CN101067188A - In-situ endogenic Al3 Ti reinforced Mg-based composite material and producing method - Google Patents
In-situ endogenic Al3 Ti reinforced Mg-based composite material and producing method Download PDFInfo
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- CN101067188A CN101067188A CN 200710023304 CN200710023304A CN101067188A CN 101067188 A CN101067188 A CN 101067188A CN 200710023304 CN200710023304 CN 200710023304 CN 200710023304 A CN200710023304 A CN 200710023304A CN 101067188 A CN101067188 A CN 101067188A
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- 239000002131 composite material Substances 0.000 title claims abstract description 32
- 238000011065 in-situ storage Methods 0.000 title claims abstract description 16
- 238000000034 method Methods 0.000 title description 10
- 239000000843 powder Substances 0.000 claims abstract description 36
- 238000005245 sintering Methods 0.000 claims abstract description 21
- 238000006243 chemical reaction Methods 0.000 claims abstract description 20
- 238000002360 preparation method Methods 0.000 claims abstract description 11
- 238000003723 Smelting Methods 0.000 abstract 1
- 238000000498 ball milling Methods 0.000 abstract 1
- 239000008187 granular material Substances 0.000 abstract 1
- 239000011777 magnesium Substances 0.000 description 53
- 239000011159 matrix material Substances 0.000 description 26
- 229910052749 magnesium Inorganic materials 0.000 description 21
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 19
- 239000000203 mixture Substances 0.000 description 17
- 239000000463 material Substances 0.000 description 13
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 10
- 229910000765 intermetallic Inorganic materials 0.000 description 9
- 239000002245 particle Substances 0.000 description 9
- 239000000919 ceramic Substances 0.000 description 8
- 238000005516 engineering process Methods 0.000 description 7
- 229910052786 argon Inorganic materials 0.000 description 5
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 4
- 238000001816 cooling Methods 0.000 description 4
- 238000000227 grinding Methods 0.000 description 4
- 238000009702 powder compression Methods 0.000 description 4
- 238000002791 soaking Methods 0.000 description 4
- 229910018575 Al—Ti Inorganic materials 0.000 description 3
- 230000002708 enhancing effect Effects 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000004134 energy conservation Methods 0.000 description 2
- 238000003786 synthesis reaction Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000003912 environmental pollution Methods 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 230000001902 propagating effect Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000001308 synthesis method Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 238000009736 wetting Methods 0.000 description 1
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Abstract
The present invention is Mg-base composite material reinforced with in-situ endogenetic Al3Ti and its preparation process, and belongs to the field of granular material reinforced metal-base composite material. The Mg-base composite material reinforced with in-situ endogenetic Al3Ti is prepared with Mg powder 49.39-91.27 wt%, Al powder 5.49-34.34 wt%, and Ti powder 3.24-16.25 wt%, and through ball milling, pressing into prefabricated block, vacuum stoving, and final reaction and sintering at temperature higher than the smelting point of Mg (648.8 deg.c) to obtain the Mg-base composite material reinforced with in-situ endogenetic Al3Ti in 5-30 vol%. The Mg-base composite material has high strength, high rigidity, high size stability and other advantages.
Description
Technical field
The present invention relates to the particles reiforced metal-base composition preparing technical field, refer in particular to a kind of in-situ endogenic Al
3Ti strengthens Mg based composites and preparation method.
Background technology
Along with developing rapidly of modern industry, reduction energy consumption and minimizing environmental pollution have become the 21st century mankind and have faced problem anxious to be solved, press for light weight, type material that intensity is high, single magnesium alloy materials since room temperature and hot strength is low, wearability difference etc. more and more be difficult to meet the demands.Therefore, discontinuous phase enhancing magnesium base composite material has a wide range of applications at aspects such as space flight, aviation, national defence, automobiles because of its low density, high specific tenacity, specific rigidity and high wear resistance.
For a long time, the preparation technology of light-weight metal based composites is laid particular emphasis on the method that strengthens body and matrix bond that adds always, not only complex process, cost are higher, and have between enhancing body and the matrix that wetting property is poor, the interface combines problems such as bad.Development in recent years a kind of novel method-reaction in synthesis method for preparing metal-base composites, this method is under certain condition, by between the element or the chemical reaction between element and the compound, the wild phase of synthetic one or more high rigidity of original position, high elastic coefficient in metal, thus reach the purpose of strengthening matrix metal.
