CN105483577A - Heat treatment technology of eutectic Al-Si-Cu-Mn heat-resistant aluminum alloy - Google Patents
Heat treatment technology of eutectic Al-Si-Cu-Mn heat-resistant aluminum alloy Download PDFInfo
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- CN105483577A CN105483577A CN201511009957.3A CN201511009957A CN105483577A CN 105483577 A CN105483577 A CN 105483577A CN 201511009957 A CN201511009957 A CN 201511009957A CN 105483577 A CN105483577 A CN 105483577A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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Abstract
The invention discloses a heat treatment technology of a eutectic Al-Si-Cu-Mn heat-resistant aluminum alloy. The heat-resistant aluminum alloy comprises the following components by weight percent: 10.0-13.0% of silicon, 3.0-4.5% of copper, 0.8-2.5% of manganese, 0.02-0.03% of strontium and the balance of aluminum. The technology comprises the steps of heating a heat-resistant aluminum alloy workpiece to 480 to 525 DEG C, keeping the temperature for 5 to 20 h, precipitating the heat-resistant aluminum alloy workpiece for separating out 100 to 200 nm Al15Mn3Si2 phase and Al20Mn3Cu2 phase particles as heat resistant phases, distributing the particles in Al matrix crystalline grains, partly dissolving eutectic copper-rich phase theta (CuAl2), and granulating and roughening the residual theta (CuAl2) phase; immediately soaking the workpiece in water with the temperature of 20 to 65 DEG C for quenching treatment; and carrying out aging treatment on the quenched heat-resistant aluminum alloy workpiece for 4 to 6 h at the temperature of 160 to 180 DEG C.
Description
Technical field
The field that the present invention relates to belongs to metal heat treatmet field, is specifically related to a kind of heat-resisting aluminium alloy thermal treatment process.
Background technology
The mechanical property of casting Al-Si alloy under as cast condition often can not meet its service requirements, so need the mechanical property being improved foundry goods by thermal treatment further.The thermal treatment of aluminium alloy, is exactly the tissue by adjustment alloy, gives full play to the potential characteristic of alloy.Usually, the strengthen connotation of aluminium alloy comprises solution treatment, quenching and ageing treatment (natural aging, artificial aging).Wherein T6 process is the most frequently used a kind of thermal treatment process of casting Al-Si alloy, namely quenches after solution treatment, then carries out artificial age-hardening's process, do not carry out cold working like this and just can obtain good strength.
The solution treatment of aluminium alloy can make this kind of sclerosis phase such as Cu, Mg and Si solute dissolve in α-Al matrix, microstructure homogenization can also be made, reduce the solute element segregation that formed in process of setting, for the precipitation of dispersion-strengthened phase during ageing treatment creates a good condition.In addition, solution treatment can change the quantity of the second-phase in aluminium alloy, size and form, for follow-up ageing treatment carries out structural preparation.Therefore, aluminum alloy T 6 process first stage---solution treatment is regarded as the critical stage of the mechanical property determining dispersion-strengthened phase microstructure and final alloy after timeliness.
As-quenched temper is not the finished heat treatment state of casting Al-Si alloy usually, and the mechanical property of alloy needs just can be improved significantly by the artificial aging of carrying out subsequently.Alloy obtains the sosoloid of hypersaturated state after solution treatment, and supersaturated solid solution is metastable mostly, place or be elevated to after certain temperature carries out insulation for some time in room temperature, to decompose gradually, separate out second-phase or form solute atoms accumulation area and metastable transition phase, this process is called precipitation.Desolvation process makes precipitation in the certain area of solute atoms in sosoloid dot matrix, assembles, forms cenotype, causes the Microstructure and properties of alloy to change, is called timeliness.Timeliness can be divided into natural aging and artificial aging, and natural aging is the precipitation process that at room temperature just can carry out, and artificial aging is heated to certain temperature artificially, and atom action ability is increased, and supersaturation solute atoms is separated out, and reaches the object of sclerosis.
At present, hypoeutectic class Al-Si-Cu-Mg is a widely used class alloy in Al-Si series heat resistant aluminium alloy, and it mainly utilizes heat-treatable strengthened copper-rich phase as heat-resisting phase.But these rich copper heat-resisting phase (θ, W are equal) heat resisting temperature the is on the low side and castability of alloy is poor, hot cracking tendency is large etc. limits its development.
