CN109554570A - A kind of molten internal in-situ multiphase mixes the method for scale ceramic reinforced aluminium alloy - Google Patents
A kind of molten internal in-situ multiphase mixes the method for scale ceramic reinforced aluminium alloy Download PDFInfo
- Publication number
- CN109554570A CN109554570A CN201811607747.8A CN201811607747A CN109554570A CN 109554570 A CN109554570 A CN 109554570A CN 201811607747 A CN201811607747 A CN 201811607747A CN 109554570 A CN109554570 A CN 109554570A
- Authority
- CN
- China
- Prior art keywords
- aluminium alloy
- powder
- alloy
- crucible
- temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 132
- 239000000919 ceramic Substances 0.000 title claims abstract description 54
- 238000011065 in-situ storage Methods 0.000 title claims abstract description 50
- 238000000034 method Methods 0.000 title claims abstract description 41
- 239000000956 alloy Substances 0.000 claims abstract description 72
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 65
- 239000002245 particle Substances 0.000 claims abstract description 61
- 229910001069 Ti alloy Inorganic materials 0.000 claims abstract description 37
- 238000006243 chemical reaction Methods 0.000 claims abstract description 28
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 27
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 27
- 238000010907 mechanical stirring Methods 0.000 claims abstract description 16
- 238000002156 mixing Methods 0.000 claims abstract description 15
- 239000000843 powder Substances 0.000 claims description 133
- 239000010936 titanium Substances 0.000 claims description 95
- 239000007788 liquid Substances 0.000 claims description 59
- 229910052719 titanium Inorganic materials 0.000 claims description 31
- 239000012459 cleaning agent Substances 0.000 claims description 29
- 239000004411 aluminium Substances 0.000 claims description 24
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 22
- 238000002844 melting Methods 0.000 claims description 19
- 230000008018 melting Effects 0.000 claims description 19
- 238000009210 therapy by ultrasound Methods 0.000 claims description 19
- 238000004321 preservation Methods 0.000 claims description 18
- 239000000523 sample Substances 0.000 claims description 18
- 238000010792 warming Methods 0.000 claims description 17
- 238000005266 casting Methods 0.000 claims description 16
- 239000004615 ingredient Substances 0.000 claims description 15
- 238000002360 preparation method Methods 0.000 claims description 14
- 238000003756 stirring Methods 0.000 claims description 12
- 239000000463 material Substances 0.000 claims description 11
- 229910052749 magnesium Inorganic materials 0.000 claims description 10
- 238000000498 ball milling Methods 0.000 claims description 9
- 239000002893 slag Substances 0.000 claims description 9
- 239000005030 aluminium foil Substances 0.000 claims description 8
- 238000002791 soaking Methods 0.000 claims description 8
- 229910000831 Steel Inorganic materials 0.000 claims description 6
- 239000010959 steel Substances 0.000 claims description 6
- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 claims description 4
- 229910033181 TiB2 Inorganic materials 0.000 claims description 4
- 230000004913 activation Effects 0.000 claims description 3
- 239000011159 matrix material Substances 0.000 abstract description 19
- 238000005728 strengthening Methods 0.000 abstract description 10
- 230000003014 reinforcing effect Effects 0.000 abstract description 9
- 238000005275 alloying Methods 0.000 abstract description 4
- 238000002604 ultrasonography Methods 0.000 abstract description 4
- 230000002939 deleterious effect Effects 0.000 abstract description 2
- 230000000977 initiatory effect Effects 0.000 abstract description 2
- 230000000295 complement effect Effects 0.000 abstract 1
- 239000008187 granular material Substances 0.000 abstract 1
- BPJYAXCTOHRFDQ-UHFFFAOYSA-L tetracopper;2,4,6-trioxido-1,3,5,2,4,6-trioxatriarsinane;diacetate Chemical compound [Cu+2].[Cu+2].[Cu+2].[Cu+2].CC([O-])=O.CC([O-])=O.[O-][As]1O[As]([O-])O[As]([O-])O1.[O-][As]1O[As]([O-])O[As]([O-])O1 BPJYAXCTOHRFDQ-UHFFFAOYSA-L 0.000 description 13
- KLZUFWVZNOTSEM-UHFFFAOYSA-K Aluminium flouride Chemical compound F[Al](F)F KLZUFWVZNOTSEM-UHFFFAOYSA-K 0.000 description 12
- TWRXJAOTZQYOKJ-UHFFFAOYSA-L Magnesium chloride Chemical compound [Mg+2].[Cl-].[Cl-] TWRXJAOTZQYOKJ-UHFFFAOYSA-L 0.000 description 12
- CDBYLPFSWZWCQE-UHFFFAOYSA-L Sodium Carbonate Chemical compound [Na+].[Na+].[O-]C([O-])=O CDBYLPFSWZWCQE-UHFFFAOYSA-L 0.000 description 12
- 238000000875 high-speed ball milling Methods 0.000 description 12
- 230000000052 comparative effect Effects 0.000 description 9
- 239000011777 magnesium Substances 0.000 description 9
- 229910052751 metal Inorganic materials 0.000 description 9
- 239000002184 metal Substances 0.000 description 9
- 239000010935 stainless steel Substances 0.000 description 9
- 229910001220 stainless steel Inorganic materials 0.000 description 9
- 238000007670 refining Methods 0.000 description 8
- 239000002105 nanoparticle Substances 0.000 description 7
- 229910020056 Mg3N2 Inorganic materials 0.000 description 6
- 229910001610 cryolite Inorganic materials 0.000 description 6
- 238000001035 drying Methods 0.000 description 6
- 238000000227 grinding Methods 0.000 description 6
- VHHHONWQHHHLTI-UHFFFAOYSA-N hexachloroethane Chemical compound ClC(Cl)(Cl)C(Cl)(Cl)Cl VHHHONWQHHHLTI-UHFFFAOYSA-N 0.000 description 6
- 229910001629 magnesium chloride Inorganic materials 0.000 description 6
- 238000000465 moulding Methods 0.000 description 6
- 229910000029 sodium carbonate Inorganic materials 0.000 description 6
- 238000007872 degassing Methods 0.000 description 5
- 239000011812 mixed powder Substances 0.000 description 5
- 238000005303 weighing Methods 0.000 description 5
- 238000003723 Smelting Methods 0.000 description 4
- 239000006185 dispersion Substances 0.000 description 4
- 238000002485 combustion reaction Methods 0.000 description 3
- 239000002131 composite material Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 230000005611 electricity Effects 0.000 description 3
- 239000000376 reactant Substances 0.000 description 3
- 229910000632 Alusil Inorganic materials 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910018566 Al—Si—Mg Inorganic materials 0.000 description 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- MCMNRKCIXSYSNV-UHFFFAOYSA-N ZrO2 Inorganic materials O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910052571 earthenware Inorganic materials 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000010406 interfacial reaction Methods 0.000 description 1
- 229910001234 light alloy Inorganic materials 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 229910052573 porcelain Inorganic materials 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
Classifications
-
- 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
-
- 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
- C22C1/1005—Pretreatment of the non-metallic additives
- C22C1/1015—Pretreatment of the non-metallic additives by preparing or treating a non-metallic additive preform
-
- 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
- C22C1/1052—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites by mixing and casting metal matrix composites with reaction
-
- 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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- 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
Abstract
The invention discloses a kind of methods that molten internal in-situ multiphase mixes scale ceramic reinforced aluminium alloy, prepare Al-Ti-B by mixing, cold moudling4C-BN system reacts green compact, intracorporal reaction in-situ and dispersed ceramic particle are melted followed by the pre-dispersed method initiation of parcel complementary melt endoparticle, whole aluminium alloys, mechanical stirring and ultrasound are finally mixed, the Al-Si-Mg-Ti alloy that multiphase mixes size granule reinforcing is obtained after refinery by de-gassing.In the Al-Si-Mg-Ti alloy for the in-situ endogenic particle strengthening prepared by this method, the ceramic particle of interior life and the interface cohesion of alloy matrix aluminum are good, clean interfaces are pollution-free, and ceramic particle is uniformly dispersed in the base, and the mechanical property of Al-Si-Mg-Ti alloy is significantly improved；Meanwhile this method can save tooling loss, avoid alloying element burning, be a kind of method of reinforcing Al-Si-Mg-Ti alloy that is economic and environment-friendly, efficiently and without deleterious interfacial reacting.
Description
Technical field
The invention belongs to aluminium alloy and reinforced aluminium alloy technical field, in particular to a kind of molten internal in-situ multiphase mixes ruler
Spend the method for ceramic reinforced aluminium alloy.
