CN110180913A - A method of improving Mg/Al linkage interface performance - Google Patents
A method of improving Mg/Al linkage interface performance Download PDFInfo
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- CN110180913A CN110180913A CN201910401576.1A CN201910401576A CN110180913A CN 110180913 A CN110180913 A CN 110180913A CN 201910401576 A CN201910401576 A CN 201910401576A CN 110180913 A CN110180913 A CN 110180913A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/02—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of sheets
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
- B22D17/007—Semi-solid pressure die casting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B37/00—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding
- B32B37/06—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the heating method
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B37/00—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding
- B32B37/10—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the pressing technique, e.g. using action of vacuum or fluid pressure
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- 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
- C22C32/0052—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 carbides
- C22C32/0063—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 carbides based on SiC
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
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Abstract
A kind of high-strength highly-conductive Cu-Ag-Sc alloy and preparation method thereof.SiC particles reinforced is introduced mutually to improve the method for the bed boundary Mg/Al by designing composite material middle layer the invention discloses a kind of, is related to a kind of preparation method for improving magnesium/aluminium interface performance " aluminium/aluminum matrix composite/magnesium/aluminum matrix composite/aluminium " stratified material.This method uses Semi-solid Stirring casting to prepare the equally distributed SiCp reinforced aluminum matrix composites of particle first, and then carries out hot rolling, has obtained the excellent aluminum matrix composite constituent element plate of matrix grain detailed performance.Then hot pressing is carried out to the metal laminate stacked with " aluminium/aluminum matrix composite/magnesium/aluminum matrix composite/aluminium " order and annealed.On the one hand this hair generates dispersion-strengtherning and refined crystalline strengthening effect to constituent element layer metal, on the other hand improve the obdurability of interface zone, can significantly improve the comprehensive performance of composite plate.
Description
Technical field
The present invention relates to a kind of improvement magnesium/aluminium interface performances " aluminium/aluminum matrix composite/magnesium/aluminum matrix composite/aluminium "
The preparation method of stratified material.
Background technique
In engineer application, magnesium and magnesium alloy are there are intensity, rigidity are low, the disadvantages such as corrosion resistance, temperature-room type plasticity difference, especially
The corrosion resistance of difference is to limit its widely applied one of the main reasons.Magnesium/aluminium laminar composite protect magnesium alloy from
The various feature performance benefits that magnesium alloy and aluminium alloy are taken into account while corrosion, are widely used.More at present is using explosive welding
The preparation such as method, roll-bonding method.High pressure that explosive welding process is instantaneously generated by explosive charge, high fever realize that plate is securely tied
It closes, so its unstable product quality, production efficiency is lower and seriously polluted, thus is not suitable for popularization and volume production；And it uses and rolls
Composite algorithm (mainly hot rolling) processed can not regulate and control the Mg generated after rolling at interface17Al12, Mg2Al3Equal brittle intermetallics
Object.The current existing research to Mg/Al laminar composite focuses mostly on improving technological parameter, and the present invention passes through design
Middle layer introduces SiCp to regulate and control the form and microscopic structure of bed boundary phase, and uses this preparation of the pressure sintering of simple process
Method there is no report at present.
Summary of the invention
In order to solve the above-mentioned technical problem, the present invention adopts the following technical scheme:
The present invention seriously affects plate for Mg/Al laminated composite plate preparation process median surface intermetallic compound and combines by force
The problems such as degree, mechanical property, and introduce enhancing aluminum-base composite material by silicon carbide particles plate and do middle layer, utilize silicon-carbide particle
(SiCp) there is the Mg/Al stratiform of the intermetallic compounds layer of fine uniform distribution to the regulating and controlling effect preparation of intermetallic compound
Composite material.
The present invention is directed to existing production technology complexity, the unstable product quality, interface for preparing Mg/Al laminated composite plate
The problem of poor bonding strength, provides a kind of hot pressing composite algorithm that combination interface is controllable.
The preparation method of the regulatable Mg/Al laminar composite in median surface of the present invention is implemented according to the following steps: one, preparation
Enhancing aluminum-base composite material by silicon carbide particles (SiCp/AMCs)；Two, aluminum matrix composite made from the first step (AMCs) is carried out
Rolling；Three, removing surface is carried out to Al, AMCs, Mg；Four, by Al, AMCs, Mg after cleaning with Al/AMCs/Mg/AMCs/Al
Form stack；Five, composite plate is placed in hot pressing die, hot pressing is carried out；Six, composite plate obtained by hot pressing is carried out at annealing
It manages to get the Mg/Al laminar composite being distributed to compound fine uniform between interface metal.
