CN102400001A - Method for preparing granule reinforced aluminum-based composite material of in-situ intermetallic compound - Google Patents

Method for preparing granule reinforced aluminum-based composite material of in-situ intermetallic compound Download PDF

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CN102400001A
CN102400001A CN2011103952968A CN201110395296A CN102400001A CN 102400001 A CN102400001 A CN 102400001A CN 2011103952968 A CN2011103952968 A CN 2011103952968A CN 201110395296 A CN201110395296 A CN 201110395296A CN 102400001 A CN102400001 A CN 102400001A
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intermetallic compound
powder
compound particle
reinforced aluminum
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CN102400001B (en
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王洪涛
纪岗昌
陈枭
董增祥
白小波
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Jiujiang University
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Abstract

The invention discloses a method for preparing a granule reinforced aluminum-based composite material of an in-situ intermetallic compound, and belongs to the field of metal-based composite materials. The method comprises the following steps of: mixing M metal powder and Al alloy powder which can form the intermetallic compound according to a ratio; preparing M(Al) solid solution alloy powder by mechanical alloying, and mixing the M(Al) powder, Al and Al alloy powder according to a ratio; preparing a coating layer by using a novel cold spraying forming technology; and converting an M(Al) solid solution into an M-Al intermetallic compound in situ through heat treatment, and thus obtaining the granule reinforced aluminum-based composite material of the in-situ intermetallic compound. The method has a simple process, a short production period and low production cost, and the compatibility of granular reinforcement and a matrix is high, so industrial application is facilitated.