Wild phase is except that minority adopts B, Ti and C (graphite) in the discontinuous phase enhancing magnesium base composite material, and great majority adopt ceramic particles as wild phase, as utilize SiC, ZrC, TiC, Mg
2Si, TiB
2, ZrB
2Deng (Chinese patent, the patent No. is: 03116168.5; 03116169.3).Because magnesium is poor to the ceramic enhancement phase wettability, and the thermal expansivity of magnesium matrix and ceramic enhancement phase, heat conductivity differ greatly, and has very big residual thermal stress between the two.In addition, the temperature that the reaction in of ceramic phase needs is higher, the time is long, and often reaction not exclusively.More than these all produce adverse influence to the preparation of magnesium base composite material and performance.
Intermetallic compound is identical with ceramic phase, has high hardness, low density, high hot strength and thermostability, also has and good wettability of magnesium liquid and thermal expansivity and the thermal conductivity close with magnesium.Therefore, adopt intermetallic compound enhanced magnesium base composite material, not only improve room temperature strength and hot strength, also help to reduce infringement plasticity.In addition, the temperature that the reaction in of intermetallic compound phase needs is lower, can simplify the preparation technology of matrix material.
The in-situ endogenic reaction sintering technology that the present invention adopts is given birth to synthetic and powder metallurgy sintered the combining of self propagating high temperature burning intermetallic compound in making and is strengthened magnesium base composite material, has advantages such as energy-conservation, material-saving, technology be easy.Do not see as yet both at home and abroad that at present adopting Mg-Al-Ti is patent or the research report that the in-situ endogenic reaction process prepares magnesium base composite material.
Summary of the invention
The purpose of this invention is to provide a kind of in-situ endogenic Al
3Ti strengthens Mg based composites and preparation method, solved that the original position synthesize ceramic strengthens in the magnesium base composite material mutually because ceramic phase and magnesium wettability difference and difference of thermal expansion coefficients are excessive, and problem such as the synthesis technique of the magnesium base composite material that problem caused such as interior living ceramic phase synthesis temperature height is wayward and performance is impaired.Adopt the synthetic in-situ endogenic intermetallic compound of reaction sintering technology to strengthen magnesium base composite material among the present invention, have high specific strength, specific rigidity, high temperature creep property and dimensional stability, have advantages such as energy-conservation, material-saving, technology be easy, prospects for commercial application is wide.
Matrix magnesium has low fusing point and density, also has good conduction, heat conduction and hot and cold processing characteristics.Wild phase Al
3Ti has low density (3.4g/cm
3), characteristics such as high-melting-point (1613K), resistance to oxidation, hot strength height, be to have very much the matrix material ideal of application potential to strengthen body.Al
3The Ti particle strengthens the Mg based composites can improve the high-temperature behavior of matrix material when keeping the original performance of matrix, and Al
3There is the good interface consistency to guarantee the high performance of matrix material between Ti and the Mg matrix.
A kind of in-situ endogenic Al
3Ti strengthens the Mg based composites, it is characterized in that: interior living Al
3The Ti phase volume fraction is 5～30%.
Above-mentioned in-situ endogenic Al
3Ti strengthens the preparation method of Mg based composites, it is characterized in that:
1, by weight percentage, the Mg powder with 49.39%～91.27%, 5.49%～34.34% Al powder, 3.24%～16.25% Ti sphere of powder mill mixes, and is pressed into prefabricated section then;
2, prefabricated section vacuum state oven dry down;
3, prefabricated section carries out reaction sintering more than being higher than Mg fusing point (648.8 ℃).
Consider the solid solution of Al in Mg, react completely in order to guarantee the Ti powder.The add-on of Al powder is higher by 2%～10% than the calculated amount of Al powder in the step 1, and the add-on of corresponding M g powder is than calculated amount low 2%～10%.
The temperature of reaction sintering is preferred 648.8 ℃～800 ℃ in the step 3, and sintering time is l～2h.
Reaction in synthetic system Mg-Al-Ti of the present invention and synthetic Al thereof
3The Ti/Mg matrix material has following advantage:
(1) Mg-Al-Ti system reaction synthetic temperature is low, is easy to control, and reacting balance, helps industrialized application.
(2) reaction synthetic Al
3The Ti particle not only has high intensity and hardness, and particle size is about 2～4 μ m, the particle form almost spherical, and be evenly distributed in the matrix.
(3) the interface cleaning between particle and the matrix, and bonding strength height.
(4) synthetic Al
3The Ti/Mg matrix material has superior mechanical property, physicals and wear resisting property.
