CN103555982A - Titanium-aluminum-carbon particle-reinforced zinc-aluminum-based composite material and hot-pressing sintering preparation method thereof - Google Patents
Titanium-aluminum-carbon particle-reinforced zinc-aluminum-based composite material and hot-pressing sintering preparation method thereof Download PDFInfo
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Abstract
The invention discloses a titanium-aluminum-carbon particle-reinforced zinc-aluminum-based composite material, which is prepared from the following raw materials in percentage by volume: 5 to 50 percent of titanium-aluminum-carbon and the balance of zinc-aluminum ally. According to the composite material, a particle reinforcing phase is uniform in distribution, and is closely bonded with a substrate, and the composite material is low in defect rate, and has high physical and mechanical performance. The invention also discloses the hot-pressing sintering preparation method for the titanium-aluminum-carbon particle-reinforced zinc-aluminum-based composite material.
Description
Technical field
The present invention relates to metal-base composites and preparation field thereof, particularly a kind of titanium aluminium carbon granule strengthens Zn Al Alloy Matrix Composites and hot pressed sintering preparation method thereof.
Background technology
Aluminium zinc (alloy series such as ZA8, ZA12, ZA22, ZA27) has good mechanical property, castability, machining property and friction and wear behavior, material cost is low simultaneously, fusing energy consumption is little, now in a lot of occasions, successfully substitute the materials such as bronze, brass, aluminium alloy, aspect the abrasive resistance sealing partses such as bearing, axle sleeve, bearing shell, be widely used.But due to the fusing point of zinc low (419.5 ℃), make the eutectic temperature of aluminium zinc low, freezing range is large, and actual solidus is roughly 380 ℃ of left and right, thereby alloy can only use lower than 100 ℃ in the situation that, its tensile strength and creep strength significantly reduce when more than 100 ℃.And in actual process of friction and wear, due to insufficient lubrication and run up, the temperature rise of friction pair is sometimes up to 150 ℃ even more than 200 ℃, this obviously understands the use properties of severe exacerbation aluminium zinc, and its range of application and work-ing life are very restricted.
In order to improve use temperature and the performance of aluminium zinc, meet the user demand under severe condition, since the eighties in last century, developed the multiple Zn Al Alloy Matrix Composites that ceramic particle, whisker or fiber be wild phase of take, improved the mechanical behavior under high temperature of aluminium zinc, also improve room temperature strength and the wear resistance of material simultaneously, and reduced the too high thermal expansivity of aluminium zinc.Wherein particle enhancing Zn Al Alloy Matrix Composites technique is simple, cost is lower, is the emphasis of Zn Al Alloy Matrix Composites research and development.At present for strengthening the ceramic particle reinforced phase of aluminium zinc, comprise aluminum oxide, silicon carbide, titanium carbide, silicon and graphite etc.Composite material preparation process has Melt Stirring casting, spray up moulding, powder hotforging method, lamination composite algorithm and original position to generate composite algorithm etc.For example patent of invention " spray-deposition nano particle reinforced zinc-based composite and preparation method thereof " (application number 201010557276.1) adopts spray deposition technique to prepare the Zn Al Alloy Matrix Composites that nano titanium carbide particle strengthens; Patent of invention " a kind of preparation method of silicon particle reinforced zinc based composite material " (application number 200810155784.X) adopts melt cast legal system for the Zinc-base compounded material of silicon grain enhancing; Patent of invention " a kind of preparation method of ceramic-powder-enhanced zinc-aluminum alloy based composite material " (application number 201110341289.X) adopts powder hotforging legal system for the Zn Al Alloy Matrix Composites of the ceramic particle enhancings such as silicon carbide, aluminum oxide, zirconium white; Patent of invention " preparation method of original position particle reinforced zinc-based composite material " (application number 200710020458.3) adopts melt cast legal system for Al
2o
3, TiB
2+ Al
3the Zn Al Alloy Matrix Composites that the ceramic particle original positions such as Ti strengthen; Patent of invention " potassium titanate fabric reinforced zinc-aluminium alloy composite material and manufacture method thereof " (application number 98113701.6) adopts melt extrusion cladding legal system for the Zn Al Alloy Matrix Composites of potassium titanate crystal whisker enhancing.