Description

A kind of preparation method of original position intermetallic compound particle reinforced aluminum matrix composites
Technical field
The invention belongs to metal-base composites and manufacturing technology field; A kind of original position intermetallic compound particle reinforced aluminum matrix composites and preparation method thereof particularly is provided, and is that cold spraying forming technique and thermal treatment recombining process prepare original position intermetallic compound particle reinforced aluminum matrix composites.
Background technology
Aluminum matrix composite has excellent, low thermal expansivity of light weight, specific tenacity height, thermostability and electrical and thermal conductivity and good series of advantages such as wear resistance, has wide application background in fields such as national defence, aerospace, automobile, electronics, communications and transportation, civilian machineries.And particle enhanced aluminum-based composite material strengthens because of it has that the body cost is low, material property isotropy, preparation technology and equipment requirements are lower, is convenient to advantages such as batch process, has wide IP prospecting.At present, the enhanced granule of aluminum matrix composite is main with ceramic-like (like oxide compound, nitride, carbide etc.) particle, like SiC, A1 2O 3, A1N, B 4C etc., its advantage is that density is low, hardness is high.But ceramic particle reinforced aluminium base composite material exists ceramic particle to strengthen that wellability is poor between body and the aluminum substrate, the interface combines bad and particle problem such as skewness in matrix, thereby has influenced the performance of the comprehensive mechanical property of aluminum matrix composite.
Intermetallic compound is a kind of high-temperature structural material, and Young's modulus, fusing point and hot strength are very high.It had both had the character of metal; Like metalluster, electroconductibility, thermal conductivity etc.; The character that has certain pottery again; Like higher specific tenacity and specific rigidity, and between alloy and pottery high use temperature and thermal expansivity, these characteristics make it become the effective wild phases of light metal material such as duraluminum.In addition; Intermetallic compound has good plasticity-with respect to pottery, thereby when improving matrix alloy intensity, can not reduce its plasticity; And between in-situ authigenic metal compound particle the crystalline structure matching with matrix alloy is good especially, interface bond strength is high.The above provides the foundation for original position intermetallic compound particle reinforced aluminum matrix composites has good comprehensive performances.At present; Original position intermetallic compound particle reinforced aluminum matrix composites preparation method mainly is liquid phase process such as stirring casting, liquid metal infiltration, extrusion casting; Its process mainly is that to generate Al-M with reactive aluminum be the intermetallic disperse phase through pure metal powder being added in the molten aluminium, thus reinforced aluminum matrix composites.But these class methods preparation technology and complex equipments, the production cycle is long, and cost is higher, is easy to occur casting flaw (gas be mingled with) in the production process, and temperature is selected the improper segregation that is prone to cause.Therefore, it is simple, quick to propose a kind of technology, and the technology of preparing of original position intermetallic compound particle reinforced aluminum matrix composites with low cost is necessary.
Summary of the invention
The objective of the invention is to overcome the deficiency of prior art, provide a kind of technology simple, reliable, and the preparation method of the original position intermetallic compound particle reinforced aluminum matrix composites that is easy to apply.The method that the present invention proposes helps controlling size, volume(tric)fraction and the distribution of intermetallic compound particle, the even zero defect of prepared aluminum matrix composite, and technology is simple, with low cost, reproducible utilization, is particularly suitable for industrialization promotion and uses.
The present invention realizes through following technical scheme:
A kind of preparation method of original position intermetallic compound particle reinforced aluminum matrix composites is characterized in that, carries out according to the following steps:
Figure 2011103952968100002DEST_PATH_IMAGE001
is with metal-powder M and Al powder; Carry out proportioning (at. is an atomic percent) by the M of 75～25at.% and the Al of 25～75at.%, under inert atmosphere, low temperature or vacuum, carry out prepared by mechanical alloy M (Al) solid solution alloy powder then;
Figure 267819DEST_PATH_IMAGE002
carries out sub-sieve with above-mentioned M (Al) solid solution alloy powder, obtains the different-grain diameter powder;
Figure 2011103952968100002DEST_PATH_IMAGE003
mixes by the M (Al) of 5～60vol.% and Al and the alloy proportion thereof of 95～40vol.% different-grain diameter M (Al) solid solution alloy powder and Al or Al alloy powder in the ball mill mixing machine;
Figure 226416DEST_PATH_IMAGE004
carries out the sandblast roughening treatment in tabular or bar-shaped matrix surface;
Figure 2011103952968100002DEST_PATH_IMAGE005
adopts cold spraying on above-mentioned matrix, to spray the powder that step (3) is prepared; Powder sending quantity 50～100g/min, coat thickness 300 μ m～50mm;
Figure 114738DEST_PATH_IMAGE006
heat-treats under vacuum or inert gas environment the coat that step (5) obtains; 450～650 ℃ of temperature; 1～8 hour time, obtain original position M-Al intermetallic compound particle reinforced aluminum matrix composites.
When matrix need be peeled off, should matrix be peeled off before the thermal treatment of step (6).
Other characteristics of the present invention are:
Described original position intermetallic compound particle reinforced aluminum matrix composites and preparation method thereof; Form by strengthening body and matrix alloy, described matrix alloy is aluminium and duraluminum, and said enhancing body is the intermetallic compound particle of in-situ authigenic; It accounts for TV 5～60%, and all the other are matrix alloy.
Described original position intermetallic compound particle reinforced aluminum matrix composites and preparation method thereof, metal-powder M can be one or more in the metals such as Fe, Ti, Ni, Cu, Co.
Described original position intermetallic compound particle reinforced aluminum matrix composites and preparation method thereof, it can be MAl, M that said M-Al intermetallic compound particle strengthens body 3Al, M 2Al 5, MAl 3Deng in the intermetallic compound one or more.