Description of drawings
Fig. 1 10vol.%Al
3The XRD analysis of Ti/Mg matrix material
Fig. 2 30vol.%Al
3The XRD analysis of Ti/Mg matrix material
Fig. 3 10vol.%Al
3The stereoscan photograph of Ti/Mg matrix material
Fig. 4 25vol.%Al
3The stereoscan photograph of Ti/Mg matrix material
Fig. 5 30vol.%Al
3The stereoscan photograph of Ti/Mg matrix material
Embodiment
Embodiment 1: the material of employing is Mg powder, Al powder and Ti powder, and its purity is respectively 99.99%, 99% and 99.5%, and granularity is respectively 150 orders, 200 orders and 325 orders, according to Al
3The volume fraction of Ti is that 10vol.% prepares burden, and calculating composition is: Mg 91.3wt.%, Al 5.5wt.% and Ti 6.2wt.%.Add the excessive Al powder (corresponding minimizing 10wt.%Mg powder) of 10wt.%, concrete composition is: Mg 78.3t.%, Al 15.5t.% and Ti 6.2wt.%.Mix powder 24h on horizontal ball mill, ratio of grinding media to material is 3: 1 (abrading-ball is an agate ball).Mix the back powder compression become prefabricated section, and under 100 ℃ of vacuum states dry 6h, prefabricated section carries out reaction sintering in argon shield.Sintering process is: 800 ℃ of sintering temperatures, soaking time 60min with the stove naturally cooling, prepares 10vol.%Al
3The Ti intermetallic compound strengthens magnesium base composite material.Fig. 1 is the XRD analysis of this material, and the matrix material of preparing as can be seen has only Mg and Al
3The Ti two-phase.Fig. 3 is the stereoscan photograph of this material, Al as can be seen
3The Ti wild phase is evenly distributed on the matrix.
Embodiment 2: the material of employing is Mg powder, Al powder and Ti powder, and its purity is respectively 99.99%, 99% and 99.5%, and granularity is respectively 150 orders, 200 orders and 325 orders, according to Al
3The volume fraction of Ti is that 15vol.% prepares burden, and calculating composition is: Mg 75.7wt.%, Al 15.3wt.% and Ti 9.0wt.%.Add the excessive Al powder of 7wt.%, concrete composition is: Mg 69.7wt.%, Al 21.3wt.% and Ti 9.0wt.%.Mix powder 24h on horizontal ball mill, ratio of grinding media to material is 3: 1 (abrading-ball is an agate ball).Mix the back powder compression become prefabricated section, and under 100 ℃ of vacuum states dry 6h, prefabricated section carries out reaction sintering in argon shield.Sintering process is: 660 ℃ of sintering temperatures, soaking time 90min with the stove naturally cooling, prepares 15vol.%Al
3The Ti intermetallic compound strengthens magnesium base composite material.
Embodiment 3: the material of employing is Mg powder, Al powder and Ti powder, and its purity is respectively 99.99%, 99% and 99.5%, and granularity is respectively 150 orders, 200 orders and 325 orders, according to Al
3The volume fraction of Ti is that 25vol.% prepares burden, and calculating composition is: Mg 61.4wt.%, Al 24.3wt.% and Ti 14.3wt.%.Add the excessive Al powder of 7.4wt.%, concrete composition is: Mg 54.0wt.%, Al 31.7wt.% and Ti 14.3wt.%.Mix powder 24h on horizontal ball mill, ratio of grinding media to material is 3: 1 (abrading-ball is an agate ball).Mix the back powder compression become prefabricated section, and under 100 ℃ of vacuum states dry 6h, prefabricated section carries out reaction sintering in argon shield.Sintering process is: 800 ℃ of sintering temperatures, soaking time 120min with the stove naturally cooling, prepares 25vol.%Al
3The Ti intermetallic compound strengthens magnesium base composite material.Fig. 4 is the stereoscan photograph of this matrix material, Al as can be seen
3Ti particle wild phase is evenly distributed on the matrix.
Embodiment 4: the material of employing is Mg powder, Al powder and Ti powder, and its purity is respectively 99.99%, 99% and 99.5%, and granularity is respectively 150 orders, 200 orders and 325 orders, according to Al
3The volume fraction of Ti is that 30vol.% prepares burden, and calculating composition is: Mg 56.2wt.%, Al 27.5wt.% and Ti 16.3wt.%.Add the excessive Al of 3.4wt.%, concrete composition is: Mg 52.8wt.%, Al 30.9wt.% and Ti 16.3wt.%.Mix powder 24h on ball mill, ratio of grinding media to material is 3: 1 (abrading-ball is an agate ball).Mix the back powder compression become prefabricated section, and under 100 ℃ of vacuum states dry 6h, prefabricated section carries out reaction sintering in argon shield.Sintering process is: 720 ℃ of sintering temperatures, and soaking time 120min, with the stove naturally cooling, whole process is taked argon shield, obtains 30vol.%Al
3The Ti intermetallic compound strengthens magnesium base composite material.Fig. 2 is the XRD analysis of this material, illustrates that this matrix material is by Al
3Ti and Mg two phase composites.Fig. 5 is the stereoscan photograph of this material, Al as can be seen
3The Ti particle size about 2～4 μ m, form almost spherical, and being evenly distributed on the Mg matrix.