Background technique
Increasingly developed with traffic transport industry, requirement of the people to material various aspects of performance constantly improves, and matter
Light inexpensive aluminium alloy is still the important light alloy material of current transportation.But traditional single aluminium alloy is increasingly
It is unable to satisfy the growing demand of modern science and technology.Therefore, nowadays the Composite of aluminum alloy materials has become material supply section
It learns and develops one of trend the most significant.Ceramic particle specific strength height, corrosion resistance and good, as reinforced phase to composite material tape
Higher intensity, corrosion-resistant, abrasion resistance properties are come, there is important development prospect.In general, particle enhanced aluminum-based composite material
There are two ways to, it outer addition and interior thinks of a way.Outer addition is a kind of method of traditional introducing particle, and ceramic particle is additionally to make
For what is come out, and it is added in melt by stirring casting method etc.；And this method has certain limitation, such as ceramic particle
The bad caused interface of wetability between matrix is easy to pollute, and chemical reaction is easy to produce between interface.And interior generation method is
It is a kind of it is possible to prevente effectively from these unnecessary reactions method.In this method, particle is by the heat release between various elements
Reaction, born in melt internal in-situ, particle is pollution-free with melt interface, is easier to obtain tiny and be evenly distributed on molten
Reinforced phase in body.The in-situ endogenic method of this initiation reaction direct in the melt can be to avoid the dirt between melt and interface
Dye, the wetability in aluminum substrate of particle are improved.
But the temperature of required melt environment is higher when causing reaction in-situ in the melt due to ceramic particle, if all closing
When golden liquid is at higher temperature, energy loss is big, lower melting-point alloying element in aluminium alloy after held for some time
Such as the easy scaling loss of magnesium elements, and higher smelting temperature is also larger to the loss of tooling device, and has certain risk.
Summary of the invention
The object of the present invention is to provide a kind of methods that molten internal in-situ multiphase mixes scale ceramic reinforced aluminium alloy, lead to
It crosses in parcel in alloy melt and causes that Al-Ti-B4C-BN system is in situ to react from climing combustion, multiphase is micro-nano mixes size for generation
TiCN, TiB2, AlN ceramic particle, particle is pre-dispersed in parcel in melt；It can be avoided alloying element scaling loss, improve pottery
The dispersion effect of porcelain particle；Rationally control the amount and intensified condition of the powder green compact added in aluminium alloy excessively simultaneously；It can be significant
Improve the mechanical property of aluminium alloy.
Technical solution provided by the invention are as follows:
A kind of molten internal in-situ multiphase mixes the method for scale ceramic reinforced aluminium alloy, includes the following steps:
Step 1: preparation Al-Ti-B4C-BN reacts green compact；
Step 2: preparation Al-Si-Mg-Ti aluminium alloy, and kept the temperature in the case where temperature is 1203K；
Step 3: crucible is warming up to 1123-1203K, the Al-Si-Mg-Ti aluminium alloy total amount prepared in step 2 is taken
10%-20% is poured into the crucible, heat preservation；
Step 4: by the Al-Ti-B4After C-BN reacts green compact preheating, the Al-Si- after keeping the temperature in the crucible is added
In Mg-Ti aluminium alloy；Al-Ti-B in the crucible4C-BN reaction green compact generates in Al-Si-Mg-Ti alloy melt
After TiCN, TiB2, AlN ceramic particle at least 1min, mechanical stirring is carried out, the crucible is cooled to 1073- after stirring
1123K obtains the first hybrid alloys liquid；
Wherein, the amount of the reaction green compact of addition is the 0.5wt.%- of the Al-Si-Mg-Ti aluminium alloy total amount of preparation
1.5wt.%；
Step 5: keeping the temperature 3-5min after to the first hybrid alloys liquid ultrasonic treatment；
Step 6: the first hybrid alloys liquid is mixed with remaining Al-Si-Mg-Ti aluminium alloy, stir, at ultrasound
After reason, 3-5min is kept the temperature；It carries out refinery by de-gassing, skim, obtain the second hybrid alloys liquid；
It is cast in mold Step 7: controlling the temperature of the second hybrid alloys liquid in 993-1023K, obtains aluminium conjunction
Golden slab.
Preferably, in said step 1, Al-Ti-B is prepared4C-BN reacts green compact, includes the following steps:
Step 1 is in molar ratio 1:1 by B4After the mixing of C powder BN powder, it is put into ball grinder, with the speed of 200-300r/min
It spends ball milling and is activated 150min-200min；
Step 2, by the B after titanium valve, aluminium powder and activation processing4The mixing of C powder BN powder, is put into ball grinder, with 30-90r/
The revolving speed mixing 8-48h of min；
Wherein, titanium valve, B4C powder, BN powder molar ratio be 9:2.4:2.4, surplus is aluminium；
The powder aluminium foil mixed is wrapped up and is sealed by step 3, is placed in mold, is applied at room temperature with axial compressive force,
Pressure maintaining 0.5-3min obtains cylindrical reaction green compact under 60-90MPa pressure.
Preferably, in the step 2, titanium valve, B4C powder, BN powder molar ratio be 9:2.8:2.8, surplus is aluminium.
Preferably, in the step 2, the method for Al-Si-Mg-Ti aluminium alloy is prepared are as follows:
Al-Si-Mg-Ti alloy is placed in crucible, 1023K, melting 40-100min are warming up to；Slag-cleaning agent is added to carry out
Refining slagging-off keeps the temperature 2~5min after slag hitting processing, obtains Al-Si-Mg-Ti aluminium alloy.
Preferably, the ingredient of the Al-Si-Mg-Ti alloy are as follows: Si:9.8-10.5wt.%, Mg:0.65-
0.78wt.%, Ti:0.1-0.6wt.%, surplus Al.
Preferably, in the step 3, soaking time is 10~20min.
Preferably, in the step 4, Al-Ti-B4C-BN reaction green compact is preheated at 753-823K
0.5-2h。
Preferably, in the step 5, method that the first hybrid alloys liquid is ultrasonically treated are as follows:
Ultrasonic probe is dropped into the position apart from liquid level 50-120mm, after keeping the temperature 3-5min, opens ultrasonic equipment,
8-10min is ultrasonically treated to hybrid alloys liquid.
Preferably, in the step 6, the method for ultrasonic treatment are as follows:
Ultrasonic probe is dropped into the position apart from liquid level 50-120mm, after keeping the temperature 3-5min, opens ultrasonic equipment,
3-8min is ultrasonically treated to hybrid alloys liquid.
Preferably, in the step 7, the material of the mold is 45# steel.
The beneficial effects of the present invention are:
(1) molten internal in-situ multiphase provided by the invention mixes the method for scale ceramic reinforced aluminium alloy, using in parcel
Cause Al-Ti-B in alloy melt4C-BN system is in situ to react from climing combustion, and multiphase is micro-nano mixes size TiCN, TiB for generation2、
AlN ceramic particle, and the pre-dispersed technological means in melt in parcel of particle strengthens aluminium alloy, cause in parcel molten
The reaction in-situ of internal particle is conducive to the complete progress of reaction system green compact raw reaction from climing combustion in melt, and in parcel
The reunion of the pre-dispersed particle that can be avoided generation；In addition, remaining aluminium alloy is always in a little higher than pouring temperature range inside holding,
The loss of tooling device can be made to reduce to avoid the scaling loss of alloying element.
(2) molten internal in-situ multiphase provided by the invention mixes the method for scale ceramic reinforced aluminium alloy, by rationally controlling
The amount and intensified condition of the powder green compact added in alloyage liquid, can be improved the dispersion effect of ceramic particle, significantly improve aluminium
The mechanical property of alloy.
(3) molten internal in-situ multiphase provided by the invention mixes the method for scale ceramic reinforced aluminium alloy, due to granular raw
Raw in position, no deleterious interfacial reaction, the dispersion effect of ceramic particle is more preferable, and strengthening process is simple and convenient, and what is enabled aluminum alloy to is tough
Property improve simultaneously, have important industrial application value.
Specific embodiment
The present invention is described in further detail below, to enable those skilled in the art's refer to the instruction text being capable of evidence
To implement.
The present invention provides a kind of molten internal in-situ multiphases to mix the method for scale ceramic reinforced aluminium alloy, including walks as follows
It is rapid:
(1) pretreatment of green compact is reacted
A, B4C powder is weighed respectively for 1:1 in molar ratio and BN powder is spare；
Wherein, B4Purity >=92.0wt.% of C powder, purity >=99.0wt.% of BN powder.
B, preparation is several fills multiple diameter ZrO2The ball grinder of abrading-ball；
Wherein, the gross mass of the abrading-ball in each ball grinder is 800g, the ZrO filled in each ball grinder2Abrading-ball is straight
Diameter is 5mm, 7mm, 11mm, 15mm, 20mm, 22mm.
C, by weighed B4C powder and the mixing of BN powder are put into ball grinder, and ball grinder is installed in planetary batch mixer, with
The speed high speed ball milling of 200-300r/min is activated 150min-200min.The ratio of grinding media to material that high speed ball milling is activated is 8:1
~10:1, the volume of mixed powder are no more than the 1/2-3/4 of ball milling tank volume.
D, by the B after aluminium powder, titanium valve and activation processing4C powder and the mixing of BN powder, make titanium valve, B4The molar ratio of C powder, BN powder
Ti:B4C:BN=9:2.4:2.4 or 9:2.8:2.8, surplus are aluminium；
Wherein, the mesh number of aluminium powder is 300~1000 mesh, purity >=99.9wt.%；The mesh number of titanium valve is 325~1000 mesh,
Purity >=99.9wt.%.
