司 | Multiphase ceramic particle dispersion reinforced iron-based composite material and preparation method thereof |
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