The preparation method of the Mg/Al laminar composite in the first step, casts legal system using Semi-solid Stirring
Standby AMCs, is passed through Ar+CO before Al is completely melt2Mixed gas, about 100 DEG C of (760 DEG C) heat preservation 1h more than aluminium alloy fusing point,
Al is completely melt.Then be cooled to semisolid (temperature range is about 550-640 DEG C), according to the big minor adjustment temperature of melt vortex ±
10 DEG C, SiCp is doped in Al melt by mechanical mixing method, and mechanical stirring rate is that 300~1000rpm (is vortexed according to melt
Big minor adjustment), positive and negative rotation is alternately.After SiCp doping completely, the homogenization stirring+10min stirring for carrying out 15-30min is removed
Gas process.
The preparation method of the Mg/Al laminar composite, in the first step, by melt during stirring degassing
About 100 DEG C of (760 DEG C) heat preservation 10min of Al fusing point or more are heated to, melt is poured into die casting, lotus is determined in setting step by step:
100kN/5s+450kN/180s, select general resistance to compression: speed 0.5mm/s moves back mould, obtains SiCp/AMCs.
The preparation method of the Mg/Al laminar composite, in the second step, at 400-450 DEG C with 2-5m/s's
Speed carries out the hot rolling of n passage to 3-5mm thickness die casting AMCs.
The preparation method of the Mg/Al laminar composite, in the third step, Mg can be replaced with AZ31B or pure magnesium,
Al can be replaced with 2024 or fine aluminium.
The preparation method of the Mg/Al laminar composite, in the third step, specific manner of cleaning up be to Mg, Al,
AMCs plate surface is polished with 80 mesh coarse sandpapers, is then cleaned by ultrasonic and is dried in alcohol；Or plate table is cleaned with acetone
Face greasy dirt, then plate is put into 10%NaOH solution and cleans 30s, then is dried with distilled water flushing, and with wire brush to surface
It polishes.
The preparation method of the Mg/Al laminar composite, in the 4th step, Al, AMCs and Mg thickness ratio are as follows: 1:
0.5-1:2。
The preparation method of the Mg/Al laminar composite, in the 5th step, hot pressing under the conditions of 400-450 DEG C,
It is arranged and determines lotus step by step: the pressure pressure maintaining 30min of the subsequent 600kN of pressure pressure maintaining 30-60min of 1000kN.
The preparation method of the Mg/Al laminar composite in the 6th step, is annealed in 250-350 DEG C/2h condition
Lower progress.
The preparation method of the Mg/Al laminar composite, in the first step, it is quality point that aluminium alloy, which matches material,
Number 4.03%Cu, 1.54%Mg, 0.145%Si, 0.19%Fe, 0.55%Mn and 93.545%Al.
The preparation method of the Mg/Al laminar composite, in the first step, silicon-carbide particle is having a size of diameter 10
μm, grain volume fraction is 5~20%.
In the first step, measured silicon-carbide particle is placed in for the preparation method of the Mg/Al laminar composite
In drying oven, 600 DEG C are risen to furnace and keeps the temperature 1-3h.
Die casting in the first step, is preheating to 150 DEG C by the preparation method of the Mg/Al laminar composite
And brush graphite oil, it is then preheating to 400 DEG C and keeps the temperature 1-3h.
The preparation method of the Mg/Al laminar composite in the first step, is using Semi-solid Stirring casting
Before preparing aluminum matrix composite, in the uniform brushing talcum powder of inner surface of crucible, ZnO.
Beneficial effects of the present invention:
The present invention obtains the two sides that the aluminium alloy with excellent corrosion resistance and superior plasticity and same lightweight is covered in magnesium material
The magnalium laminate of Mg, Al alloy advantage must be had both.But in process because interface inevitably generates brittleness gold
Compound (such as Mg between category17Al12, Mg2Al3Deng), cause sheet material forming ability poor.In order to improve interface state to improve plate
Forming capacity, introduce SiCp/AMCs between Mg/Al plate, be prepared for " Al/AMCs/Mg/AMCs/Al " composite plate.SiCp
Have following effect: one, SiCp reinforcement can further improve the elasticity modulus of plate, and elevated temperature strength makes it be expected to apply more
In high temperature environment；Two, SiCp the refinement effect of constituent element layer metal grain can be improved the intensity and plasticity of plate；Three,
SiCp has regulating and controlling effect to intermetallic compound, it is made to be changed into tiny interrupted shape, this non-continuous state from coarse sequential like
Distribution can limit propagation of the crackle on interface to a certain extent, improve the obdurability of interface zone, and then improve multiple
The binding performance of plywood.
