CN1293214C - Dibismuth trioxide enveloped ceramic phase reinforced aluminium base composite material - Google Patents
Dibismuth trioxide enveloped ceramic phase reinforced aluminium base composite material Download PDFInfo
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- CN1293214C CN1293214C CNB2005100096842A CN200510009684A CN1293214C CN 1293214 C CN1293214 C CN 1293214C CN B2005100096842 A CNB2005100096842 A CN B2005100096842A CN 200510009684 A CN200510009684 A CN 200510009684A CN 1293214 C CN1293214 C CN 1293214C
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- ceramic phase
- reinforcement
- composite material
- bismuth trioxide
- matrix
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- 239000000919 ceramic Substances 0.000 title claims abstract description 73
- 239000002131 composite material Substances 0.000 title claims abstract description 59
- WMWLMWRWZQELOS-UHFFFAOYSA-N bismuth(iii) oxide Chemical compound O=[Bi]O[Bi]=O WMWLMWRWZQELOS-UHFFFAOYSA-N 0.000 title claims abstract description 47
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 40
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 40
- 239000004411 aluminium Substances 0.000 title 1
- 230000002787 reinforcement Effects 0.000 claims abstract description 65
- 239000011159 matrix material Substances 0.000 claims abstract description 42
- 239000000203 mixture Substances 0.000 claims description 6
- 239000000835 fiber Substances 0.000 claims description 4
- 239000002245 particle Substances 0.000 claims description 4
- 229910000838 Al alloy Inorganic materials 0.000 claims description 3
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims 2
- 229910052797 bismuth Inorganic materials 0.000 abstract description 10
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 abstract description 10
- 229910052751 metal Inorganic materials 0.000 abstract description 10
- 239000002184 metal Substances 0.000 abstract description 10
- 238000002844 melting Methods 0.000 abstract description 7
- 230000008018 melting Effects 0.000 abstract description 6
- 238000006243 chemical reaction Methods 0.000 abstract description 2
- 239000007788 liquid Substances 0.000 abstract description 2
- 238000005253 cladding Methods 0.000 abstract 1
- 239000000314 lubricant Substances 0.000 abstract 1
- 239000000155 melt Substances 0.000 abstract 1
- 239000003832 thermite Substances 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 45
- 229920001169 thermoplastic Polymers 0.000 description 8
- 239000004416 thermosoftening plastic Substances 0.000 description 8
- 239000004033 plastic Substances 0.000 description 6
- 238000000034 method Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 4
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 230000001965 increasing effect Effects 0.000 description 3
- 239000007791 liquid phase Substances 0.000 description 3
- 238000007133 aluminothermic reaction Methods 0.000 description 2
- 238000005461 lubrication Methods 0.000 description 2
- 239000007790 solid phase Substances 0.000 description 2
- 238000012876 topography Methods 0.000 description 2
- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910000416 bismuth oxide Inorganic materials 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- TYIXMATWDRGMPF-UHFFFAOYSA-N dibismuth;oxygen(2-) Chemical compound [O-2].[O-2].[O-2].[Bi+3].[Bi+3] TYIXMATWDRGMPF-UHFFFAOYSA-N 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
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Abstract
三氧化二铋包覆陶瓷相增强铝基复合材料，它涉及一种新型的复合材料。本发明的铝基复合材料由三氧化二铋、陶瓷相增强体和铝基体三种成分组成，其中陶瓷相增强体的体积分数占总体积分数的5～50%，三氧化二铋的加入量占陶瓷相增强体质量的2～20%。包覆物三氧化二铋基本都在增强体和基体的界面处，并且三氧化二铋和基体铝发生铝热反应，生成低熔点金属铋都分布在增强体和基体的界面处。在复合材料热变形时，温度高于金属铋的熔点270℃，界面处的低熔点金属铋熔化变成液体，在增强体和基体之间起到润滑作用，降低了变形温度和加工成本，减少了陶瓷相增强体的损伤，变形后的复合材料仍有优良的力学性能。The invention discloses bismuth trioxide-coated ceramic phase-reinforced aluminum matrix composite material, which relates to a new type of composite material. The aluminum-based composite material of the present invention is composed of bismuth trioxide, a ceramic phase reinforcement and an aluminum matrix, wherein the volume fraction of the ceramic phase reinforcement accounts for 5% to 50% of the total fraction, and the added amount of bismuth trioxide It accounts for 2 to 20% of the mass of the ceramic phase reinforcement. The cladding bismuth trioxide is basically at the interface between the reinforcement and the matrix, and bismuth trioxide and the matrix aluminum undergo a thermite reaction to generate low-melting metal bismuth that is distributed at the interface between the reinforcement and the matrix. When the composite material is thermally deformed, the temperature is 270°C higher than the melting point of metal bismuth, and the low melting point metal bismuth at the interface melts and becomes liquid, which acts as a lubricant between the reinforcement and the matrix, reducing the deformation temperature and processing costs, and reducing The damage of the ceramic phase reinforcement is eliminated, and the deformed composite still has excellent mechanical properties.