Described original position intermetallic compound particle reinforced aluminum matrix composites and preparation method thereof, the M (Al) in the step (1) is the solid solution alloy powder;
Described original position intermetallic compound particle reinforced aluminum matrix composites and preparation method thereof can directly deposit coat to the matrix sandblast during preparation bulk;
Described original position intermetallic compound particle reinforced aluminum matrix composites and preparation method thereof should be peeled off matrix in the thermal treatment of step (6) when the preparation bulk before;
Described original position intermetallic compound particle reinforced aluminum matrix composites and preparation method thereof, the size and the volume(tric)fraction of intermetallic compound particle are controlled.
Compared with prior art, beneficial effect of the present invention is,
Original position intermetallic compound particle reinforced aluminum matrix composites that the present invention proposes and preparation method thereof; Can control weave construction, particle size and the volume(tric)fraction of intermetallic compound particle reinforced aluminum matrix composites through regulating material composition, granularity, mechanical alloy metallization processes, cold spray process and kinds of processes parameters such as thermal treatment temp and time; Intermetallic compound enhanced granule original position generates; Surface cleaning, good with matrix bond, technology is simple; With short production cycle, with low cost being easy to applied.
Description of drawings
Fig. 1 process flow sheet of the present invention.
Embodiment
Below make specific embodiment the present invention is further described, but the present invention is not limited to these instances according to technical scheme of the present invention.
Embodiment 1:
Choose Fe powder and the Al powder of granularity less than 50 μ m, according to mol ratio 50:50 proportioning, powder morphology is as shown in Figure 2.In planetary ball mill, carry out mechanical alloying, ball-to-powder weight ratio is 15: 1, and the ball milling time is 24h, and rotating speed 180 rpm obtain Fe (Al) solid solution alloy powder, and the powder fractography is as shown in Figure 3.With Fe (Al) solid solution alloy powder and pure Al powder by volume Al:Fe (Al)=50:50 in the ball mill mixing machine, mix; Cold spraying deposits coat then; Matrix is 40mm * 25mm * 3mm duraluminum, before the spraying matrix surface is adopted the sandblasting of 24 orders palm fibre corundum, and spraying gas is N 2Gas, wherein, accelerating gas pressure 1.0MPa; Powder feeding gas pressure 1.2MPa, 350 ℃ of spraying temperatures, powder feeding rate 50g/min; Spray distance 20mm, spray gun translational speed 50mm/s is about the about 20mm of coat thickness; Its tissue can see shown in Fig. 4 (a), disperse white Fe (Al) the solid solution alloy particle that distributing on the aluminum substrate of black.Peel off matrix after the spraying, in vacuum oven, heat-treat, vacuum tightness 3 * 10 -3Pa rises to 500 ℃ with the speed of 5 ℃/s, is incubated 5 hours; Cool to room temperature with the furnace; Obtain original position FeAl intermetallic compound particle reinforced aluminum matrix composites, its tissue can be seen shown in Fig. 4 (b); Also there is a small amount of not white Fe (Al) solid solution alloy particle of complete reaction simultaneously in the gray FeAl intermetallic compound particle that on the Al of black matrix, distributing.
Embodiment 2:
Choose granularity less than the Fe powder of 25 μ m and granularity less than the Al powder of 10 μ m, according to mol ratio 75:25 proportioning, in planetary ball mill, carry out mechanical alloying; Ball-to-powder weight ratio is 10: 1, and the ball milling time is 12h, rotating speed 200 rpm; Obtain Fe (Al) solid solution alloy powder; With itself and pure Al powder by volume Al:Fe (Al)=75:25 in the ball mill mixing machine, mix, cold spraying deposition coat then, matrix is 40mm * 25mm * 3mm soft steel; Before the spraying matrix surface is adopted the sandblasting of 100 orders palm fibre corundum, spraying gas is N 2Gas, wherein, accelerating gas pressure 2.0MPa, powder feeding gas pressure 2.2MPa, 400 ℃ of spraying temperatures, about powder feeding rate 70g/min, spray distance 20mm, spray gun translational speed 20mm/s, coat thickness 40mm.Peel off matrix after the spraying, in the tube furnace of argon shield that flows, heat-treat, rise to 450 ℃, be incubated 5 hours, cool to room temperature with the furnace, acquisition Fe with the speed of 10 ℃/s 2Al 5The intermetallic compound particle reinforced aluminum matrix composites.
Embodiment 3:
Choose Ni powder and the Al powder of granularity,, in planetary ball mill, carry out mechanical alloying according to mol ratio 75:25 proportioning less than 25 μ m; Ball-to-powder weight ratio is 20: 1, and the ball milling time is 24h, rotating speed 180 rpm; Obtain Ni (Al) solid solution alloy powder; With itself and pure Al powder by volume Al:Ni (Al)=80:20 in the ball mill mixing machine, mix, cold spraying deposition coat then, matrix is 40mm * 25mm * 3mm soft steel; Before the spraying matrix surface is adopted the sandblasting of 150 orders palm fibre corundum, spraying gas is N 2Gas, wherein, accelerating gas pressure 2MPa, powder feeding gas pressure 2.2MPa, 500 ℃ of spraying temperatures, about powder feeding rate 50g/min, spray distance 20mm, spray gun translational speed 30mm/s, coat thickness 20mm.Peel off matrix after the spraying, in the tube furnace of argon shield that flows, heat-treat, rise to 550 ℃, be incubated 5 hours, cool to room temperature with the furnace, acquisition NiAl with the speed of 10 ℃/s 3The intermetallic compound particle reinforced aluminum matrix composites.
Embodiment 4:
Choose Ti powder and granularity 5～10 μ m Al powder of granularity less than 45 μ m, according to mol ratio 50:50 proportioning, in planetary ball mill, carry out mechanical alloying, ball-to-powder weight ratio is 10: 1; The ball milling time is 12h, and rotating speed 200 rpm obtain Ti (Al) solid solution alloy powder, with itself and pure Al powder by volume Al:Ti (Al)=60:40 in the ball mill mixing machine, mix; Cold spraying deposits coat then, and matrix is 40mm * 25mm * 3mm soft steel, before the spraying matrix surface is adopted the sandblasting of 150 orders palm fibre corundum; Spraying gas is He gas, wherein, and accelerating gas pressure 1.5MPa; Powder feeding gas pressure 1.7MPa, 350 ℃ of spraying temperatures are about powder feeding rate 40g/min; Spray distance 20mm, spray gun translational speed 40mm/s, coat thickness 20mm.Peel off matrix after the spraying, in vacuum oven, heat-treat, vacuum tightness 3 * 10 -3Pa rises to 650 ℃ with the speed of 5 ℃/s, is incubated 5 hours, cools to room temperature with the furnace, obtains TiAl intermetallic compound particle reinforced aluminum matrix composites.