And the present invention introduces SiCp by design middle layer to regulate and control the form and microscopic structure of bed boundary phase, and uses
This preparation method of the pressure sintering of simple process, there is no report at present.
Compared with prior art, the invention proposes a kind of preparation sides of the regulatable Mg/Al laminar composite in interface
Method, the first step are prepared for SiCp/AMCs, are uniformly introduced into SiCp in aluminium alloy by Semi-solid Stirring casting；Second step pair
AMCs obtained by the first step carries out hot rolling, has effectively refined alloy matrix aluminum crystal grain, and improve casting flaw.5th step
Lotus hot pressing is determined to laminated plate progress step by step, makes to form more firm metallurgical bonding between magnalium laminate, and SiCp this increasing
The presence of strong body not only plays dispersion-strengtherning and refined crystalline strengthening effect, but also compound between controllable interface metal to constituent element plate
Form and boundary layer microscopic structure (as shown in figures 1 and 2), hinder propagation of the crackle on interface to a certain extent, improve
The obdurability of interface zone, and then improve the comprehensive performance of composite plate.
Detailed description of the invention
Fig. 1 is by composite plate section macrograph made from specific embodiment one, wherein figure (a) is Al/AMCs/Mg/
AMCs/Al composite plate section macrograph, figure (b) are Al/Mg/Al composite plate section macrograph.
Fig. 2 is by composite plate cross-sectional scans figure made from specific embodiment one, wherein figure (a) is that the interface AMCs/Mg is swept
Tracing and corresponding EDS linear sweep graph, figure (b) are Al/Mg interface scanning figure and corresponding EDS linear sweep graph；
Fig. 3 is by composite plate different location Vickers hardness variation diagram made from specific embodiment one, and (a) is Al/ in figure
Each constituent element plate center AMCs/Mg/AMCs/Al and the variation of interface Vickers hardness, (b) are each constituent element plate center Al/Mg/Al and boundary
Vickers hardness changes at face
Specific embodiment
With reference to the accompanying drawing and specific embodiment is further elaborated the contents of the present invention, but embodiment is only this
The better embodiment of invention, therefore all equivalence changes done according to feature described in present patent application range and principle,
It is included in the scope of the patent application of the present invention.
Specific embodiment 1: present embodiment is a kind of method of introducing SiCp reinforced phase improvement bed boundary Mg/Al, tool
Body carries out according to the following steps:
One, prepare SiCp/AMCs.10 μm of SiCp partial size, grain volume fraction 10% sets measured silicon-carbide particle
In drying oven, 600 DEG C are risen to furnace and keeps the temperature 2-3h.Die casting is preheating to 150 DEG C and brush graphite oil, is then preheating to
400 DEG C and keep the temperature 1-3h.Before preparing AMCs, in the uniform brushing talcum powder of inner surface of crucible, ZnO, to block crucible and melt
Between possible reaction.AMCs is prepared using Semi-solid Stirring casting, Ar+CO2 mixing is passed through before aluminium alloy is completely melt
Gas, about 100 DEG C of (760 DEG C) heat preservation 1h, aluminium alloy are completely melt more than aluminium alloy fusing point.Then it is cooled to semisolid (temperature
Spending section is about 550-640 DEG C), according to big minor adjustment temperature ± 10 DEG C of melt vortex, SiCp is doped to by mechanical mixing method
In aluminium alloy melt, mechanical stirring rate is 300~1000rpm, and positive and negative rotation is alternately.After SiCp doping completely, 15- is carried out
Homogenization stirring+10min stirring degassing the process of 30min.During stirring degassing by melt be heated to aluminium alloy fusing point with
Upper about 100 DEG C (760 DEG C) heat preservation 10min, melt is poured into die casting, and lotus is determined in setting step by step: 100N/5S+450N/
180s, then select general resistance to compression: speed 0.5mm/s moves back mould, obtains SiCp/AMCs.
Two, SiCp/AMCs made from the first step is rolled.In the 400-450 DEG C of speed with 2-5m/s, to 4mm thickness
Die casting aluminum matrix composite carries out 5 passage hot rollings.