Description
The technical field is as follows:
the invention relates to a novel composite material, in particular to a method for coating bismuth oxide (Bi) on the surface of a ceramic phase reinforcement2O3) A reinforced aluminum matrix composite.
Background art:
in recent years, ceramic phase reinforced metals, especially reinforced aluminum matrix composites, are gaining widespread attention. The most attractive properties of this material are its excellent properties of high strength, high modulus and low coefficient of thermal expansion. Great attention has been paid to the potential superiority of ceramic phase reinforced aluminum matrix composites, and some composites have been used in the automotive, aerospace, astronomical and general engineering fields. Although commercial application is emerging, the low plasticity of the composite material is a fatal weakness, which becomes a difficulty that the composite material cannot be used for producing parts at room temperature by using a conventional forming method, and the application prospect of commercializing the composite material is severely limited. Moreover, most aluminum matrix composite parts can only be formed by thermoplastic processing due to the inherent low plasticity limit. The composite material must therefore be subjected to a thermoplastic deformation process at a temperature well above room temperature. The composite material is subjected to plastic deformation at the medium temperature, the matrix is not softened, the rotation of the reinforcement and the plastic deformation of the matrix cannot be coordinated, the reinforcement can be damaged, and the mechanical property of the composite material is seriously reduced; if the plastic deformation of the composite material is carried out at a high temperature close to the liquid-solid phase line of the matrix, the reinforcement is easy to rotate and damage is reduced because the matrix is softened and even liquid phase occurs, but because the deformation temperature is close to the liquid-solid phase line of the matrix, the reinforcement in the matrix is unevenly distributed, an enrichment area and a depletion area are formed, the mechanical property of the material is also reduced, and the secondary processing cost of the composite material is increased because the deformation temperature is too high.
The invention content is as follows:
the invention aims to develop a bismuth trioxide coated ceramic phase reinforced aluminum matrix composite, which not only can reduce the thermoplastic deformation temperature of the composite and reduce the hot processing cost of the composite, but also can reduce the damage of a reinforcement in the plastic deformation process of a matrix, and the composite still has good mechanical properties after thermal deformation. The composite material of the invention is prepared by bismuth trioxide (Bi)2O3) The ceramic phase reinforcement comprises three components, namely a ceramic phase reinforcement and an aluminum matrix, wherein the volume fraction of the ceramic phase reinforcement accounts for 5-50% of the total volume fraction, and the addition amount of the bismuth trioxide accounts for 2-20% of the mass of the ceramic phase reinforcement.
The maximum deformation resistance and resistance difference of the bismuth trioxide-coated reinforced aluminum-based composite material and the aluminum-based composite material without bismuth trioxide coating on the surface of the ceramic phase reinforcement at different temperatures are shown in figure 1. As can be seen from the figure: with the increase of the deformation temperature, the deformation resistance of the two materials is reduced, and the difference value of the deformation resistance isIncreasing and then decreasing with increasing temperature. The difference value of the deformation resistance of the two composite materials has a steep slope after 270 ℃, after the deformation temperature is higher than 270 ℃, the metal bismuth on the interface is completely melted, but the matrix is not softened, and the liquid phase on the interface plays a role in lubrication and coordination in the deformation process, so that the difference value of the deformation resistance of the two composite materials is suddenly increased; after the deformation temperature is higher than 320 ℃, the matrix gradually begins to soften, the binding capacity for the rotation of the ceramic phase reinforcement is weakened, although a trace amount of liquid phase on the interface also plays a certain lubricating role, the softening of the matrix plays a decisive role, the ceramic phase reinforcement is easy to rotate, and therefore the difference of the maximum deformation resistance of the ceramic phase reinforcement and the maximum deformation resistance of the ceramic phase reinforcement is reduced. The scanning photographs of the two composites after deformation at 350 ℃ are shown in FIGS. 2 and 3, respectively, and the scanning photographs of the two composites are compared, and at the same temperature, no Bi is contained2O3The damage condition of the composite material ceramic phase reinforcement is higher than that of the composite material containing Bi2O3The composite material is much more severe, andand the average grain size of the ceramic phase reinforcement is smaller, so that the fact that the metal Bi on the interface of the ceramic phase reinforcement and the matrix reduces the maximum compressive deformation stress, reduces the damage quantity of the ceramic phase reinforcement and improves the plastic forming capability of the material is powerfully proved.