E, prepared powder is put into ball grinder described in step (1) b, ball grinder is placed in batch mixer, mixing
The mixed time of machine is set as 8-48h, revolving speed 30-90r/min.
F, the powder mixed is wrapped up and sealed with thin aluminium foil, and the powder wrapped is placed in the stainless steel mould of Φ 30mm
In, it is equipped with a stainless steel column above powder, is applied at room temperature by hydraulic press with unidirectional axial compressive force, then in 60-
Pressure maintaining 0.5-3min under 90MPa obtains a height of 35-45mm, diameter of phi 30, the cylindrical green compact that consistency is 65 ± 5%.
(2) reaction in-situ and particle are pre-dispersed in parcel
A, Al-Si-Mg-Ti alloy (name are as follows: crucible 1) in a dry crucible is prepared, total matter of alloy is recorded
Amount, crucible 1 is put into crucible type melting resistance furnace；Aluminium alloy is warming up to 1023K, melting 40-100min；
Wherein, the ingredient of Al-Si-Mg-Ti alloy are as follows: Si:9.8-10.5wt.%, Mg:0.65-0.78wt.%, Ti:
0.1-0.6wt.%, surplus Al；
B, slag-cleaning agent is added, refining slagging-off is carried out to aluminium alloy, keep the temperature 2~5min after slag hitting processing, obtain Al-Si-Mg-
Ti aluminium alloy, and crucible 1 is kept keeping the temperature under 1023K.Wherein, the additional amount of slag-cleaning agent is the 0.05- of aluminium alloy total amount
0.10wt.%.
C, the crucible (name are as follows: crucible 2) for preparing another drying is put into crucible type melting resistance furnace, is warming up to
1123-1203K；The 10-20% of the Al-Si-Mg-Ti aluminium alloy total amount prepared in crucible 1 is poured into crucible 2,10- is kept the temperature
20min.Crucible 1 remains to be kept the temperature under 1023K.
D, powder green compact obtained in step (1) is preheated into 0.5-2h at 753-823K, the alloy being added in crucible 2
In liquid；The amount that powder green compact is added is the 0.5wt.%-1.5wt.% of the aluminium alloy total amount prepared.
E, when the flame for having moment bright in 2 melt of crucible (illustrates Al-Ti-B4C-BN system is in aluminium alloy melt
Inside generate TiCN, TiB2, AlN ceramic particle) after at least 1 minute, carry out mechanical stirring, time 1-5min；It, will after stirring
The furnace temperature of crucible 2 is down to 1073-1123K；
F, ultrasonic probe is dropped into the position apart from liquid level 50-120mm in crucible 2, keeps the temperature 3-5min；When heat preservation
Between after open ultrasonic equipment, 8-10min is ultrasonically treated to hybrid alloys liquid in crucible 2, the dispersion of aided nano particle is equal
It is even；Ultrasonic device is removed later, keeps the temperature 3-5min.
Preferably, the use of the ingredient of slag-cleaning agent being 35~50wt.%KCl, 30~40wt.%MgCl2, 5~10wt.%
AlF3, 10~15wt.%Na3AlF6, 5~10wt.%Mg3N2, 2~5wt.%Na2CO3, 2~5wt.%C2Cl6。
(3) cast molding of Al-Si-Mg-Ti alloy after strengthening
A, the hybrid alloys liquid in crucible 2 is quickly poured into crucible 1, is mixed with remaining aluminium alloy in crucible 1, it is mechanical
Stir 1-2min；
B, twice ultrasonic processing is carried out, ultrasonic probe drops to the position apart from liquid level 50-120mm, keeps the temperature 3-5min；
After heat preservation, 3-8min is ultrasonically treated to hybrid alloys liquid；Then heat preservation 3-5min.
C, the aluminium alloy slag-cleaning agent of the aluminium alloy addition 0.05-0.10wt.% after ultrasonic treatment, mechanical stirring 1-2min,
It carries out refinery by de-gassing, skim；Then the temperature of control aluminium alloy is 993-1023K, prepares casting；
E, casting die is preheated, the obtained Al-Si-Mg-Ti aluminium alloy containing endogenetic particle is cast to metal pattern die
At plate aluminium alloy slab in tool.
Preferably, the material of metal type dies is 45# steel；The size of metal type dies are as follows: 200mm × 150mm ×
20mm。
Embodiment 1
(1) pretreatment of green compact is reacted
A, B is weighed respectively for 1:1 in molar ratio4C powder and BN powder are spare；
Wherein, B4Purity >=92.0wt.% of C powder, purity >=99.0wt.% of BN powder.
B, preparation is several fills the ZrO that diameter is respectively the total 800g of 5mm, 7mm, 11mm, 15mm, 20mm, 22mm mass2Mill
The ball grinder of ball；
C, by B4It is put into ball grinder after C powder and the mixing of BN powder, ball grinder is installed in planetary batch mixer, and use is planetary
Ball mill is activated 200min with the speed high speed ball milling of 200r/min；The ratio of grinding media to material that high speed ball milling is activated is 10:1,
The volume of mixed powder is no more than the 1/2 of ball milling tank volume；
D, weighing mesh number is 500 mesh, purity >=99.9wt.% aluminium powder, and mesh number is 500 mesh, purity >=99.9wt.%
Titanium valve；And by the B after aluminium powder and titanium valve and activation4C powder and the mixing of BN powder；Make reactant titanium valve, B4The molar ratio of C powder, BN powder
Ti:B4C:BN=9:2.4:2.4, surplus are aluminium；Wherein, Al powder is 70g；Ti powder is 20.7g；B4C powder is 6.43g；BN powder is
2.87g；
E, prepared powder is put into ball grinder clean described in step (1) b, ball grinder is placed in batch mixer
In, the mixed time of batch mixer is set as 48h, revolving speed 30r/min；
F, the powder mixed in above-mentioned steps is wrapped up and sealed with thin aluminium foil, and the powder wrapped is placed in stainless steel mould
In, a stainless steel column is equipped with above powder, hydraulic press room temperature applies with unidirectional axial compressive force, then at 60MPa lower
Pressure maintaining 3min obtains a height of 35mm, diameter of phi 30, the cylindrical green compact that consistency is 70%.
(2) reaction in-situ and particle are pre-dispersed in parcel
A, Al-Si-Mg-Ti alloy (name are as follows: crucible 1) in a dry crucible is prepared, total matter of alloy is recorded
Amount, crucible 1 is put into crucible type melting resistance furnace, 1023K, melting 60min are warming up to；
Wherein, the ingredient of Al-Si-Mg-Ti alloy are as follows: Si:10.5wt.%, Mg:0.78wt.%, Ti:0.1wt.%, it is remaining
Amount is Al；
B, slag-cleaning agent is added, refining slagging-off is carried out to aluminium alloy, keep the temperature 5min after slag hitting processing, obtain Al-Si-Mg-Ti conjunction
Golden liquid；The additional amount of slag-cleaning agent is the 0.10wt.% of aluminium alloy total amount；
C, the crucible (name are as follows: crucible 2) for preparing another drying is put into crucible type melting resistance furnace, is warming up to
1123K；About 20% aluminum alloy melt for taking the Al-Si-Mg-Ti aluminium alloy total content prepared in crucible 1, is poured into crucible 2, is protected
Warm 10min.Crucible 1 remains to be kept the temperature under 1023K；
D, powder green compact obtained in step (1) is preheated into 1h at 773K, the alloy being then added in described in crucible 2
In liquid；The quality that powder green compact is added is about the 1.5wt.% of aluminium alloy total amount.
E, green compact is kept to immerse not less than 1 minute in alloy melt after the flame for having moment to become clear in 2 melt of crucible,
Then carry out mechanical stirring, time 5min；The furnace temperature of crucible 2 is down to 1073K；
F, ultrasonic probe is dropped into the position apart from liquid level 50mm in crucible 2, keeps the temperature 5min；Soaking time terminates
After open ultrasonic equipment, 8min is ultrasonically treated to hybrid alloys liquid, aided nano particle is uniformly dispersed, then removes ultrasound and set
It is standby, keep the temperature 5min.