Yet up to the present, Zn Al Alloy Matrix Composites is still in the research and development stage, reach far away suitability for industrialized production level of application, its major cause is between these particulates reinforcements used in matrix material and alloy substrate that wettability is poor, particle surface is easy to adsorbed gas and causes material internal to produce between defect and particle and matrix because thermal expansion coefficient difference causes greatly interface disengagement etc., these problems cause the isolate effect of particle in matrix obviously, reinforced effects is weakened, thus remarkably influenced applying of Zn Al Alloy Matrix Composites.For breaking through this bottleneck of Zn Al Alloy Matrix Composites development, find a more applicable particulates reinforcements effective approach beyond doubt.
Summary of the invention
First technical problem to be solved by this invention is to provide a kind of titanium aluminium carbon granule and strengthens Zn Al Alloy Matrix Composites, and in this material, particulates reinforcements is evenly distributed, and between matrix and wild phase, in conjunction with tight, defect is few, has good physicals and mechanical property.
Second technical problem that the present invention will solve is to provide the hot pressed sintering preparation method that a kind of titanium aluminium carbon granule strengthens Zn Al Alloy Matrix Composites.
For solving above-mentioned first technical problem, the technical solution used in the present invention is to provide a kind of titanium aluminium carbon granule and strengthens Zn Al Alloy Matrix Composites, the raw material that described matrix material comprises following percent by volume: 5～50% titanium aluminium carbon, surplus is aluminium zinc.
Preferably, described titanium aluminium carbon be granularity at the particle of 0.5～20 μ m, its purity is greater than 90%; Described aluminium zinc is granularity 100～400 object powder.
For solving above-mentioned second technical problem, the invention provides the hot pressed sintering preparation method that this titanium aluminium carbon granule strengthens Zn Al Alloy Matrix Composites, the method comprises the steps:
1) by titanium aluminium carbon dust and aluminium zinc powder weigh batching;
2) by step 1) two kinds of spheres of powder mills weighing mix 6～48 hours;
3) by step 2) mixed powder put into mould, carry out hot pressed sintering, obtain titanium aluminium carbon granule and strengthen Zn Al Alloy Matrix Composites.
Preferably, step 2) described ball milling adopts roller ball mill method.
Preferably, step 3) described mould is graphite jig.
Preferably, step 3) condition of described hot pressed sintering is: under vacuum, nitrogen or argon gas atmosphere protection, with the temperature rise rate of 10～40 ℃/min, rise to 430～500 ℃, and under 10～30MPa pressure, hot pressed sintering 0.5～3 hour.
Particulates reinforcements titanium aluminium carbon (Ti of the present invention
3alC
2) be a kind of ternary layered carbide ceramics, it had both had high conduction, thermal conductivity, high-temp plastic and the machinability of metalloid, had again ceramic high elastic coefficient, low density, high thermal stability and good antioxidant property simultaneously; And there is self lubricity and excellent tribological property.Titanium aluminium carbon belongs to hexagonal system, in its crystalline structure, the Ti-C octahedron of rib is separated by an Al atomic plane layer altogether, C atom is positioned at the octahedra center of Ti, between Ti atom and C atom, be combined into strong covalent bond, and be combined into the weak binding that is similar to graphite layers between Ti atom and Al atomic shell.These features of titanium aluminium carbon make it when the particulates reinforcements as Zn Al Alloy Matrix Composites, have the advantage of following uniqueness:
1) interface compatibility is good: in titanium aluminium carbon crystal, the Al atomic shell of weak binding at high temperature can partly be deviate to enter in metallic matrix, because matrix itself contains Al, to from Ti
3alC
2in the Al that deviates from have good affinity, this is conducive to improve the wettability between matrix and wild phase, thereby obtains comparatively ideal interface.Al atom deviate from amount and temperature is closely related, because the preparation temperature of Zinc-base compounded material is lower, Al to deviate from amount less, but still be enough to the generation of interfaces favorable influence to both.
2) be conducive to improve wear resistance: the existence of Al atom weak binding layer makes titanium aluminium carbon be easy under external force throw off along Al atomic shell, thereby there is excellent self lubricity, this is very favourable to the Zn Al Alloy Matrix Composites as high-abrasive material, especially under more severe friction environment, its effect will be more outstanding.
3) matched coefficients of thermal expansion: the thermal expansivity (～10 * 10 of titanium aluminium carbon
-6k
-1) between conventional ceramic and metal, than other ceramic enhancement phase, closer to metal, thereby the thermal mismatching between itself and zinc alloy is less than other compound system, when composite temperature changes, the thermal stresses in material is less, and performance is more stable.
As can be seen here, selecting titanium aluminium carbon granule to strengthen aluminium zinc, is to solve in current Zn Al Alloy Matrix Composites matrix interface between wild phase to be combined the not Appropriate method of good this difficult problem.