Summary of the invention
The object of this invention is to provide a kind of thermal treatment process of eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy, the present invention can improve the comprehensive mechanical property of heat-resisting aluminium alloy, particularly high-temperature capability.
The thermal treatment process of a kind of eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy of the present invention, wherein said heat-resisting aluminium alloy composition is as follows by weight percentage: silicon 10.0-13.0%, copper 3.0-4.5%, manganese 0.8-2.5%, strontium 0.02-0.03%, aluminium is surplus, and described thermal treatment process is as follows:
S1) solution treatment: by described heat-resisting aluminium alloy workpiece heat to 480 ~ 525 DEG C and isothermal holding 5 ~ 20h, heat-resisting aluminium alloy workpiece Precipitation is as the Al of 100 ~ 200 nanosizeds of heat-resisting phase
15mn
3si
2phase and Al
20mn
3cu
2phase particle, and be distributed in Al matrix grain, eutectic copper-rich phase θ (CuAl
2) generating portion is dissolved, residual θ (CuAl
2) there is granulating and alligatoring mutually;
S2) quench treatment: immediately workpiece is immersed in 20 ~ 65 DEG C of water and carry out quench treatment;
S3) ageing treatment: by the heat-resisting aluminium alloy workpiece ageing treatment 4-6h at 160-180 DEG C after quenching, has separated out in heat-resisting aluminium alloy workpiece as promoting alloy hardening main phases precipitated and having needle-like the θ " (CuAl of consistent directivity
2) phase.
Beneficial effect of the present invention is as follows:
In technical scheme of the present invention, eutectic class Al-Si-Cu-Mn refractory alloy introduces the more excellent heat-resisting phase Al of rich Mn of new resistance toheat
15mn
3si
2, making alloy have higher heat resisting temperature, is the very potential heat-resistant aluminium alloy material of one.The Al of eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy 100 ~ 200 nanosizeds that meeting Precipitation is a large amount of after solution treatment in the present invention
15mn
3si
2phase and Al
20mn
3cu
2phase particle, is distributed in Al matrix, and in these solid solution processes, the rich Mn phase of Precipitation significantly improves the thermotolerance of alloy.
After solutionizing step process of the present invention, in tissue, form the Al of a large amount of disperse educt
15mn
3si
2phase and Al
20mn
3cu
2rich manganese strengthened phase particle, significantly improves alloy thermotolerance.Fig. 1 shows the microstructure of heat-resisting aluminium alloy after solution treatment.There is passivation fusing and spheroidizing when solution treatment in eutectic Si particle, its form changes corynebacterium or particulate state into by the threadiness under as cast condition.But when solution treatment overlong time or temperature too high time, then Eutectic Silicon in Al-Si Cast Alloys particle there will be obvious coarsening phenomenon.CuAl
2the quantity of phase reduces to some extent after solution treatment, and has occurred obvious dissolution phenomena and be transformed into particulate state; And form rich manganese in solid solution process in process of setting when reasonable offer, all there is not considerable change in its quantity and form.Fig. 2 shows the micro-vickers hardness of α-Al matrix under the different solution treatment time with the change curve of solid solution temperature, can find: preferably solid solution temperature scope is 495-510 DEG C.Can be found by (a) TEM structure observation in Fig. 3, very clean in Al matrix under as cast condition, almost do not observe any tiny precipitated phase.And by Fig. 3 (b), after 525 DEG C × 20h solution treatment, in Al matrix, there is the tiny in a large number and rich Mn precipitated phase of disperse.Fig. 4 shows these precipitated phase forms and size and corresponding TEM-EDS result and SAD (selected area electron diffraction style) result.XRD result before and after the solution treatment of this eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy as shown in Figure 5, not only Al after solution treatment
15mn
3si
2phase peak strengthens, and has newly occurred Al
20mn
3cu
2peak.Comprehensive above tissue characterization, this eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy is after solution treatment of the present invention, and in aluminum substrate tissue, the tiny Al that size is about 100 ~ 200 nanometers has been separated out in a large amount of intergranular precipitation
15mn
3si
2phase and Al
20mn
3cu
2rich manganese phase particle, they are positioned at Al intrinsic silicon mostly, at high temperature stable existence, hinder the motion of dislocation thus significantly strengthen matrix, improve the thermotolerance that namely Al matrix opposing high temperature deformation ability improves alloy.What carry out after solid solution and quench treatment is ageing treatment thereupon.Fig. 6 is the transmission electron microscope photo of eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy timeliness 6h at 165 DEG C, and contrast pertinent literature is known, and the black needlelike phase in figure is the CuAl that alloy is separated out in ag(e)ing process
2phase, and there is consistent directivity, be the main phases precipitated promoting Alloy At Room Temperature sclerosis.But the CuAl of Precipitation
2can again dissolve after being heated under the service temperature of Xiang Gao, do not have the effect improving alloy thermotolerance, and the rich manganese of solid solution stage disperse educt does not all change in pyroprocessing and low temperature aging process subsequently, it is heat-resisting phase main in eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy.