Claims (8)

1. the preparation method of an original position intermetallic compound particle reinforced aluminum matrix composites is characterized in that concrete steps are following:
Figure 2011103952968100001DEST_PATH_IMAGE001
is with metal-powder M and Al powder; Carry out proportioning (at. is an atomic percent) by the M of 75～25at.% and the Al of 25～75at.%, under inert atmosphere, low temperature or vacuum, carry out prepared by mechanical alloy M (Al) solid solution alloy powder then;
Figure 202627DEST_PATH_IMAGE002
carries out sub-sieve with above-mentioned M (Al) solid solution alloy powder, obtains the different-grain diameter powder;
mixes by the M (Al) of 5～60vol.% and Al and the alloy proportion thereof of 95～40vol.% different-grain diameter M (Al) solid solution alloy powder and Al or Al alloy powder in the ball mill mixing machine;
Figure 492794DEST_PATH_IMAGE004
carries out the sandblast roughening treatment in tabular or bar-shaped matrix surface;
Figure 2011103952968100001DEST_PATH_IMAGE005
adopts cold spraying on above-mentioned matrix, to spray the powder that step (3) is prepared; Powder sending quantity 50～100g/min, coat thickness 300 μ m～50mm;
Figure 622293DEST_PATH_IMAGE006
heat-treats under vacuum or inert gas environment the coat that step (5) obtains; 450～650 ℃ of temperature; 1～8 hour time, obtain original position M-Al intermetallic compound particle reinforced aluminum matrix composites.
2. the preparation method of a kind of original position intermetallic compound particle reinforced aluminum matrix composites according to claim 1; It is characterized in that; Original position intermetallic compound particle reinforced aluminum matrix composites is formed by strengthening body and matrix alloy, and described matrix alloy is aluminium and duraluminum, and said enhancing body is the intermetallic compound particle of in-situ authigenic; It accounts for TV 5～60%, and all the other are matrix alloy.
3. the preparation method of a kind of original position intermetallic compound particle reinforced aluminum matrix composites according to claim 1 is characterized in that, metal-powder M is one or more in Fe, Ti, Ni, Cu, the Co metal.
4. the preparation method of a kind of original position intermetallic compound particle reinforced aluminum matrix composites according to claim 1 is characterized in that, it is MAl, M that said M-Al intermetallic compound particle strengthens body 3Al, M 2Al 5, MAl 3In the intermetallic compound one or more.
5. the preparation method of a kind of original position intermetallic compound particle reinforced aluminum matrix composites according to claim 1 is characterized in that, the M (Al) in the step (1) is the solid solution alloy powder.
6. the preparation method of a kind of original position intermetallic compound particle reinforced aluminum matrix composites according to claim 1 is characterized in that, need not directly deposit coat to the matrix sandblast during preparation bulk.
7. the preparation method of a kind of original position intermetallic compound particle reinforced aluminum matrix composites according to claim 1 is characterized in that, when the preparation bulk, matrix is peeled off in the thermal treatment of step (6) before.
8. the preparation method of a kind of original position intermetallic compound particle reinforced aluminum matrix composites according to claim 1 is characterized in that, the size and the volume(tric)fraction of intermetallic compound particle are controlled.
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Cited By (11)