Three, to Al, Mg, AMCs removing surface.It is polished with 80 mesh coarse sandpapers, and is cleaned by ultrasonic in alcohol.
Four, Al, Mg, AMCs after cleaning are stacked in the form of Al/AMCs/Mg/AMCs/Al, wherein Al, AMCs, Mg
Thickness ratio are as follows: 1:0.5-1:2.
Five, the composite plate after taking out annealing is placed in hot pressing die, carries out hot pressing.Hot pressing under the conditions of 400-450 DEG C, if
It sets and determines lotus step by step: the pressure pressure maintaining 30min of the subsequent 600kN of pressure pressure maintaining 30-60min of 1000kN.
Six, by the annealing under the conditions of 250-350 DEG C/2h of the progress of composite plate obtained by hot pressing to get between interface metal
Magnesium/aluminium laminar composite of compound fine uniform distribution.
Specific embodiment 2: the present embodiment is different from the first embodiment in that described in step 1 spherical
SiCp volume fraction is 5%, other are same as the specific embodiment one.
Specific embodiment 3: the present embodiment is different from the first embodiment in that described in step 1 spherical
SiCp volume fraction is 15%, other are same as the specific embodiment one.
Specific embodiment 4: the present embodiment is different from the first embodiment in that rolling temperature described in step 2
Degree is 400 DEG C, other are same as the specific embodiment one.
Specific embodiment 5: the present embodiment is different from the first embodiment in that Al, AMCs, Mg are thick in step 4
Spend ratio are as follows: other are same as the specific embodiment one by 0.3:0.5:2.
Specific embodiment 6: the present embodiment is different from the first embodiment in that Al, AMCs, Mg are thick in step 4
Spend ratio are as follows: other are same as the specific embodiment one by 0.3:1:2.
Above-mentioned aluminum or aluminum alloy used is all business fine aluminiums and aluminium alloy plate that can be plastically deformed, as 1A99,2A12,
6061,5052 etc.
As shown in Figure 1, for by composite plate section macrograph made from specific embodiment one, wherein figure (a) is Al/
AMCs/Mg/AMCs/Al composite plate section macrograph, figure (b) are Al/Mg/Al composite plate section macrograph；It can from figure
Out, Al/AMCs/Mg/AMCs/Al composite plate linkage interface out-of-flatness forms the rippled interface being mutually embedded between each constituent element plate,
Its bond strength is connected much larger than the straight interface of Al/Mg/Al composite plate.
As shown in Fig. 2, for by composite plate cross-sectional scans figure made from specific embodiment one, wherein figure (a) is AMCs/Mg
Interface scanning figure and corresponding EDS linear sweep graph, figure (b) are Al/Mg interface scanning figure and corresponding EDS linear sweep graph；It can from figure
To find out, after grained silicon carbide is added, interface diffusion layer thickness is obviously thinned, and the presence of grained silicon carbide has regulated and controled interface metal
Between compound tissue.
As shown in figure 3, for by composite plate different location Vickers hardness variation diagram made from specific embodiment one, wherein scheming
(a) change for each constituent element plate center Al/AMCs/Mg/AMCs/Al and interface Vickers hardness, figure (b) is each constituent element of Al/Mg/Al
Plate center and the variation of interface Vickers hardness；It can be seen from the figure that Al/AMCs/Mg/AMCs/Al composite plate different location is tieed up
Family name's hardness number is all larger than Al/Mg/Al composite plate, and the introducing of composite layer greatly improves the whole strong hardness of composite plate.
Finally, it should be noted that the foregoing is only a preferred embodiment of the present invention, it is not intended to restrict the invention,
Although the present invention is described in detail referring to the foregoing embodiments, for those skilled in the art, still may be used
To modify the technical solutions described in the foregoing embodiments or equivalent replacement of some of the technical features.
All within the spirits and principles of the present invention, any modification, equivalent replacement, improvement and so on should be included in of the invention
Within protection scope.
Claims (10)
1. a kind of method for improving Mg/Al linkage interface performance, which is characterized in that introduce SiC particle-reinforced Al matrix composite wood
Flitch does middle layer, prepares the magnesium/aluminium laminar composite with the intermetallic compounds layer of fine uniform distribution.