The invention has the following advantages:
(1) coating bismuth trioxide on the surface of the ceramic phase reinforcement can prevent the reinforcement from carrying out interface reaction with elements in the matrix;
(2) the bismuth trioxide and aluminum are subjected to aluminothermic reaction to generate metal bismuth with a low melting point, and the specific aluminothermic reaction equation is as follows:
the metal bismuth with low melting point is distributed on the interface of the reinforcement and the matrix, which is beneficial to the thermoplastic deformation of the ceramic phase reinforced aluminum matrix composite;
(3) the plastic deformation is carried out at the temperature 270 ℃ higher than the melting point of the metal bismuth, the bismuth on the interface is changed into liquid, the lubrication effect is realized on the interface, compared with the aluminum-based composite material of which the surface of the reinforcement is not coated with the bismuth trioxide, the thermoplastic deformation capability of the composite material is improved, the damage of the ceramic phase reinforcement is obviously reduced, and the mechanical property of the aluminum-based composite material after the thermoplastic deformation is not reduced.
Description of the drawings:
FIG. 1 is a graph showing the maximum deformation resistance and resistance difference of the ceramic phase reinforcement surface coated with bismuth trioxide reinforced aluminum matrix composite and the aluminum matrix composite not coated with bismuth trioxide under different temperature compression deformation, wherein the left coordinate is the relationship between the maximum rheological stress of the two composites and the temperature, and the right coordinate is the relationship between the difference between the maximum rheological stress of the two composites and the temperature; FIG. 2 shows the surface of the reinforcement coated with bismuth trioxide (Bi)2O3) Enhancing the surface topography of the aluminum-based composite material after thermal deformation; FIG. 3 shows the non-coated bismuth trioxide (Bi)2O3) Is subjected to thermal deformationAnd (5) surface topography map.
The specific implementation mode is as follows:
the first embodiment is as follows: the composite material of the present embodiment is composed of bismuth (Bi) oxide2O3) The ceramic phase reinforcement comprises three components, namely a ceramic phase reinforcement and an aluminum matrix, wherein the volume fraction of the ceramic phase reinforcement accounts for 5-50% of the total volume fraction, the addition amount of bismuth trioxide accounts for 2-20% of the mass of the ceramic phase reinforcement, and the surface of the ceramic phase reinforcement is coated with the bismuth trioxide firstly; the surface is then coated with a bismuth trioxide ceramic phase and aluminum or an aluminum alloy to prepare a composite. The surface-coated bismuth trioxide ceramic phase reinforced aluminum-based composite material is subjected to thermoplastic deformation at a temperature of 270 ℃ higher than the melting point of metal bismuth, so that the thermal deformation temperature and the processing cost of the composite material can be reduced, the damage of a ceramic phase reinforcement is obviously reduced, and the mechanical property of the aluminum-based composite material subjected to thermoplastic deformation is not reduced. The ceramic phase reinforcement is one or a mixture of a plurality of short fibers, particles and whiskers, wherein the short fibers are Al2O3、SiC、B2O3One or more of TiN and Al as particles2O3、SiC、Al18B4O33、Si3N4、AlN、B4C. One or more of TiC, and crystal whisker of SiC, AlN, 9Al2O3·2B2O3(Al18B4O33)、Si3N4、2MgO·B2O3(Mg2B3O5) One or a mixture of more of the above; the aluminum matrix is pure aluminum or aluminum alloy.