The invention has the beneficial effects as follows:
1) in matrix material of the present invention, titanium aluminium carbon granule wild phase is evenly distributed, and between matrix and wild phase, in conjunction with tight, defect is few.
2) utilize hot-pressing sintering technique to prepare titanium aluminium carbon granule and strengthen Zn Al Alloy Matrix Composites, can make material approach completely fine and close, as depicted in figs. 1 and 2, the physicals of matrix material and good mechanical performance.
Accompanying drawing explanation
Fig. 1 is the surface microscopic topographic figure that the titanium aluminium carbon granule prepared of embodiment 2 hot-pressing sintering techniques strengthens Zn Al Alloy Matrix Composites;
Fig. 2 is the fracture microscopic appearance figure that the titanium aluminium carbon granule prepared of embodiment 2 hot-pressing sintering techniques strengthens Zn Al Alloy Matrix Composites.
Embodiment
Below in conjunction with drawings and Examples, the present invention is further illustrated.
Embodiment 1
1. titanium aluminium carbon dust: in the present embodiment, titanium aluminium carbon dust purity used is 95%, median size 7.39 μ m.
2. aluminium zinc powder: in the present embodiment, aluminium zinc used is commercially available ZA8 alloy powder, and powder size is 200 orders, and its mass percent composition is as follows: Zn91.73%, Al7.95%, Fe0.19%, Si0.10%, other 0.03%.
3. ZA8 alloy powder and titanium aluminium carbon dust are prepared burden according to the volume ratio of 6:4; take ZA8 powder 68.98g; titanium aluminium carbon dust 31.02g; put into ball grinder intermediate roll ball milling 24h; take mixed powder 30g and put into graphite jig, pre-molding under 8MPa pressure, puts into mould the hot pressing furnace of the argon shield of flowing; speed with 30 ℃/min is warming up to 460 ℃, under the pressure of 25MPa, is incubated 60min.
Prepared 40vol%Ti
3alC
2the mechanical property of/ZA8 matrix material is: flexural strength 159MPa, Vickers' hardness 110HV.
Embodiment 2
1. titanium aluminium carbon dust: in the present embodiment, titanium aluminium carbon dust purity used is 95%, median size 7.39 μ m.
2. aluminium zinc powder: in the present embodiment, aluminium zinc used is commercially available ZA8 alloy powder, and powder size is 200 orders, and its mass percent composition is as follows: Zn91.73%, Al7.95%, Fe0.19%, Si0.10%, other 0.03%.
3. ZA8 alloy powder and titanium aluminium carbon dust are prepared burden according to the volume ratio of 7:3; take ZA8 powder 77.57g; titanium aluminium carbon dust 22.43g; put into the mixed cylinder of ball grinder ball milling 48h; take mixed powder 31g and put into graphite jig, pre-molding under 8MPa pressure, puts into mould the hot pressing furnace of flowing nitrogen protection; speed with 40 ℃/min is warming up to 490 ℃, under the pressure of 30MPa, is incubated 120min.
Prepared 30vol%Ti
3alC
2the mechanical property of/ZA8 matrix material is: flexural strength 316MPa, Vickers' hardness 105HV.
Embodiment 3
1. titanium aluminium carbon dust: in the present embodiment, titanium aluminium carbon dust purity used is 92%, median size 12.52 μ m.
2. aluminium zinc powder: in the present embodiment, aluminium zinc used is commercially available ZA8 alloy powder, and powder size is 200 orders, and its mass percent composition is as follows: Zn91.73%, Al7.95%, Fe0.19%, Si0.10%, other 0.03%.
3. ZA8 alloy powder and titanium aluminium carbon dust are prepared burden according to the volume ratio of 8:2; take ZA8 powder 85.57g; titanium aluminium carbon dust 14.43g; put into the mixed cylinder of ball grinder ball milling 36h; take mixed powder 32g and put into graphite jig, pre-molding under 8MPa pressure, puts into mould the hot pressing furnace of the argon shield of flowing; speed with 20 ℃/min is warming up to 440 ℃, under the pressure of 15MPa, is incubated 180min.
Prepared 20vol%Ti
3alC
2the mechanical property of/ZA8 matrix material is: flexural strength 320MPa, Vickers' hardness 88HV.
Embodiment 4
1. titanium aluminium carbon dust: in the present embodiment, titanium aluminium carbon dust purity used is 92%, median size 12.52 μ m.
