CN106834833A - The strong TiB of a kind of high-modulus, superelevation2Particle REINFORCED Al Zn Mg Cu composites and preparation method thereof - Google Patents
The strong TiB of a kind of high-modulus, superelevation2Particle REINFORCED Al Zn Mg Cu composites and preparation method thereof Download PDFInfo
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- CN106834833A CN106834833A CN201710022771.4A CN201710022771A CN106834833A CN 106834833 A CN106834833 A CN 106834833A CN 201710022771 A CN201710022771 A CN 201710022771A CN 106834833 A CN106834833 A CN 106834833A
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- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
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- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
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Abstract
The strong TiB of a kind of high-modulus, superelevation2Particle REINFORCED Al Zn Mg Cu composites and preparation method thereof, belong to field of compound material.With zinc Al Zn Mg Cu Zr alloys high as matrix, mass fraction is 6.0 10.0% and TiB of the average-size less than 1 μm2It is enhancing particle.Al TiB are prepared using melt self- propagating direct synthesis technique2Intermediate alloy, by composite Materials Design ingredient composition melting, with Al TiB2Intermediate alloy is matrix, adds fine aluminium ingot, pure zinc ingot, pure magnesium ingot, Al Cu and Al Zr intermediate alloys, is stood after stirring, casting.By after 420 470 DEG C/25 45h Homogenization Treatments, being extruded at 330 430 DEG C, extrusion ratio is (15 20) to ingot casting:1.T6 artificial aging treatment is carried out to the material after extruding, matrix alloy intensity is significantly improved, elastic modelling quantity is than matrix alloy lifting 45%.
Description
Technical field
The invention belongs to field of compound material, the composition design and optimum preparation condition of more particularly to a kind of composite.
Background technology
Al-Zn-Mg-Cu aluminum alloy is one kind of 7xxx line aluminium alloys, also referred to as ultra-high-strength aluminum alloy.It is low based on its
The advantages of density, high specific strength and hardness, easy processing shaping, preferable decay resistance and toughness higher, be Aero-Space
And important lightweight structural material in defense industry.The aircraft and lightweight tank of modernization, it is more towards more at a high speed
Carry, the direction of more high traffic is developed, and service life and driving safety become more and more important, it is higher that this requires that material therefor has
Intensity, the Good All-around Property such as more preferable anti-fatigue performance and wearability.
Since the birth of the alloy of nineteen forty-three 7075, Al-Zn-Mg-Cu aluminum alloy optimizes after alloying component, and melt is net
Change, processing technology improves, nowadays the research of the aspect such as heat treatment optimization have developed into Zn contents and may be up to 11%, Zn/Mg values height
Up to 6, ultra-high-strength aluminum alloy of the tensile strength more than 700Mpa.However, because Zn/Mg is too high, the stress corrosion cracking of alloy is tight
Weight, the Zn contents of alloy are difficult to further lifting after bringing up to 11%.And the addition of endogenetic particle can significantly improve conjunction
Intensity, the hardness of gold, its synthetic system are main based on stirring addition and fabricated in situ, and at present with the strong Al-Zn- of zinc superelevation high
Mg-Cu systems alloy is less for the research that matrix prepares composite, and how larger with particle size, is combined not enough with basal body interface
Close SiC is even more and is directly carried out in ultra-high-strength aluminum alloy solution as enhancing particle, enhancing particle prepared by original position, certainly will
Certain loss can be caused to the main component element in alloy.The present invention starts with from microstructure design and control, introduces Gao Mo
Amount particle TiB2 prepares the strong aluminum matrix composite of superelevation, further lifts the strength of materials, and significantly improve alloy elastic modulus.Adopt
Composite preparation is carried out with two-step method, it is to avoid directly carry out in Al-Zn-Mg-Cu matrix alloys highly exothermic original position anti-
The scaling loss that reply alloying element is caused, and remain TiB2With the interfacial cleanliness degree and interface cohesion degree of Al matrixes.Using excellent
Homogenization process after change, makes material farthest eliminate segregation before being deformed, and material is made using the extrusion process after optimization
Deformational behavior is excellent, and after further carrying out T6 heat treatments, the TiB in composite2Particle size is smaller and is evenly distributed, and is
The performance of composite provides safeguard.