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CN102921361A (en) * 2012-09-25 2013-02-13 中国科学院金属研究所 Intermetallic compound with micro-channel structure and preparation method thereof
CN103898343A (en) * 2013-12-26 2014-07-02 中北大学 Method for preparing aluminum-rich intermetallic compound reinforced aluminum-based composite material
CN103921493A (en) * 2014-04-16 2014-07-16 同济大学 Aluminium alloy substrate/NiAL coating composite material and preparation method thereof
CN104870113A (en) * 2012-10-30 2015-08-26 海德鲁铝业钢材有限公司 Aluminum composite material and forming method
CN106916984A (en) * 2017-03-13 2017-07-04 湖州师范学院 A kind of inertia multilevel hierarchy tungsten aluminium composite material and preparation method thereof
CN108778595A (en) * 2016-03-02 2018-11-09 德仕托金属有限公司 Increasing material manufacturing is carried out with metallic composite
CN108866536A (en) * 2018-06-26 2018-11-23 新余学院 A kind of nanometer crystalline Ni Al/Ni of fabricated in situ3The preparation method of compound coat between Al bimetallic
CN110168140A (en) * 2017-01-17 2019-08-23 国立大学法人信州大学 The manufacturing method of ceramic circuit board
CN110545943A (en) * 2017-04-27 2019-12-06 小岩井株式会社 High-strength aluminum alloy laminate molding and method for producing same
CN110964951A (en) * 2019-12-27 2020-04-07 成都航空职业技术学院 Fe-C-Ti/ZL108 composite material and preparation method thereof
CN115505798A (en) * 2022-06-22 2022-12-23 安徽工程大学 Spherical intermetallic compound particle reinforced aluminum matrix composite and preparation method thereof

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CN101058881A (en) * 2007-06-04 2007-10-24 西安交通大学 Method for preparing compound coat between metals
CN102154640A (en) * 2011-03-16 2011-08-17 上海交通大学 Method for enhancing bonding strength of aluminum coating

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WO2006109956A1 (en) * 2005-04-15 2006-10-19 Snt Co., Ltd Method of preparing metal matrix composite and coating layer and bulk prepared thereby
CN101058881A (en) * 2007-06-04 2007-10-24 西安交通大学 Method for preparing compound coat between metals
CN102154640A (en) * 2011-03-16 2011-08-17 上海交通大学 Method for enhancing bonding strength of aluminum coating

Cited By (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102921361B (en) * 2012-09-25 2015-09-02 中国科学院金属研究所 A kind of intermetallic compound and manufacture method thereof with micro-channel structure
CN102921361A (en) * 2012-09-25 2013-02-13 中国科学院金属研究所 Intermetallic compound with micro-channel structure and preparation method thereof
US9855592B2 (en) 2012-10-30 2018-01-02 Hydro Aluminium Rolled Products Gmbh Aluminium composite material and forming method
CN104870113A (en) * 2012-10-30 2015-08-26 海德鲁铝业钢材有限公司 Aluminum composite material and forming method
CN104870113B (en) * 2012-10-30 2017-02-22 海德鲁铝业钢材有限公司 Aluminum composite material and forming method
US10279385B2 (en) 2012-10-30 2019-05-07 Hydro Aluminium Rolled Products Gmbh Aluminum composite material and forming method
CN103898343B (en) * 2013-12-26 2016-05-04 中北大学 A kind of rich Al intermetallic reinforced aluminum matrix composites preparation method
CN103898343A (en) * 2013-12-26 2014-07-02 中北大学 Method for preparing aluminum-rich intermetallic compound reinforced aluminum-based composite material
CN103921493A (en) * 2014-04-16 2014-07-16 同济大学 Aluminium alloy substrate/NiAL coating composite material and preparation method thereof
CN108778595A (en) * 2016-03-02 2018-11-09 德仕托金属有限公司 Increasing material manufacturing is carried out with metallic composite
CN110168140A (en) * 2017-01-17 2019-08-23 国立大学法人信州大学 The manufacturing method of ceramic circuit board
CN110168140B (en) * 2017-01-17 2021-07-30 国立大学法人信州大学 Method for manufacturing ceramic circuit board
CN106916984A (en) * 2017-03-13 2017-07-04 湖州师范学院 A kind of inertia multilevel hierarchy tungsten aluminium composite material and preparation method thereof
CN110545943A (en) * 2017-04-27 2019-12-06 小岩井株式会社 High-strength aluminum alloy laminate molding and method for producing same
CN108866536A (en) * 2018-06-26 2018-11-23 新余学院 A kind of nanometer crystalline Ni Al/Ni of fabricated in situ3The preparation method of compound coat between Al bimetallic
CN108866536B (en) * 2018-06-26 2020-06-16 新余学院 In-situ synthesized nanocrystalline NiAl/Ni3Preparation method of Al bimetal compound coating
CN110964951A (en) * 2019-12-27 2020-04-07 成都航空职业技术学院 Fe-C-Ti/ZL108 composite material and preparation method thereof
CN115505798A (en) * 2022-06-22 2022-12-23 安徽工程大学 Spherical intermetallic compound particle reinforced aluminum matrix composite and preparation method thereof

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