2. aluminium zinc powder: in the present embodiment, aluminium zinc used is commercially available ZA8 alloy powder, and powder size is 200 orders, and its mass percent composition is as follows: Zn91.73%, Al7.95%, Fe0.19%, Si0.10%, other 0.03%.
3. ZA8 alloy powder and titanium aluminium carbon dust are prepared burden according to the volume ratio of 9:1, take ZA8 powder 93.03g, titanium aluminium carbon dust 6.97g, put into the mixed cylinder of ball grinder ball milling 12h, take mixed powder 33g and put into graphite jig, pre-molding under 8MPa pressure, puts into hot pressing furnace by mould, speed with 10 ℃/min under vacuum condition is warming up to 450 ℃, under the pressure of 25MPa, is incubated 60min.
Prepared 10vol%Ti
3alC
2the mechanical property of/ZA8 matrix material is: flexural strength 259MPa, Vickers' hardness 74HV.
Embodiment 5
1. titanium aluminium carbon dust: in the present embodiment, titanium aluminium carbon dust purity used is 97%, median size 4.21 μ m.
2. aluminium zinc powder: in the present embodiment, aluminium zinc used is commercially available ZA12 alloy powder, and powder size is 400 orders, and its mass percent composition is as follows: Zn88.33%, Al11.47%, Fe0.07%, Si0.10%, other 0.03%.
3. ZA12 alloy powder and titanium aluminium carbon dust are prepared burden according to the volume ratio of 8:2; take ZA12 powder 84.98g; titanium aluminium carbon dust 15.02g; put into the mixed cylinder of ball grinder ball milling 24h; take mixed powder 31g and put into graphite jig, pre-molding under 10MPa pressure, puts into mould the hot pressing furnace of the argon shield of flowing; speed with 25 ℃/min is warming up to 440 ℃, under the pressure of 30MPa, is incubated 60min.
Prepared 20vol%Ti
3alC
2the mechanical property of/ZA12 matrix material is: flexural strength 243MPa, Vickers' hardness 83HV.
Embodiment 6
1. titanium aluminium carbon dust: in the present embodiment, titanium aluminium carbon dust purity used is 97%, median size 4.21 μ m.
2. aluminium zinc powder: in the present embodiment, aluminium zinc used is commercially available ZA 27 alloy powder, and powder size is 300 orders, and its mass percent composition is as follows: Zn72.31%, Al27.47%, Fe0.09%, Si0.10%, other 0.03%.
3. ZA 27 alloy powder and titanium aluminium carbon dust are prepared burden according to the volume ratio of 8:2; take ZA27 powder 82.50g; titanium aluminium carbon dust 17.50g; put into the mixed cylinder of ball grinder ball milling 36h; take mixed powder 30g and put into graphite jig, pre-molding under 8MPa pressure, puts into mould the hot pressing furnace of flowing nitrogen protection; speed with 20 ℃/min is warming up to 460 ℃, under the pressure of 25MPa, is incubated 90min.
Prepared 20vol%Ti
3alC
2the mechanical property of/ZA27 matrix material is: flexural strength 339MPa, Vickers' hardness 117HV.
The major impurity of the present invention's titanium aluminium used carbon dust is titanium carbide, and in theory, the existence of titanium carbide can have a certain impact to the performance of matrix material, but because its content is less, from actual result, little on the impact of composite property.
Fig. 1 is the surface microscopic topographic figure that the titanium aluminium carbon granule prepared of embodiment 2 hot-pressing sintering techniques strengthens Zn Al Alloy Matrix Composites.As can be seen from the figure, comprise 3 kinds of obvious microtextures of feature in matrix material, wherein the more shallow part of color is Zn solid solution phase, and striated is partly Zn-Al eutectoid structure, and the darker block of color is Ti
3alC
2wild phase.Visible Ti in figure
3alC
2uniform particles is distributed in aluminium zinc matrix, and interface, in conjunction with good, has a small amount of pore to exist simultaneously in matrix material between the two.
Fig. 2 is the fracture microscopic appearance figure that the titanium aluminium carbon granule prepared of embodiment 2 hot-pressing sintering techniques strengthens Zn Al Alloy Matrix Composites.As seen from the figure, titanium aluminium carbon granule wild phase be take transgranular fracture mode as main, illustrates that it is combined well with aluminium zinc matrix.
Claims (6)
1. titanium aluminium carbon granule strengthens a Zn Al Alloy Matrix Composites, it is characterized in that the raw material that described matrix material comprises following percent by volume: 5～50% titanium aluminium carbon, surplus is aluminium zinc.