(3) cast molding of Al-Si-Mg-Ti alloy after strengthening
A, the hybrid alloys liquid in crucible 2 is quickly poured into crucible 1, is mixed with remaining aluminium alloy in crucible 1, it is mechanical
Stir 2min；
B, twice ultrasonic processing is carried out, ultrasonic probe drops to the position apart from liquid level 50mm, keeps the temperature 5min；When heat preservation
Between after open ultrasonic equipment, to hybrid alloys liquid be ultrasonically treated 3min.Then heat preservation 3min；
C, the aluminium alloy slag-cleaning agent of 0.10wt.% is added in the aluminium alloy after ultrasonic treatment, and mechanical stirring 2min carries out degasification
It refines, skim；Then control temperature 993K prepares casting；
D, casting die is preheated, the obtained Al-Si-Mg-Ti aluminium alloy containing endogenetic particle is then cast to metal
At plate aluminium alloy slab in pattern tool, wherein plate slab with a thickness of 20mm；
In the present embodiment, the ingredient of the slag-cleaning agent used is 45wt.%KCl, 30wt.%MgCl2, 5wt.%AlF3、
10wt.%Na3AlF6, 5wt.%Mg3N2, 2wt.%Na2CO3, 3wt.%C2Cl6。
In the present embodiment, by adding Al-Ti-B into Al-Si-Mg-Ti matrix alloy4C-BN system reacts green compact
After causing the in-situ endogenic reaction for generating ceramic particle, particle is evenly distributed in the base, and interface cohesion is good.It is generated in melt
The content of ceramic particle accounts for the 0.3wt.% of aluminium alloy total amount, as shown in table 1, mixes scale reinforcing by in-situ endogenic multiphase
Al-Si-Mg-Ti alloy yield strength, tensile strength, breaking strain are respectively 279MPa, 331MPa, 9.8%, (Al-Si-Mg-
The tensile strength of Ti matrix alloy, breaking strain are respectively 238MPa, 284MPa, 7.1%).In-situ endogenic multiphase mixes scale
The yield strength of the Al-Si-Mg-Ti of reinforcing, tensile strength, breaking strain mention respectively compared to Al-Si-Mg-Ti matrix alloy
High by 17.2%, 16.5%, 38.0%, mechanical property is significantly improved.
Embodiment 2
(1) pretreatment of green compact is reacted
A, B is weighed respectively for 1:1 in molar ratio4C powder and BN powder are spare；
Wherein, B4Purity >=92.0wt.% of C powder, purity >=99.0wt.% of BN powder.
B, preparation is several fills the ZrO that diameter is respectively the total 800g of 5mm, 7mm, 11mm, 15mm, 20mm, 22mm mass2Mill
The ball grinder of ball；
C, by B4C powder and BN powder are put into ball grinder, and ball grinder is installed in planetary batch mixer, planetary type ball-milling is used
Machine is activated 150min with the speed high speed ball milling of 300r/min；The ratio of grinding media to material that high speed ball milling is activated is 10:1, mixing
The volume of powder is no more than the 1/2 of ball milling tank volume.
D, weighing mesh number is 1000 mesh, purity >=99.9wt.% aluminium powder, and mesh number is 325 mesh, purity >=99.9wt.%
Titanium valve；And by the B after aluminium powder and titanium valve and activation4C powder and the mixing of BN powder；Make reactant titanium valve, B4Mole of C powder, BN powder
Compare Ti:B4C:BN=9:2.8:2.8, surplus are aluminium；Wherein, Al powder is 80g；Ti powder is 13.16g；B4C powder is 4.72g；BN powder
For 2.12g；
E, prepared powder is put into ball grinder clean described in step (1) b, ball grinder is placed in batch mixer
In, the mixed time of batch mixer is set as 8h, revolving speed 90r/min；
F, the powder mixed in above-mentioned steps is wrapped up and sealed with thin aluminium foil, and the powder wrapped is placed in Φ 30mm not
In steel mold of becoming rusty, a stainless steel column is equipped with above powder, hydraulic press room temperature, with unidirectional axial compressive force, then exists in lower application
Pressure maintaining 3min obtains a height of 35mm, diameter of phi 30, the cylindrical green compact that consistency is 61% under 60MPa.
(2) reaction in-situ and particle are pre-dispersed in parcel
A, it prepares Al-Si-Mg-Ti alloy and (is named as crucible 1) in a dry crucible, crucible 1 is put into crucible type
In melting resistance furnace；The gross mass for recording alloy, is warming up to 1023K, melting 100min for aluminium alloy；
Wherein, the ingredient of Al-Si-Mg-Ti alloy are as follows: Si:9.8wt.%, Mg:0.65wt.%, Ti:0.6wt.%, it is remaining
Amount is Al；
B, slag-cleaning agent is added, refining slagging-off is carried out to aluminium alloy, keep the temperature 2min after slag hitting processing, obtain Al-Si-Mg-Ti conjunction
Golden liquid；The additional amount of slag-cleaning agent is the 0.05wt.% of aluminium alloy total amount；
C, the crucible (name are as follows: crucible 2) for preparing another drying is put into crucible type melting resistance furnace, is warming up to
1123K；20% aluminum alloy melt for taking the Al-Si-Mg-Ti aluminium alloy total content prepared in crucible 1, is poured into crucible 2, heat preservation
20min.Crucible 1 remains to be kept the temperature under 1023K.
D, powder green compact obtained in step (1) is preheated into 2h at 753K, the aluminium alloy being then added in crucible 2
In；The quality that powder green compact is added is the 0.5wt.% of aluminium alloy total amount.
E, it after the flame for thering is moment to become clear in 2 melt of crucible, keeps green compact to immerse and is not less than 1 point in alloy melt
Clock then carries out mechanical stirring, time 5min；The furnace temperature of crucible 2 is down to 1073K；
F, in crucible 2, ultrasonic probe is dropped into the position apart from liquid level 50mm, keeps the temperature 3min；Soaking time knot
Ultrasonic equipment is opened after beam, 10min is ultrasonically treated to hybrid alloys liquid, aided nano particle is uniformly dispersed, then removes super
Acoustic equipment keeps the temperature 3min.
(3) cast molding of Al-Si-Mg-Ti alloy after strengthening
A, the hybrid alloys liquid in crucible 2 is quickly poured into crucible 1, is mixed with remaining aluminium alloy in crucible 1, it is mechanical
Stir 2min；
B, twice ultrasonic processing is carried out, ultrasonic probe is dropped into the position apart from liquid level 50mm, keeps the temperature 3min；Heat preservation
Ultrasonic equipment is opened after time, to hybrid alloys liquid using ultrasonic treatment 3min.Then heat preservation 3min.
C, the aluminium alloy slag-cleaning agent of 0.05wt.% is added in the aluminium alloy after ultrasonic treatment, and mechanical stirring 1min carries out degasification
It refines, skim；Then control temperature 1023K prepares casting；
D, casting die is preheated, the obtained Al-Si-Mg-Ti aluminium alloy containing endogenetic particle is cast to metal pattern die
At plate aluminium alloy slab in tool, wherein plate slab with a thickness of 20mm；
In the present embodiment, the ingredient of the slag-cleaning agent used is 35wt.%KCl, 30wt.%MgCl2, 10wt.%AlF3、
15wt.%Na3AlF6, 5wt.%Mg3N2, 3wt.%Na2CO3, 2wt.%C2Cl6。
In the present embodiment, by adding Al-Ti-B into Al-Si-Mg-Ti matrix alloy4C-BN system reacts green compact
After causing the in-situ endogenic reaction for generating ceramic particle, particle is evenly distributed in the base, and interface cohesion is good.It is generated in melt
The content of ceramic particle accounts for the 0.1wt.% of aluminium alloy total amount, as shown in table 1, mixes scale reinforcing by in-situ endogenic multiphase
Al-Si-Mg-Ti alloy yield strength, tensile strength, breaking strain are respectively 265MPa, 318MPa, 12.5%, (Al-Si-
The tensile strength of Mg-Ti matrix alloy, breaking strain are respectively 238MPa, 284MPa, 7.1%).In-situ endogenic multiphase mixes ruler
Spend the yield strength, tensile strength, breaking strain of the Al-Si-Mg-Ti strengthened compared to Al-Si-Mg-Ti matrix alloy, respectively
11.3%, 12.0%, 76.1% is improved, mechanical property is significantly improved.
Embodiment 3
(1) pretreatment of green compact is reacted
A, B is weighed respectively for 1:1 in molar ratio4C powder and BN powder are spare；
Wherein, B4Purity >=92.0wt.% of C powder, purity >=99.0wt.% of BN powder.
B, preparation is several fills the ZrO that diameter is respectively the total 800g of 5mm, 7mm, 11mm, 15mm, 20mm, 22mm mass2Mill
The ball grinder of ball；
C, by B4C powder and BN powder are put into ball grinder, and ball grinder is installed in planetary batch mixer, use planetary ball mill
180min is activated with the speed high speed ball milling of 250r/min；The ratio of grinding media to material that high speed ball milling is activated is 9:1, mixed powder
Volume be no more than ball milling tank volume 1/2；
D, weighing mesh number is 300 mesh, purity >=99.9wt.% aluminium powder；Mesh number is 1000 mesh, purity >=99.9wt.%
Titanium valve；And by the B after aluminium powder and titanium valve and activation4C powder and the mixing of BN powder；Make reactant titanium valve, B4Mole of C powder, BN powder
Compare Ti:B4C:BN=9:2.8:2.8, surplus are aluminium；Wherein, Al powder is 60g；Ti powder is 26.31g；B4C powder is 9.45g；BN powder
For 4.24g；
E, prepared powder being put into ball grinder clean described in step (1) b, ball grinder is placed in batch mixer,
The mixed time of batch mixer is set as 8h, revolving speed 90r/min；
F, the powder mixed in above-mentioned steps is wrapped up and sealed with thin aluminium foil, and the powder wrapped is placed in having a size of Φ
In the stainless steel mould of 30mm, a stainless steel column is equipped with above powder, hydraulic press room temperature is in lower application with unidirectionally axial pressure
Power, then the pressure maintaining 3min at 60MPa；Obtain a height of 45mm, diameter of phi 30, the cylindrical green compact that consistency is 60%.