The content of the invention
It is an object of the invention to overcome zinc ultra-high-strength aluminum alloy high to be absorbed in lifting bottleneck in the too high rear intensity of Zn content, close
Elastic modelling quantity of gold itself is relatively low, and high-modulus TiB is introduced in zinc ultra-high-strength aluminum alloy high2Particle, is prepared compound using two-step method
Material, adjusts TiB2The mass fraction of particle, it is intended to prepare a kind of low-loss, high intensity, the advanced composite material (ACM) of high-modulus.
To achieve the above object, the present invention takes following design.
A kind of TiB2Particle strengthens zinc Al-Zn-Mg-Cu composites high, it is characterised in that：With the Al-Zn- of high zinc content
Mg-Cu alloys are matrix, and mass fraction is 6%-10%, and average-size is less than 1 μm of TiB2It is enhancing particle, matrix alloy
Mass percent component Zn：9-11%, Mg：1.0-2.5%, Cu：1.0-1.5%, Zr：0.05-0.20%, balance of Al.
In composite, TiB2Even particle distribution, matrix strengthening phase nanoscale MgZn2 phases are uniformly distributed in aluminum substrate.
A kind of TiB described above2Particle strengthens the preparation method of zinc Al-Zn-Mg-Cu composites high, and its feature exists
In, composite is prepared using two-step method, will original position prepare particle and separated with matrix alloy founding, it is to avoid directly in Al-
The scaling loss that highly exothermic reaction in-situ is caused to alloying element is carried out in Zn-Mg-Cu matrix alloys；Specifically include following steps：
(1) with aluminium ingot, Al powder, Ti powder, TiO2、H3BO3It is raw material, wherein mol ratio=1 of total Ti/B:4, Al powder, Ti powder
And TiO2Mass ratio be 2:2:3, prepare that mass fraction is higher, average-size is less than 1 μ using melt self- propagating direct synthesis technique
The Al-TiB of m2Intermediate alloy；The main image composition of intermediate alloy is α-Al, TiB2, wherein there is the TiAl of residual3；TiB2With
Basal body interface is clean, and combination degree is high.
(2) with fine aluminium, pure magnesium, pure zinc, Al-50%Cu, Al-4%Zr intermediate alloy as raw material, prepared with step (1)
Al-TiB2Intermediate alloy is matrix, and TiB is adjusted by above-mentioned raw materials2The mass fraction of particle is 6%-10%, in 720-780
Alloy solution is melting at a temperature of DEG C, cast temperature is 720-750 DEG C；
(3) after the composite that step (2) has been cast is cooled down, and carried out at homogenization in 420-470 DEG C/25-45h
Reason, extrudes composite ingot casting at 330-430 DEG C, and extrusion ratio is (15-20):1；
(4) composite board that step (3) has been extruded is carried out into T6 heat treatments, finally obtains TiB2/Al-Zn-Mg-Cu
Composite.
The present invention is prepared for a kind of high elastic modulus TiB2Particle REINFORCED Al-Zn-Mg-Cu composites, optimize compound
The homogenization process and extrusion process of material, solve the segregation problems in endogenetic particle composite ingot casting.And with Gao Xinchao
High strength alumin ium alloy is TiB prepared by matrix2In/Al-Zn-Mg-Cu composites, TiB2Particle distribution area is wide and uniform, size
It is smaller, it is that the performance of composite provides safeguard.
Composite material strength improves 11.4% than matrix alloy, and its image composition is mainly the TiB2 particles of large area, receives
Meter level η ' (MgZn2) phase, elastic modelling quantity is than matrix alloy lifting 45%.
Brief description of the drawings
Fig. 1 is Al-TiB2Intermediate alloy microscopic structure.
Fig. 2 is as cast condition TiB2/ Al-Zn-Mg-Cu composite microscopic structures.
Fig. 3 is homogenization state TiB2/ Al-Zn-Mg-Cu composite microscopic structures.
Fig. 4 is As-extruded TiB2/ Al-Zn-Mg-Cu composite microscopic structures.
Fig. 5 is solid solution state composite microscopic structure.
Fig. 6 is aging state composite microscopic structure.
Specific embodiment
With reference to embodiment, the invention will be further described, but the present invention is not limited to following examples.
Embodiment 1
Two-step method prepares TiB2The process of/Al-Zn-Mg-Cu composites is as follows：
(1) allocation plan of composite is：9.96%TiB2, 10%Zn, 1.9%Mg, 1.7%Cu, 0.12%Zr, it is remaining
It is Al to measure.Wherein Al-TiB2Intermediate alloy is by aluminium ingot, aluminium powder, titanium valve, TiO2、H3BO3Be prepared, wherein total Ti/B mole
Than=1:4, Al powder, Ti powder and TiO2Mass ratio be 2:2:3, high-quality point is prepared using melt self- propagating direct synthesis technique
The Al-TiB2 intermediate alloys of number, average-size less than 1 μm.