2. a kind of method for improving Mg/Al linkage interface performance according to claim 1, which is characterized in that the magnesium/aluminium
The preparation method of laminar composite is implemented according to the following steps:
(1) enhancing aluminum-base composite material by silicon carbide particles is prepared；
(2) aluminum matrix composite is rolled；
(3) removing surface is carried out to aluminium, aluminum matrix composite, magnesium；
(4) by after cleaning aluminium, aluminum matrix composite, magnesium is with aluminium/aluminum matrix composite/magnesium/aluminum matrix composite/aluminium shape
Formula is stacked into composite plate；
(5) composite plate is placed in hot pressing die, carries out hot pressing；
(6) by composite plate obtained by hot pressing make annealing treatment to get the magnesium being distributed to compound fine uniform between interface metal/
Aluminium laminar composite.
3. a kind of method for improving Mg/Al linkage interface performance according to claim 2, which is characterized in that described first
In step, aluminum matrix composite, specific preparation step are prepared using Semi-solid Stirring casting are as follows: be passed through Ar before aluminium is completely melt
+CO2Mixed gas, about 100 DEG C of heat preservation 1h, aluminium alloy are completely melt more than aluminium alloy fusing point；
It then is cooled to semisolid, according to big minor adjustment temperature ± 10 DEG C of melt vortex, silicon-carbide particle passes through mechanical mixing method
It is doped in aluminium alloy melt, mechanical stirring rate is 300~1000rpm, and positive and negative rotation is alternately.Silicon-carbide particle has adulterated
Quan Hou carries out the homogenization stirring+10min stirring degassing process of 15-30min；
Melt is heated to about 100 DEG C of heat preservation 10min of aluminium alloy fusing point or more during stirring degassing, melt is poured into die casting
In mold, lotus is determined in setting step by step: 100kN/5s+450kN/180s, select general resistance to compression: speed 0.5mm/s moves back mould, is carbonized
Silicon particle intensifying aluminum based compound material.
4. a kind of method for improving Mg/Al linkage interface performance according to claim 2, which is characterized in that described second
In step, in the 400-450 DEG C of speed with 2-5m/s, the hot rolling of n passage is carried out to 3-5mm thickness die casting aluminum matrix composite.
5. a kind of method for improving Mg/Al linkage interface performance according to claim 2, which is characterized in that the third
In step, magnesium is AZ31B or pure magnesium, and aluminium is 2024 or fine aluminium；Specific cleaning method are as follows: to magnesium, aluminium, aluminum-based composite material plate table
Face is polished with 80 mesh coarse sandpapers, is then cleaned by ultrasonic and is dried in alcohol.
6. a kind of method for improving Mg/Al linkage interface performance according to claim 2, which is characterized in that the described 4th
In step, aluminium, aluminum matrix composite and magnesium thickness ratio are as follows: 1:0.5-1:2.
7. a kind of method for improving Mg/Al linkage interface performance according to claim 2, which is characterized in that the described 5th
In step, under the conditions of 400-450 DEG C, lotus is determined in setting step by step: the pressure of the subsequent 600kN of pressure pressure maintaining 30-60min of 1000kN for hot pressing
It tries hard to keep and presses 30min；In 6th step, annealing carries out under the conditions of 250-350 DEG C/2h.
8. a kind of method for improving Mg/Al linkage interface performance according to claim 3, which is characterized in that the aluminium closes
Gold proportion material is mass fraction 4.03%Cu, 1.54%Mg, 0.145%Si, 0.19%Fe, 0.55%Mn and 93.545%
Al。
9. a kind of method for improving Mg/Al linkage interface performance according to claim 3, which is characterized in that described compound
For silicon-carbide particle having a size of 10 μm of diameter, it is 5 that silicon-carbide particle, which accounts for silicon carbide and the volume fraction of aluminium alloy total volume, in material
~20%.The silicon-carbide particle is placed in drying oven in advance, rise to 600 DEG C with furnace and keeps the temperature 1-3h, is then doped to aluminium
It is stirred in alloy melt.
10. a kind of method for improving Mg/Al linkage interface performance according to claim 3, which is characterized in that in advance by institute
It states die casting and is preheating to 150 DEG C and brush graphite oil, be then preheating to 400 DEG C and keep the temperature 1-3h.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111136277A (en) * | 2019-12-03 | 2020-05-12 | 同济大学 | Multilayer aluminum/magnesium composite board and powder hot-pressing preparation method thereof |
| CN111318801A (en) * | 2020-03-09 | 2020-06-23 | 中南大学 | Intermetallic compound based on high-entropy alloy diffusion welding and preparation method thereof |
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| CN110180913B (en) | 2020-10-23 |
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