(2) reaction in-situ and particle are pre-dispersed in parcel
A, it prepares Al-Si-Mg-Ti alloy and (is named as crucible 1) in a dry crucible, crucible 1 is put into crucible type electricity
It hinders in smelting furnace, records the gross mass of alloy, and be warming up to 1023K, melting 60min；
Wherein, the ingredient of Al-Si-Mg-Ti alloy are as follows: Si:10.1wt.%, Mg:0.72wt.%, Ti:0.3wt.%, it is remaining
Amount is Al；
B, slag-cleaning agent is added, refining slagging-off is carried out to aluminium alloy, keep the temperature 4min after slag hitting processing, obtain Al-Si-Mg-Ti conjunction
Golden liquid；The additional amount of slag-cleaning agent is the 0.05wt.% of aluminium alloy total amount；
C, the crucible (name are as follows: crucible 2) for preparing another drying is put into crucible type melting resistance furnace, is warming up to
1203K；About the 20% of the Al-Si-Mg-Ti aluminium alloy total content prepared in crucible 1 is taken, is poured into crucible 2,15min is kept the temperature.Earthenware
Crucible 1 remains to be kept the temperature under 1023K.
D, powder green compact obtained in step (1) is preheated into 3h at 803K, the aluminium alloy being then added in crucible 2
In；The quality that powder is added is the 1.0wt.% of aluminium alloy total amount.
E, it after the flame for thering is moment to become clear in 2 melt of crucible, keeps green compact to immerse and is not less than 1 point in alloy melt
Clock then carries out mechanical stirring, time 1min；The furnace temperature of crucible 2 is down to 1123K；
F, ultrasonic probe is dropped into the position apart from liquid level 120mm in crucible 2, keeps the temperature 5min；Soaking time knot
Ultrasonic equipment is opened after beam, 10min is ultrasonically treated to hybrid alloys liquid, aided nano particle is uniformly dispersed；It then removes super
Acoustic equipment keeps the temperature 5min.
(3) cast molding of Al-Si-Mg alloy after strengthening
A, the aluminium alloy in crucible 2 is quickly poured into crucible 1, is mixed with remaining aluminium alloy in crucible 1, mechanical stirring
1min；
B, twice ultrasonic processing is carried out, ultrasonic probe is dropped into the position apart from liquid level 120mm, keeps the temperature 5min；It protects
Ultrasonic equipment is opened after the warm time, to hybrid alloys liquid using ultrasonic treatment 3min.Then heat preservation 5min；
C, the aluminium alloy slag-cleaning agent of 0.05wt.% is added in the aluminium alloy after ultrasonic treatment, and mechanical stirring 1min carries out degasification
It refines, skim；Then control temperature 1023K prepares casting；
D, casting die is preheated, the obtained Al-Si-Mg-Ti aluminium alloy containing endogenetic particle is then cast to metal
Pattern tool at plate aluminium alloy slab, wherein plate slab with a thickness of 20mm；
In the present embodiment, the ingredient of the slag-cleaning agent used is 40wt.%KCl, 30wt.%MgCl2, 8wt.%AlF3、
10wt.%Na3AlF6, 5wt.%Mg3N2, 5wt.%Na2CO3, 2wt.%C2Cl6。
In the present embodiment, by adding Al-Ti-B into Al-Si-Mg-Ti matrix alloy4C-BN system reacts green compact
After causing the in-situ endogenic reaction for generating ceramic particle, particle is evenly distributed in the base, and interface cohesion is good.It is generated in melt
The content of ceramic particle accounts for the 0.2wt.% of aluminium alloy total amount, as shown in table 1, mixes scale reinforcing by in-situ endogenic multiphase
Al-Si-Mg-Ti alloy yield strength, tensile strength, breaking strain are respectively 272MPa, 326MPa, 10.7%, (Al-Si-
The tensile strength of Mg-Ti matrix alloy, breaking strain are respectively 238MPa, 284MPa, 7.1%).In-situ endogenic multiphase mixes ruler
Spend the yield strength, tensile strength, breaking strain of the Al-Si-Mg-Ti strengthened compared to Al-Si-Mg-Ti matrix alloy, respectively
14.3%, 14.8%, 50.7% is improved, mechanical property is significantly improved.
Comparative example 1
It prepares matrix alloy Al-Si-Mg-Ti (being not added with multiphase ceramic particle strengthening in situ), specific as follows:
A, it prepares and is not added with ceramics particle strengthened Al-Si-Mg-Ti alloy in a dry crucible, crucible is put into crucible
In formula melting resistance furnace；The gross mass for recording alloy, is warming up to 1023K, melting 50min；
Wherein, the ingredient of Al-Si-Mg-Ti alloy are as follows: Si:10.2wt.%, Mg:0.69wt.%, Ti:0.3wt.%, it is remaining
Amount is Al；
B, slag-cleaning agent is added, refining slagging-off is carried out to aluminium alloy, keep the temperature 3min after slag hitting processing, obtain Al-Si-Mg-Ti conjunction
Golden liquid；The additional amount of slag-cleaning agent is the 0.05wt.% of aluminium alloy total amount；
C, ultrasonic probe is dropped into the position apart from liquid level 50-120mm in crucible, keeps the temperature 5min；Soaking time knot
Ultrasonic equipment is opened after beam, to aluminium alloy using ultrasonic treatment 8min.Ultrasonic device is then removed, 3min is kept the temperature.
D, the aluminium alloy after ultrasonic treatment carries out refinery by de-gassing, skims；The aluminium alloy slag-cleaning agent of 0.05wt.%, machine is added
Tool stirs 2min；Then control temperature 1023K prepares casting；
E, casting die is preheated, the obtained Al-Si-Mg-Ti aluminium alloy containing endogenetic particle is then cast to metal
At plate aluminium alloy slab in pattern tool, wherein plate slab with a thickness of 20mm；
As shown in table 1, TiCN, TiB are not added with obtained in the comparative example2, AlN ceramic particle strengthening Al-Si-Mg-
The tensile strength of Ti matrix alloy, breaking strain are respectively 238MPa, 284MPa, 7.1%.
Comparative example 2
Multiphase mixes the ceramics particle strengthened alusil alloy of scale, and the amount of control addition powder green compact makes to generate ceramic particle
Content account for the 0.05wt.% of aluminium alloy total amount.Detailed process are as follows:
(1) pretreatment of green compact is reacted
A, B is weighed respectively for 1:1 in molar ratio4C powder and BN powder are spare；
Wherein, B4Purity >=92.0wt.% of C powder, purity >=99.0wt.% of BN powder.
B, preparation is several fills the ZrO that diameter is respectively the total 800g of 5mm, 7mm, 11mm, 15mm, 20mm, 22mm mass2Mill
The ball grinder of ball；
C, by B4C powder and BN powder are put into ball grinder, and ball grinder is installed in planetary batch mixer, use planetary ball mill
150min is activated with the speed high speed ball milling of 300r/min；The ratio of grinding media to material that high speed ball milling is activated is 10:1, mixed powder
The volume of body is no more than the 1/2 of ball milling tank volume.
D, weighing mesh number is 1000 mesh, purity >=99.9wt.% aluminium powder, and mesh number is 325 mesh, purity >=99.9wt.%
Titanium valve；Make titanium valve, B4The molar ratio Ti:B of C powder, BN powder4C:BN=9:2.8:2.8, surplus are aluminium；Wherein, Al powder is 80g；
Ti powder is 13.16g；B4C powder is 4.72g；BN powder is 2.12g；
E, prepared powder being put into ball grinder clean described in step (1) b, ball grinder is placed in batch mixer,
The mixed time of batch mixer is set as 8h, revolving speed 90r/min；
F, the powder mixed in above-mentioned steps is wrapped up and sealed with thin aluminium foil, and the powder wrapped is placed in Φ 30mm not
In steel mold of becoming rusty, a stainless steel column is equipped with above powder, hydraulic press room temperature, with unidirectional axial compressive force, then exists in lower application
Pressure maintaining 3min obtains a height of 42mm, diameter of phi 30, the cylindrical green compact that consistency is 61% under 60MPa.