The second embodiment is as follows: the difference between the present embodiment and the first embodiment is that the volume fraction of the ceramic phase reinforcement is 8% of the total volume fraction, and the addition amount of the bismuth trioxide is 5% of the mass of the ceramic phase reinforcement.
The third concrete implementation mode: the difference between the first embodiment andthe second embodiment is that the volume fraction of the ceramic phase reinforcement is 15% of the total volume fraction, and the addition amount of the bismuth trioxide is 10% of the mass of the ceramic phase reinforcement.
The fourth concrete implementation mode: the difference between this embodiment and the first, second and third embodiments is that the volume fraction of the ceramic phase reinforcement is 20% of the total volume fraction, and the addition amount of the bismuth trioxide is 8% of the mass of the ceramic phase reinforcement.
The fifth concrete implementation mode: the difference between this embodiment and the first, second, third and fourth embodiments is that the volume fraction of the ceramic phase reinforcement is 25% of the total volume fraction, and the addition amount of the bismuth trioxide is 14% of the mass of the ceramic phase reinforcement.
The sixth specific implementation mode: the difference between this embodiment and the first, second, third, fourth and fifth embodiments is that the volume fraction of the ceramic phase reinforcement is 40% of the total volume fraction, and the addition amount of the bismuth trioxide is 18% of the mass of the ceramic phase reinforcement.
The seventh embodiment: the difference between this embodiment and the first, second, third, fourth, fifth and sixth embodiments is that the volume fraction of the ceramic phase reinforcement is 32% of the total volume fraction, and the addition amount of bismuth trioxide is 16% of the mass of the ceramic phase reinforcement.
The specific implementation mode is eight: the difference between this embodiment and the first, second, third, fourth, fifth, sixth and seventh embodiments is that the volume fraction of the ceramic phase reinforcement is 12% of the total volume fraction, and the addition amount of the bismuth trioxide is 10% of the massof the ceramic phase reinforcement.
Claims (10)
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2005100096842A CN1293214C (en) | 2005-01-31 | 2005-01-31 | Dibismuth trioxide enveloped ceramic phase reinforced aluminium base composite material |
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| CNB2005100096842A CN1293214C (en) | 2005-01-31 | 2005-01-31 | Dibismuth trioxide enveloped ceramic phase reinforced aluminium base composite material |
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| CN1648270A CN1648270A (en) | 2005-08-03 |
| CN1293214C true CN1293214C (en) | 2007-01-03 |
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| CN101698913B (en) * | 2009-11-16 | 2011-07-20 | 哈尔滨工业大学 | Method for preparing low-melting-point alloy-coated ceramic-phase reinforced body/aluminum-matrix composite materials |
| KR101526657B1 (en) * | 2013-05-07 | 2015-06-05 | 현대자동차주식회사 | Wear-resistant alloys having a complex microstructure |
| CN105624758B (en) * | 2014-11-03 | 2018-07-06 | 宁波瑞隆表面技术有限公司 | A kind of preparation method of cast aluminum alloy micro-arc oxidation ceramic film |
| CN105086527A (en) * | 2015-08-18 | 2015-11-25 | 电子科技大学 | Low-infrared-emissivity composite pigment and preparation method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1104568A (en) * | 1993-11-24 | 1995-07-05 | 哈尔滨工业大学 | Manufacture of uncontinuously enhanced aluminum based composite material |
| CN1227206A (en) * | 1998-12-25 | 1999-09-01 | 北京航空材料研究院 | Foamed silicon carbide particle reinforced aluminium base composite material and its producing technology |
| CN1422970A (en) * | 2001-12-06 | 2003-06-11 | 北京有色金属研究总院 | Particle reinforced aluminium-based composite material and manufacture method thereof |
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1104568A (en) * | 1993-11-24 | 1995-07-05 | 哈尔滨工业大学 | Manufacture of uncontinuously enhanced aluminum based composite material |
| CN1227206A (en) * | 1998-12-25 | 1999-09-01 | 北京航空材料研究院 | Foamed silicon carbide particle reinforced aluminium base composite material and its producing technology |
| CN1422970A (en) * | 2001-12-06 | 2003-06-11 | 北京有色金属研究总院 | Particle reinforced aluminium-based composite material and manufacture method thereof |
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