Claims (4)
1, a kind of in-situ endogenic Al
3Ti strengthens the Mg based composites, it is characterized in that: interior living Al
3The Ti phase volume fraction is 5～30%.
2, the described a kind of in-situ endogenic Al of claim 1
3Ti strengthens the preparation method of Mg based composites, it is characterized in that:
(1) by weight percentage, the Mg powder with 49.39%～91.27%, 5.49%～34.34% Al powder, 3.24%～16.25% Ti sphere of powder mill mixes, and is pressed into prefabricated section then:
(2) prefabricated section vacuum state oven dry down;
(3) prefabricated section carries out reaction sintering more than being higher than Mg fusing point (648.8 ℃).
3, the described a kind of in-situ endogenic Al of claim 2
3Ti strengthens the preparation method of Mg based composites, and it is characterized in that: the add-on of Al powder is higher by 2%～10% than the calculated amount of Al powder in the step 1, and the add-on of Mg powder is than calculated amount low 2%～10%.
4, the described a kind of in-situ endogenic Al of claim 2
3Ti strengthens the preparation method of Mg based composites, and it is characterized in that: the temperature of reaction sintering is preferred 648.8 ℃～800 ℃ in the step 3, and sintering time is 1～2h.
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| CNB200710023304XA CN100513624C (en) | 2007-06-08 | 2007-06-08 | In-situ endogenic Al3 Ti reinforced Mg-based composite material and producing method |
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| CN100513624C CN100513624C (en) | 2009-07-15 |
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102002649A (en) * | 2010-09-16 | 2011-04-06 | 无锡南理工科技发展有限公司 | High-toughness magnesium based block body metal glass composite material and preparation method thereof |
| CN102230096A (en) * | 2011-06-27 | 2011-11-02 | 常州大学 | Method for preparing dispersed Al3Ti phase-enhanced Al-Cu-Mg system alloy |
| CN104384506A (en) * | 2014-11-05 | 2015-03-04 | 王宏颖 | Electromagnetic shielding-type composite material for mechanical equipment and preparation method for electromagnetic shielding-type composite material |
| CN105603228A (en) * | 2016-01-28 | 2016-05-25 | 大连理工大学 | Preparation method of in-situ nanoparticle reinforced magnesium-based composite |
| CN108817384A (en) * | 2018-06-28 | 2018-11-16 | 北京理工大学 | A kind of preparation method of core-shell structure particles reinforced aluminum matrix composites |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102896321B (en) * | 2012-10-26 | 2016-03-02 | 攀钢集团攀枝花钢铁研究院有限公司 | A kind of processing method of titanium or titanium alloy particle |
-
2007
- 2007-06-08 CN CNB200710023304XA patent/CN100513624C/en not_active Expired - Fee Related
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102002649A (en) * | 2010-09-16 | 2011-04-06 | 无锡南理工科技发展有限公司 | High-toughness magnesium based block body metal glass composite material and preparation method thereof |
| CN102002649B (en) * | 2010-09-16 | 2013-08-14 | 南京理工大学 | High-toughness magnesium based block body metal glass composite material and preparation method thereof |
| CN102230096A (en) * | 2011-06-27 | 2011-11-02 | 常州大学 | Method for preparing dispersed Al3Ti phase-enhanced Al-Cu-Mg system alloy |
| CN102230096B (en) * | 2011-06-27 | 2013-01-16 | 常州大学 | Method for preparing dispersed Al3Ti phase-enhanced Al-Cu-Mg system alloy |
| CN104384506A (en) * | 2014-11-05 | 2015-03-04 | 王宏颖 | Electromagnetic shielding-type composite material for mechanical equipment and preparation method for electromagnetic shielding-type composite material |
| CN105603228A (en) * | 2016-01-28 | 2016-05-25 | 大连理工大学 | Preparation method of in-situ nanoparticle reinforced magnesium-based composite |
| CN105603228B (en) * | 2016-01-28 | 2017-08-01 | 大连理工大学 | A kind of preparation method of in-situ nano particle reinforced magnesium base compound material |
| CN108817384A (en) * | 2018-06-28 | 2018-11-16 | 北京理工大学 | A kind of preparation method of core-shell structure particles reinforced aluminum matrix composites |
| CN108817384B (en) * | 2018-06-28 | 2020-11-17 | 北京理工大学 | Preparation method of core-shell structure particle reinforced aluminum matrix composite |
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