(2) reaction in-situ and particle are pre-dispersed in parcel
A, it prepares Al-Si-Mg-Ti alloy and (is named as crucible 1) in a dry crucible, crucible 1 is put into crucible type electricity
It hinders in smelting furnace；The gross mass for recording alloy, is warming up to 1023K, melting 100min；
Wherein, the ingredient of Al-Si-Mg-Ti alloy are as follows: Si:9.9wt.%, Mg:0.67wt.%, Ti:0.56wt.%, it is remaining
Amount is Al；
B, slag-cleaning agent is added, refining slagging-off is carried out to aluminium alloy, keep the temperature 2min after slag hitting processing, obtain Al-Si-Mg-Ti conjunction
Golden liquid；The additional amount of slag-cleaning agent is the 0.05wt.% of aluminium alloy total amount；
C, the crucible (name are as follows: crucible 2) for preparing another drying is put into crucible type melting resistance furnace, is warming up to
1123K；20% aluminum alloy melt for taking the Al-Si-Mg-Ti aluminium alloy total content prepared in crucible 1, is poured into crucible 2, heat preservation
20min.Crucible 1 remains to be kept the temperature under 1023K.
D, powder green compact obtained in step (1) is preheated into 2h at 753K, the alloy being then added in described in crucible 2
In liquid；The quality that powder is added is the 0.25wt.% of the aluminium alloy total amount prepared.
E, it after the flame for thering is moment to become clear in 2 melt of crucible, keeps green compact to immerse and is not less than 1 point in alloy melt
Clock then carries out mechanical stirring, time 5min；The furnace temperature of crucible 2 is down to 1073K.
F, ultrasonic probe is dropped into the position apart from liquid level 50mm in crucible 2, keeps the temperature 3min；Soaking time terminates
After open ultrasonic equipment, to hybrid alloys liquid using ultrasonic treatment 10min, aided nano particle is uniformly dispersed；Then remove
Ultrasonic device keeps the temperature 3min.
(3) cast molding of Al-Si-Mg-Ti alloy after strengthening
A, the aluminium alloy in crucible 2 is quickly poured into crucible 1, is mixed with remaining aluminum alloy melt in crucible 1, machinery stirs
Mix 2min；
B, twice ultrasonic processing is carried out, ultrasonic probe is dropped into the position apart from liquid level 50mm, keeps the temperature 3min；Heat preservation
Ultrasonic equipment is opened after time, 10min is ultrasonically treated to hybrid alloys liquid, aided nano particle is uniformly dispersed；It will surpass
After sonic probe heat preservation, to hybrid alloys liquid using ultrasonic treatment 3min；Then heat preservation 3min.
C, the aluminium alloy slag-cleaning agent of 0.05wt.%, mechanical stirring 1min is added in the aluminium alloy after ultrasonic treatment；Carry out degasification
It refines, skim；Then control temperature 1023K prepares casting；
D, casting die is preheated, the obtained Al-Si-Mg-Ti aluminium alloy containing endogenetic particle is then cast to metal
Pattern tool at plate aluminium alloy slab, wherein plate slab with a thickness of 20mm；
In the comparative example, the ingredient of the slag-cleaning agent used is 35wt.%KCl, 30wt.%MgCl2, 10wt.%AlF3、
15wt.%Na3AlF6, 5wt.%Mg3N2, 3wt.%Na2CO3, 2wt.%C2Cl6。
The comparative example is by adding Al-Ti-B into Al-Si-Mg-Ti matrix alloy4C-BN system reacts green compact and causes life
After the in-situ endogenic reaction of ceramic particle, particle is evenly distributed in the base, and interface cohesion is good.Ceramics are generated in melt
The content of grain accounts for the 0.05wt.% of aluminium alloy total amount, as shown in table 1, the Al- of scale reinforcing is mixed by in-situ endogenic multiphase
Si-Mg-Ti alloy yield strength, tensile strength, breaking strain are respectively 245MPa, 292MPa, 7.5%, (Al-Si-Mg-Ti
The tensile strength of matrix alloy, breaking strain are respectively 238MPa, 284MPa, 7.1%).It is strong that in-situ endogenic multiphase mixes scale
The yield strength of the Al-Si-Mg-Ti of change, tensile strength, breaking strain are respectively increased compared to Al-Si-Mg-Ti matrix alloy
2.9%, 2.8%, 5.6%, mechanical property is not significantly improved, illustrate that the content of ceramic particle accounts for aluminium alloy total amount
When 0.05wt.%, the performance of Al-Si-Mg-Ti alloy is improved limited.
Comparative example 3
Multiphase mixes the ceramics particle strengthened alusil alloy of scale, and the amount of control addition powder green compact makes to generate ceramic particle
Content account for the 0.5wt.% of aluminium alloy total amount.Detailed process are as follows:
(1) pretreatment of green compact is reacted
A, B is weighed respectively for 1:1 in molar ratio4C powder and BN powder are spare；
Wherein, B4Purity >=92.0wt.% of C powder, purity >=99.0wt.% of BN powder.
B, preparation is several fills the ZrO that diameter is respectively the total 800g of 5mm, 7mm, 11mm, 15mm, 20mm, 22mm mass2Mill
The ball grinder of ball；
C, by B4C powder and BN powder are put into ball grinder, and ball grinder is installed in planetary batch mixer, use planetary ball mill
200min is activated with the speed high speed ball milling of 200r/min；The ratio of grinding media to material that high speed ball milling is activated is 10:1, mixed powder
The volume of body is no more than the 1/2 of ball milling tank volume.
D, weighing mesh number is 500 mesh, purity >=99.9wt.% aluminium powder, and mesh number is 500 mesh, purity >=99.9wt.%
Titanium valve.Make titanium valve, B4The molar ratio Ti:B of C powder, BN powder4C:BN=9:2.4:2.4, surplus are aluminium；Wherein, Al powder is 70g；Ti
Powder is 20.7g；B4C powder is 6.43g；BN powder is 2.87g；
E, prepared powder being put into ball grinder clean described in step (1) b, ball grinder is placed in batch mixer,
The mixed time of batch mixer is set as 48h, revolving speed 30r/min；
G, the powder mixed in above-mentioned steps is wrapped up and sealed with thin aluminium foil, and the powder wrapped is placed in Φ 30mm not
In steel mold of becoming rusty, a stainless steel column is equipped with above powder, hydraulic press room temperature, with unidirectional axial compressive force, then exists in lower application
Pressure maintaining 3min obtains a height of 35mm, diameter of phi 30, the cylindrical green compact that consistency is 70% under 60MPa.
(2) reaction in-situ and particle are pre-dispersed in parcel
A, it prepares Al-Si-Mg-Ti alloy and (is named as crucible 1) in a dry crucible, crucible 1 is put into crucible type electricity
It hinders in smelting furnace；The gross mass for recording alloy, is warming up to 1023K, melting 60min；
Wherein, the ingredient of Al-Si-Mg-Ti alloy are as follows: Si:10.3wt.%, Mg:0.73wt.%, Ti:0.16wt.%,
Surplus is Al；
B, slag-cleaning agent is added, refining slagging-off is carried out to aluminium alloy, keep the temperature 5min after slag hitting processing, obtain Al-Si-Mg-Ti conjunction
Golden liquid；The additional amount of slag-cleaning agent is the 0.10wt.% of aluminium alloy total amount；
C, the crucible (name are as follows: crucible 2) for preparing another drying is put into crucible type melting resistance furnace, is warming up to
1123K；About 20% aluminium alloy for taking the Al-Si-Mg-Ti aluminium alloy total amount prepared in crucible 1, is poured into crucible 2, heat preservation
10min；Crucible 1 remains to be kept the temperature under 1023K.
D, powder green compact obtained in step (1) is preheated into 1h at 773K, the alloy being then added in described in crucible 2
In liquid；The quality that powder is added is the 2.5wt.% of the aluminium alloy total amount prepared.
E, it after the flame for thering is moment to become clear in 2 melt of crucible, keeps green compact to immerse and is not less than 1 point in alloy melt
Clock then carries out mechanical stirring, time 5min；The furnace temperature of crucible 2 is down to 1073K；
F, ultrasonic probe is dropped into the position apart from liquid level 50mm in crucible 2, keeps the temperature 5min；After soaking time
Ultrasonic equipment is opened, to hybrid alloys liquid using ultrasonic treatment 8min, aided nano particle is uniformly dispersed；Then remove ultrasound
Equipment keeps the temperature 5min.
(3) cast molding of Al-Si-Mg-Ti alloy after strengthening
A, the aluminium alloy in crucible 2 is quickly poured into crucible 1, is mixed with remaining aluminum alloy melt in crucible 1, machinery stirs
Mix 2min；
B, twice ultrasonic processing is carried out, ultrasonic probe is dropped into the position apart from liquid level 50mm, keeps the temperature 5min；Heat preservation
Ultrasonic equipment is opened after time, to hybrid alloys liquid using ultrasonic treatment 3min.Then heat preservation 3min.