(2) it is prepared, wherein total Ti/B=1:4.Al-Zn-Mg-Cu matrix alloys are by fine aluminium ingot, pure zinc ingot, pure magnesium
Ingot, Al-50%Cu and Al-4%Zr intermediate alloys are prepared.
(3) Al-TiB is prepared2Intermediate alloy, weighs TiO on request2、H3BO3, two kinds of powder are well mixed, and 200
DEG C heating two hours, remove H3BO3In moisture.By the TiO after heating2And H3BO3Mixed-powder with require weigh aluminium powder and
Titanium valve is well mixed, and during the powder that will be well mixed is as mould, is pressed into the cylindricality powder agglomates (cylindricality of such as 15 × φ 62.5mm3
Powder agglomates).By mould and coatings of instrument brushing one such as slag spoons, Fe magazine element pollutions are prevented.Melted from graphite crucible
Refining, graphite stirring rod prevents Si from polluting.Aluminium ingot is heated to 780-800 DEG C using well formula resistance furnace, treats that aluminium ingot is completely melt,
Melt is warming up to 900-1000 DEG C, graphite bell jar press-in cylindricality powder agglomates, graphite rod uniform stirring reacts 10min；Reaction is completed
Afterwards, 5min is stood, is skimmed, aluminum melt is poured into warmed-up 250 DEG C of punching block, obtain Al-TiB2Intermediate alloy.
(4) matrix alloy composition fine aluminium ingot, pure zinc ingot, pure magnesium ingot, the Al-TiB that will be designed by step (1)2Close centre
Gold, Al-50%Cu and Al-4%Zr intermediate alloys are matched.The intermediate alloy that step (2) is obtained is carried out again at 780 DEG C
Fusing, adds fine aluminium, pure zinc, aluminum bronze intermediate alloy, aluminium zirconium hardener in order；After metal and intermediate alloy all dissolve,
Take the scum silica frost on solution surface off, when solution temperature reaches 715-735 DEG C, add pure magnesium.To make alloying elements distribution uniform, to molten
Body is stirred, and is refined afterwards, and refining stands 10min at 710-730 DEG C, skims, and melt is cast into warmed-up 250
DEG C punching block in, obtain composite ingot casting.
(5) Homogenization Treatments of 443 DEG C/40h are carried out to the composite ingot casting for obtaining.
(6) the composite ingot casting after Homogenization Treatments is extruded, extrusion temperature is 400 DEG C, and extrusion ratio is 16:1.
(7) T6 heat treatments (120 DEG C/24h of solid solution 460 DEG C/2h+ timeliness) are carried out to the composite after extruding.
(8) TiB obtained by the method2/ Al-Zn-Mg-Cu composites have the advantages such as high-modulus, high intensity.
The matrix alloy of table 1 and composite material strength elastic modelling quantity contrast table.
Claims (3)
1. a kind of TiB2Particle strengthens zinc Al-Zn-Mg-Cu composites high, it is characterised in that：With the Al-Zn-Mg- of high zinc content
Cu alloys are matrix, and mass fraction is 6%-10%, and average-size is less than 1 μm of TiB2It is enhancing particle, matrix alloy matter
Amount percentage component Zn：9-11%, Mg：1.0-2.5%, Cu：1.0-1.5%, Zr：0.05-0.20%, balance of Al.
2. according to the TiB described in claim 12Particle strengthens zinc Al-Zn-Mg-Cu composites high, it is characterised in that TiB2
Grain is evenly distributed, and matrix strengthening phase nanoscale MgZn2 phases are uniformly distributed in aluminum substrate.
3. the TiB described in claim 1 is prepared2The method that particle strengthens zinc Al-Zn-Mg-Cu composites high, it is characterised in that：
Composite is prepared using two-step method, will original position prepare particle and separated with matrix alloy founding；Specifically include following step
Suddenly：
(1) with aluminium ingot, Al powder, Ti powder, TiO2、H3BO3It is raw material, wherein mol ratio=1 of total Ti/B:4, Al powder, Ti powder and
TiO2Mass ratio be 2:2:3, prepare that mass fraction is higher, average-size is less than 1 μm using melt self- propagating direct synthesis technique
Al-TiB2Intermediate alloy；The main image composition of intermediate alloy is α-Al, TiB2, wherein there is the TiAl of residual3；TiB2With base
Body interface is clean, and combination degree is high.