2. titanium aluminium carbon granule according to claim 1 strengthens Zn Al Alloy Matrix Composites, it is characterized in that: described titanium aluminium carbon be granularity at the particle of 0.5～20 μ m, its purity is greater than 90%; Described aluminium zinc is granularity 100～400 object powder.
3. a hot pressed sintering preparation method for titanium aluminium carbon granule enhancing Zn Al Alloy Matrix Composites described in claim 1 or 2, is characterized in that, comprises the steps:
1) by titanium aluminium carbon dust and aluminium zinc powder weigh batching;
2) by step 1) two kinds of powder ball millings weighing mix 6～48 hours;
3) by step 2) mixed powder put into mould, carry out hot pressed sintering, obtain titanium aluminium carbon granule and strengthen Zn Al Alloy Matrix Composites.
4. preparation method according to claim 3, is characterized in that: step 2) described ball milling employing roller ball mill method.
5. preparation method according to claim 3, is characterized in that: step 3) described mould is graphite jig.
6. preparation method according to claim 3; it is characterized in that: step 3) condition of described hot pressed sintering is: under vacuum, nitrogen or argon gas atmosphere protection; temperature rise rate with 10～40 ℃/min rises to 430～500 ℃, under 10～30MPa pressure, and hot pressed sintering 0.5～3 hour.
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| CN104099488A (en) * | 2014-07-24 | 2014-10-15 | 北京交通大学 | Pressureless sintering-pressurized densifying preparation method for titanium-aluminum-carbon particle enhanced zinc-aluminum matrix composite |
| CN104928511A (en) * | 2015-06-30 | 2015-09-23 | 中南大学 | Hot pressing sintering particle reinforcing zinc-based composite material and preparation method thereof |
| CN105200252A (en) * | 2014-06-24 | 2015-12-30 | 江苏朗亿新材料有限公司 | Novel high-conductivity and high-abrasion-resistance aluminum matrix composite |
| CN105219981A (en) * | 2014-06-24 | 2016-01-06 | 江苏朗亿新材料有限公司 | A kind of controlled volume mark Ti 2alC pthe preparation method of/Al based composites |
| CN106334719A (en) * | 2015-07-15 | 2017-01-18 | 柳州市双铠工业技术有限公司 | Method for producing composite wear-resistant product through extrusion molding |
| CN106345834A (en) * | 2015-07-15 | 2017-01-25 | 柳州市双铠工业技术有限公司 | Extrusion forming production method for composite wear resistant product with cold plastic matrix |
| CN110747378A (en) * | 2019-11-06 | 2020-02-04 | 北京交通大学 | Ti3AlC2-Al3Ti dual-phase reinforced Al-based composite material and hot-pressing preparation method thereof |
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| CN105200252A (en) * | 2014-06-24 | 2015-12-30 | 江苏朗亿新材料有限公司 | Novel high-conductivity and high-abrasion-resistance aluminum matrix composite |
| CN105219981A (en) * | 2014-06-24 | 2016-01-06 | 江苏朗亿新材料有限公司 | A kind of controlled volume mark Ti 2alC pthe preparation method of/Al based composites |
| CN104099488A (en) * | 2014-07-24 | 2014-10-15 | 北京交通大学 | Pressureless sintering-pressurized densifying preparation method for titanium-aluminum-carbon particle enhanced zinc-aluminum matrix composite |
| CN104099488B (en) * | 2014-07-24 | 2016-07-06 | 北京交通大学 | The method that titanium aluminum carbon granule strengthens Zn Al Alloy Matrix Composites is prepared in a kind of pressureless sintering-pressurization densification |
| CN104928511A (en) * | 2015-06-30 | 2015-09-23 | 中南大学 | Hot pressing sintering particle reinforcing zinc-based composite material and preparation method thereof |
| CN106334719A (en) * | 2015-07-15 | 2017-01-18 | 柳州市双铠工业技术有限公司 | Method for producing composite wear-resistant product through extrusion molding |
| CN106345834A (en) * | 2015-07-15 | 2017-01-25 | 柳州市双铠工业技术有限公司 | Extrusion forming production method for composite wear resistant product with cold plastic matrix |
| CN110747378A (en) * | 2019-11-06 | 2020-02-04 | 北京交通大学 | Ti3AlC2-Al3Ti dual-phase reinforced Al-based composite material and hot-pressing preparation method thereof |
| CN110747378B (en) * | 2019-11-06 | 2020-12-25 | 北京交通大学 | Ti3AlC2-Al3Ti dual-phase reinforced Al-based composite material and hot-pressing preparation method thereof |
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