C, the aluminium alloy slag-cleaning agent of 0.10wt.%, mechanical stirring 2min is added in the aluminium alloy after ultrasonic treatment；Carry out degasification
It refines, skim；Then control temperature 993K prepares casting；
D, casting die is preheated, the obtained Al-Si-Mg-Ti aluminium alloy containing endogenetic particle is then cast to metal
Pattern tool at plate aluminium alloy slab, wherein plate slab with a thickness of 20mm；
In the comparative example, the ingredient of the slag-cleaning agent used is 45wt.%KCl, 30wt.%MgCl2, 5wt.%AlF3、
10wt.%Na3AlF6, 5wt.%Mg3N2, 2wt.%Na2CO3, 3wt.%C2Cl6。
The comparative example is by adding Al-Ti-B into Al-Si-Mg-Ti matrix alloy4C-BN system reacts green compact and causes life
After the in-situ endogenic reaction of ceramic particle, particle is evenly distributed in the base, and interface cohesion is good.Ceramics are generated in melt
The content of grain accounts for the 0.5wt.% of aluminium alloy total amount, as shown in table 1, the Al-Si- of scale reinforcing is mixed by in-situ endogenic multiphase
Mg-Ti alloy yield strength, tensile strength, breaking strain are respectively 255MPa, 289MPa, 6.2%, (Al-Si-Mg-Ti matrix
The tensile strength of alloy, breaking strain are respectively 238MPa, 284MPa, 7.1%).In-situ endogenic multiphase mixes scale reinforcing
The yield strength of Al-Si-Mg-Ti, tensile strength, breaking strain are respectively increased compared to Al-Si-Mg-Ti matrix alloy
7.1%, 1.8%, -12.7%, mechanical property is not significantly improved, and breaking strain significantly reduces, and illustrates excessive addition
Interior raw ceramic particle be also unfavorable for the raising of performance.
The Al-Si-Mg-Ti alloy and ceramics particle strengthened Al-Si-Mg-Ti alloy of 1 comparative example of table and embodiment preparation
Performance
Although the embodiments of the present invention have been disclosed as above, but its is not only in the description and the implementation listed
With it can be fully applied to various fields suitable for the present invention, for those skilled in the art, can be easily
Realize other modification, therefore without departing from the general concept defined in the claims and the equivalent scope, the present invention is simultaneously unlimited
In specific details.
Claims (10)
1. a kind of molten internal in-situ multiphase mixes the method for scale ceramic reinforced aluminium alloy, which comprises the steps of:
Step 1: preparation Al-Ti-B4C-BN reacts green compact；
Step 2: preparation Al-Si-Mg-Ti aluminium alloy, and kept the temperature in the case where temperature is 1203K；
Step 3: crucible is warming up to 1123-1203K, the Al-Si-Mg-Ti aluminium alloy total amount prepared in step 2 is taken
10%-20% is poured into the crucible, heat preservation；
Step 4: by the Al-Ti-B4After C-BN reacts green compact preheating, the Al-Si-Mg-Ti after keeping the temperature in the crucible is added
In aluminium alloy；Al-Ti-B in the crucible4C-BN reaction green compact generated in Al-Si-Mg-Ti alloy melt TiCN,
After TiB2, AlN ceramic particle at least 1min, mechanical stirring is carried out, the crucible is cooled to 1073-1123K after stirring, is obtained
First hybrid alloys liquid；
Wherein, the Al-Ti-B of addition4The amount of C-BN reaction green compact is the Al-Si-Mg-Ti aluminium alloy total amount of preparation
0.5wt.%-1.5wt.%；
Step 5: keeping the temperature 3-5min after to the first hybrid alloys liquid ultrasonic treatment；
Step 6: the first hybrid alloys liquid is mixed with remaining Al-Si-Mg-Ti aluminium alloy, stir, after ultrasonic treatment,
Keep the temperature 3-5min；It carries out refinery by de-gassing, skim, obtain the second hybrid alloys liquid；
It is cast in mold Step 7: controlling the temperature of the second hybrid alloys liquid in 993-1023K, obtains aluminium alloy casting
Base.
2. molten internal in-situ multiphase according to claim 1 mixes the method for scale ceramic reinforced aluminium alloy, feature exists
In, in said step 1, preparation Al-Ti-B4C-BN reacts green compact, includes the following steps:
Step 1 is in molar ratio 1:1 by B4After the mixing of C powder BN powder, it is put into ball grinder, with the speed ball milling of 200-300r/min
It is activated 150min-200min；
Step 2, by the B after titanium valve, aluminium powder and activation processing4The mixing of C powder BN powder, is put into ball grinder, with turning for 30-90r/min
Fast mixing 8-48h；
Wherein, titanium valve, B4C powder, BN powder molar ratio be 9:2.4:2.4, surplus is aluminium；
The powder aluminium foil mixed is wrapped up and is sealed by step 3, is placed in mold, is applied at room temperature with axial compressive force,
Pressure maintaining 0.5-3min obtains cylindrical reaction green compact under 60-90MPa pressure.
3. molten internal in-situ multiphase according to claim 2 mixes the method for scale ceramic reinforced aluminium alloy, feature exists
In, in the step 2, titanium valve, B4C powder, BN powder molar ratio be 9:2.8:2.8, surplus is aluminium.
4. the side that molten internal in-situ multiphase according to claim 1 to 3 mixes scale ceramic reinforced aluminium alloy
Method, which is characterized in that in the step 2, the method for preparing Al-Si-Mg-Ti aluminium alloy are as follows:
Al-Si-Mg-Ti alloy is placed in crucible, 1023K, melting 40-100min are warming up to；Slag-cleaning agent is added to be refined
Slagging-off keeps the temperature 2~5min after slag hitting processing, obtains Al-Si-Mg-Ti aluminium alloy.
5. molten internal in-situ multiphase according to claim 4 mixes the method for scale ceramic reinforced aluminium alloy, feature exists
In the ingredient of the Al-Si-Mg-Ti alloy are as follows: Si:9.8-10.5wt.%, Mg:0.65-0.78wt.%, Ti:0.1-
0.6wt.%, surplus Al.
6. molten internal in-situ multiphase according to claim 5 mixes the method for scale ceramic reinforced aluminium alloy, feature exists
In in the step 3, soaking time is 10~20min.
7. molten internal in-situ multiphase according to claim 6 mixes the method for scale ceramic reinforced aluminium alloy, feature exists
In, in the step 4, by the Al-Ti-B4C-BN reaction green compact preheat 0.5-2h at 753-823K.
8. molten internal in-situ multiphase according to claim 7 mixes the method for scale ceramic reinforced aluminium alloy, feature exists
In, in the step 5, method that the first hybrid alloys liquid is ultrasonically treated are as follows:
Ultrasonic probe is dropped into the position apart from liquid level 50-120mm, after keeping the temperature 3-5min, ultrasonic equipment is opened, to mixed
It closes aluminium alloy and is ultrasonically treated 8-10min.
9. molten internal in-situ multiphase according to claim 8 mixes the method for scale ceramic reinforced aluminium alloy, feature exists
In, in the step 6, the method for ultrasonic treatment are as follows:
Ultrasonic probe is dropped into the position apart from liquid level 50-120mm, after keeping the temperature 3-5min, ultrasonic equipment is opened, to mixed
It closes aluminium alloy and is ultrasonically treated 3-8min.