(2) with fine aluminium, pure magnesium, pure zinc, Al-50%Cu, Al-4%Zr intermediate alloy as raw material, with the Al- prepared in step (1)
TiB2Intermediate alloy is matrix, and TiB is adjusted by above-mentioned raw materials2The mass fraction of particle is 6%-10%, in 720-780 DEG C of temperature
Alloy solution is melting under degree, cast temperature is 720-750 DEG C；
(3) after the composite that step (2) has been cast is cooled down, and Homogenization Treatments are carried out in 420-470 DEG C/25-45h, it is right
Composite ingot casting is extruded at 330-430 DEG C, and extrusion ratio is (15-20):1；
(4) composite board that step (3) has been extruded is carried out into T6 heat treatments, finally obtains TiB2/ Al-Zn-Mg-Cu is combined
Material.
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| CN201710022771.4A CN106834833A (en) | 2017-01-12 | 2017-01-12 | The strong TiB of a kind of high-modulus, superelevation2Particle REINFORCED Al Zn Mg Cu composites and preparation method thereof |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109576526A (en) * | 2018-12-27 | 2019-04-05 | 吉林大学 | A kind of molten internal in-situ multiphase mixes scale ceramic reinforced Al-Zn-Mg-Cu aluminium alloy and preparation method thereof |
| CN109957685A (en) * | 2019-04-19 | 2019-07-02 | 大连科天新材料有限公司 | A kind of high dispersive TiB2/ A356 composite material and preparation method thereof |
| CN110016597A (en) * | 2019-04-19 | 2019-07-16 | 大连科天新材料有限公司 | A kind of TiB2Particle enhances ultra-high-strength aluminum alloy composite material and homogenizes preparation method |
| CN110205527A (en) * | 2019-06-28 | 2019-09-06 | 江西理工大学 | A kind of increasing material manufacturing Al-Mg-Si alloy wire rod and preparation method thereof |
| CN111500908A (en) * | 2020-06-05 | 2020-08-07 | 威海万丰镁业科技发展有限公司 | Ultrahigh-strength ultrafine-grained TiB2Reinforced Al-Zn-Mg-Cu composite material and preparation |
| CN114000005A (en) * | 2021-11-03 | 2022-02-01 | 大连理工大学 | Based on TiB2pLow-sag large-span power transmission conductor made of/Al composite material and preparation method thereof |
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| CN106367644A (en) * | 2016-09-23 | 2017-02-01 | 北京工业大学 | Super-high strength and high hardness TiB2 particle reinforced Al-Zn-Mg-Cu composite material and preparation method thereof |
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| CN102337423A (en) * | 2011-11-02 | 2012-02-01 | 中南大学 | Preparation method of ceramic-powder-enhanced zinc-aluminum alloy based composite material |
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109576526A (en) * | 2018-12-27 | 2019-04-05 | 吉林大学 | A kind of molten internal in-situ multiphase mixes scale ceramic reinforced Al-Zn-Mg-Cu aluminium alloy and preparation method thereof |
| CN109957685A (en) * | 2019-04-19 | 2019-07-02 | 大连科天新材料有限公司 | A kind of high dispersive TiB2/ A356 composite material and preparation method thereof |
| CN110016597A (en) * | 2019-04-19 | 2019-07-16 | 大连科天新材料有限公司 | A kind of TiB2Particle enhances ultra-high-strength aluminum alloy composite material and homogenizes preparation method |
| CN110205527A (en) * | 2019-06-28 | 2019-09-06 | 江西理工大学 | A kind of increasing material manufacturing Al-Mg-Si alloy wire rod and preparation method thereof |
| CN110205527B (en) * | 2019-06-28 | 2020-05-05 | 江西理工大学 | Al-Mg-Si alloy wire for additive manufacturing and preparation method thereof |
| CN111500908A (en) * | 2020-06-05 | 2020-08-07 | 威海万丰镁业科技发展有限公司 | Ultrahigh-strength ultrafine-grained TiB2Reinforced Al-Zn-Mg-Cu composite material and preparation |
| CN114000005A (en) * | 2021-11-03 | 2022-02-01 | 大连理工大学 | Based on TiB2pLow-sag large-span power transmission conductor made of/Al composite material and preparation method thereof |
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