10. molten internal in-situ multiphase according to claim 9 mixes the method for scale ceramic reinforced aluminium alloy, feature exists
In in the step 7, the material of the mold is 45# steel.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811607747.8A CN109554570B (en) | 2018-12-27 | 2018-12-27 | Method for strengthening aluminum alloy by in-situ multiphase mixed scale ceramic in melt |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811607747.8A CN109554570B (en) | 2018-12-27 | 2018-12-27 | Method for strengthening aluminum alloy by in-situ multiphase mixed scale ceramic in melt |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109554570A true CN109554570A (en) | 2019-04-02 |
| CN109554570B CN109554570B (en) | 2020-07-31 |
Family
ID=65871485
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201811607747.8A Active CN109554570B (en) | 2018-12-27 | 2018-12-27 | Method for strengthening aluminum alloy by in-situ multiphase mixed scale ceramic in melt |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109554570B (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111041297A (en) * | 2019-12-17 | 2020-04-21 | 江苏大学 | High-corrosion-resistance in-situ nanoparticle reinforced aluminum-based composite material and preparation method thereof |
| CN113073253A (en) * | 2021-03-31 | 2021-07-06 | 浙江理工大学 | Method for preparing nanoparticle reinforced nodular cast iron by using aluminum-based intermediate alloy |
Citations (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63312901A (en) * | 1987-06-16 | 1988-12-21 | Kobe Steel Ltd | Heat resistant high tensile al alloy powder and composite ceramics reinforced heat resistant al alloy material using said powder |
| EP0620286A1 (en) * | 1993-03-18 | 1994-10-19 | Hitachi, Ltd. | Ceramic-particle-dispersed metallic member, manufacturing method of same and use of same |
| US5989310A (en) * | 1997-11-25 | 1999-11-23 | Aluminum Company Of America | Method of forming ceramic particles in-situ in metal |
| US6036792A (en) * | 1996-01-31 | 2000-03-14 | Aluminum Company Of America | Liquid-state-in-situ-formed ceramic particles in metals and alloys |
| CN1718806A (en) * | 2005-07-28 | 2006-01-11 | 上海交通大学 | In situ mixed granula reinforced aluminium base composite material |
| CN101148721A (en) * | 2006-09-22 | 2008-03-26 | 比亚迪股份有限公司 | Aluminum-base composite material and preparation method thereof |
| CN101166700A (en) * | 2005-02-23 | 2008-04-23 | 钴碳化钨硬质合金公司 | Alumina-boron carbide ceramics and methods of making and using the same |
| CN101748306A (en) * | 2008-12-02 | 2010-06-23 | 苏州有色金属研究院有限公司 | Multiphase ceramic hybrid composite reinforced metal matrix composite material and preparation process thereof |
| CN101775518A (en) * | 2010-04-02 | 2010-07-14 | 哈尔滨工业大学 | Device and method for preparing particle-reinforced gradient composite materials by using ultrasonic waves |
| CN102260814A (en) * | 2011-07-26 | 2011-11-30 | 吉林大学 | In situ nano TiC ceramic particle reinforced aluminum based composite material and preparation method thereof |
| JP2013036088A (en) * | 2011-08-09 | 2013-02-21 | Isuzu Motors Ltd | Method for producing composite material of ceramic particle-reinforced aluminum-silicon-based alloy |
| US20150007925A1 (en) * | 2013-07-05 | 2015-01-08 | Deeder Mohammad Aurongzeb | High-strength structural elements using metal foam for portable information handling systems |
| CN104532068A (en) * | 2014-12-15 | 2015-04-22 | 河海大学 | Nano TiC ceramic particle reinforced aluminum matrix composite and preparation method thereof |
| CN105441734A (en) * | 2014-09-30 | 2016-03-30 | 黄晓艺 | Al-Si-Mg-Ti-Sr-Fe alloy material and preparation process thereof |
| CN107012354A (en) * | 2017-04-05 | 2017-08-04 | 江苏大学 | A kind of preparation method of Al Si9Cu1 particulate reinforced composites |
| CN108103368A (en) * | 2017-06-12 | 2018-06-01 | 吉林大学 | The tough as-cast aluminum alloy of novel high-strength and preparation method |
| CN109055860A (en) * | 2018-09-07 | 2018-12-21 | 吉林大学 | One specific admixture scale TiCN and TiB2Particle Strengthening and Toughening low-alloy steel and preparation method thereof |
-
2018
- 2018-12-27 CN CN201811607747.8A patent/CN109554570B/en active Active
Patent Citations (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63312901A (en) * | 1987-06-16 | 1988-12-21 | Kobe Steel Ltd | Heat resistant high tensile al alloy powder and composite ceramics reinforced heat resistant al alloy material using said powder |
| EP0620286A1 (en) * | 1993-03-18 | 1994-10-19 | Hitachi, Ltd. | Ceramic-particle-dispersed metallic member, manufacturing method of same and use of same |
| US6036792A (en) * | 1996-01-31 | 2000-03-14 | Aluminum Company Of America | Liquid-state-in-situ-formed ceramic particles in metals and alloys |
| US5989310A (en) * | 1997-11-25 | 1999-11-23 | Aluminum Company Of America | Method of forming ceramic particles in-situ in metal |
| CN101166700A (en) * | 2005-02-23 | 2008-04-23 | 钴碳化钨硬质合金公司 | Alumina-boron carbide ceramics and methods of making and using the same |
| CN1718806A (en) * | 2005-07-28 | 2006-01-11 | 上海交通大学 | In situ mixed granula reinforced aluminium base composite material |
| CN101148721A (en) * | 2006-09-22 | 2008-03-26 | 比亚迪股份有限公司 | Aluminum-base composite material and preparation method thereof |
| CN101748306A (en) * | 2008-12-02 | 2010-06-23 | 苏州有色金属研究院有限公司 | Multiphase ceramic hybrid composite reinforced metal matrix composite material and preparation process thereof |
| CN101775518A (en) * | 2010-04-02 | 2010-07-14 | 哈尔滨工业大学 | Device and method for preparing particle-reinforced gradient composite materials by using ultrasonic waves |
| CN102260814A (en) * | 2011-07-26 | 2011-11-30 | 吉林大学 | In situ nano TiC ceramic particle reinforced aluminum based composite material and preparation method thereof |
| JP2013036088A (en) * | 2011-08-09 | 2013-02-21 | Isuzu Motors Ltd | Method for producing composite material of ceramic particle-reinforced aluminum-silicon-based alloy |
| US20150007925A1 (en) * | 2013-07-05 | 2015-01-08 | Deeder Mohammad Aurongzeb | High-strength structural elements using metal foam for portable information handling systems |
| CN105441734A (en) * | 2014-09-30 | 2016-03-30 | 黄晓艺 | Al-Si-Mg-Ti-Sr-Fe alloy material and preparation process thereof |
| CN104532068A (en) * | 2014-12-15 | 2015-04-22 | 河海大学 | Nano TiC ceramic particle reinforced aluminum matrix composite and preparation method thereof |
| CN107012354A (en) * | 2017-04-05 | 2017-08-04 | 江苏大学 | A kind of preparation method of Al Si9Cu1 particulate reinforced composites |
| CN108103368A (en) * | 2017-06-12 | 2018-06-01 | 吉林大学 | The tough as-cast aluminum alloy of novel high-strength and preparation method |
| CN109055860A (en) * | 2018-09-07 | 2018-12-21 | 吉林大学 | One specific admixture scale TiCN and TiB2Particle Strengthening and Toughening low-alloy steel and preparation method thereof |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111041297A (en) * | 2019-12-17 | 2020-04-21 | 江苏大学 | High-corrosion-resistance in-situ nanoparticle reinforced aluminum-based composite material and preparation method thereof |
| CN113073253A (en) * | 2021-03-31 | 2021-07-06 | 浙江理工大学 | Method for preparing nanoparticle reinforced nodular cast iron by using aluminum-based intermediate alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| CN109554570B (en) | 2020-07-31 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN107955888B (en) | A kind of micro-nano TiC-TiB for aluminium alloy2Grain refiner and thinning method | |
| CN100519791C (en) | A method of and a device for producing a liquid-solid metal composition | |
| CN109554572B (en) | Multi-scale ceramic particle-mixed high-elasticity-modulus high-strength aluminum alloy and preparation method thereof | |
| CN1195090C (en) | Mixed salt process to preparing in-situ reinforced Mg-based composite material | |
| EP1737993B1 (en) | Improved recycling method for al-b, c composite materials | |
| CN109576526A (en) | A kind of molten internal in-situ multiphase mixes scale ceramic reinforced Al-Zn-Mg-Cu aluminium alloy and preparation method thereof | |
| CN109554570A (en) | A kind of molten internal in-situ multiphase mixes the method for scale ceramic reinforced aluminium alloy | |
| WO2021035772A1 (en) | Manufacturing method for rare-earth magnesium alloy composite material | |
| CN109609814A (en) | A kind of double scale ceramic particles mix high elastic modulus high-strength aluminum alloy and preparation method thereof | |
| WO2021035774A1 (en) | Preparation method for lithium-containing magnesium/aluminum-based composite material | |
| CN1995418A (en) | Preparation method of granule-mixed reinforced aluminium-based composite material | |
| CN1327020C (en) | Method for preparing aluminium based composite material enhanced by miscellaneous granules in situ | |
| CN109439951B (en) | Method for strengthening aluminum-silicon alloy based on multiphase mixed scale ceramic particle enhancer | |
| CN109609798A (en) | A kind of micro micro-nano miscellaneous granules REINFORCED Al-Cu-Mg-Si plate controlled rolling preparation method | |
| CN100465317C (en) | Special-purpose multi-component low rare earth vermiculizer for producing thick wall Vermicular iron element by furnace cupola | |
| CN109439973B (en) | Aluminum-silicon alloy based on multiphase mixed scale ceramic particles and preparation method thereof | |
| CN109680180A (en) | A method of strengthening Al-Zn-Mg-Cu aluminum alloy extrusion section bar | |
| CN109576525A (en) | A method of strengthening 7075 aluminum alloy rolled plates | |
| CN112853175B (en) | Preparation method of high-strength and high-toughness aluminum alloy section based on nano in-situ/precipitated phase regulation mechanism | |
| CN1089118C (en) | Telchnique for preparing in-situ authigenic metal-base composite material | |
| CN109022888A (en) | Novel in-situ authigenic transcocrystallized Al-Si alloy composite modifier and preparation method thereof | |
| CN108103330A (en) | A kind of preparation method of die-cast aluminum alloy material | |
| CN100491563C (en) | Grain-mixing strengthened aluminum-base composite material | |
| CN109628788B (en) | Method for preparing high-elasticity-modulus and high-strength aluminum alloy by mixing multi-phase ceramic particles | |
| CN109396422B (en) | A kind of method evenly dispersed in the pre-dispersed complementary melt of nano particle in parcel |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20240324 Address after: 266000 No.1 Loushan Road, Licang District, Qingdao City, Shandong Province Patentee after: QINGDAO AUTOMOTIVE RESEARCH INSTITUTE, JILIN University Country or region after: China Patentee after: Jilin University Address before: 266000 No.1 Loushan Road, Licang District, Qingdao City, Shandong Province Patentee before: QINGDAO AUTOMOTIVE RESEARCH INSTITUTE, JILIN University Country or region before: China |