Accompanying drawing explanation
Fig. 1 is (525 DEG C of+15h) optical microscope picture under alloy solid solution state.
Fig. 2 is the change curve of micro-vickers hardness with solid solution temperature of α-Al matrix under the different solution treatment time.
Fig. 3 is the TEM image of Al-12Si-4Cu-1.2Mn alloy: (a) as cast condition; B () 525 DEG C × 20h as-quenched temper, has separated out a large amount of tiny rich Mn phase.
Fig. 4 is rich Mn phase TEM photo, TEM-EDS result and the TEM-SAD result separated out in Al-12Si-4Cu-1.2Mn alloy 525 DEG C × 20h as-quenched temper tissue, and (a) demonstrates Al
15mn
3si
2phase; B () demonstrates Al
20mn
3cu
2phase.
Fig. 5 is the XRD figure spectrum before and after Al-12Si-4Cu-1.2Mn alloy 525 DEG C × 20h solution treatment, has separated out Al in display solid solution process
15mn
3si
2phase and Al
20mn
3cu
2phase.
Fig. 6 is TEM picture under Al-12Si-4Cu-1.2Mn alloy aging state, has separated out a large amount of needle-like θ " (CuAl in ag(e)ing process
2) mutually and there is consistent directivity.
Embodiment
A thermal treatment process for eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy, described heat-resisting aluminium alloy composition is as follows by weight percentage: silicon 10.0-13.0%, copper 3.0-4.5%, manganese 0.8-2.5%, strontium 0.02-0.03%, aluminium is surplus, and described thermal treatment process is as follows:
S1) solution treatment: by described heat-resisting aluminium alloy workpiece heat to 480 ~ 525 DEG C and isothermal holding 5 ~ 20h, heat-resisting aluminium alloy workpiece Precipitation is as the Al of 100 ~ 200 nanosizeds of heat-resisting phase
15mn
3si
2phase and Al
20mn
3cu
2phase particle, and be distributed in Al matrix, eutectic copper-rich phase θ (CuAl
2) generating portion is dissolved, residual θ (CuAl
2) there is granulating and alligatoring mutually;
S2) quench treatment: immediately workpiece is immersed in 20 ~ 65 DEG C of water and carry out quench treatment;
S3) ageing treatment: by the heat-resisting aluminium alloy workpiece ageing treatment 4-6h at 160-180 DEG C after quenching, has separated out in heat-resisting aluminium alloy workpiece as promoting alloy hardening main phases precipitated and having needle-like the θ " (CuAl of consistent directivity
2) phase.In the present embodiment,
Described eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy is the alloy adopting following preparation method to obtain, and described preparation method is:
S101): by aluminium silicon master alloy, red copper, aluminium manganese master alloy and crystallization silico briquette heat fused, formed the mass percent of element silicon between 10.0 ~ 13.0%, the mass percent of copper 3.0 ~ 4.5%, the alloy melt of mass percent between 0.8 ~ 2.5% of manganese element;
S102): the hexachloroethane adding melt quality 0.06% when alloy melt being heated to 710 ~ 730 DEG C carries out refining, leave standstill after 10 minutes, adding Al, Sr mass ratio is that the Al-Sr master alloy of 9:1 carries out Metamorphism treatment, be incubated 30 minutes, carry out chemical constituents determination, make the mass percent content of strontium Sr in the alloy melt after adding Al-Sr master alloy be 0.02-0.03%;
S103): carry out vacuum subsequently and leave standstill 30-60 minute, reheat and be poured in metal die after 710 ~ 730 DEG C, solidify and form nascent rich manganese phase Al in the alloy
15mn
3si
2, Al
15mn
3si
2the three-phase eutectic of+α-Al+Si and Al
15mn
3si
2+ α-Al+Si+ θ (CuAl
2) four phase eutectics, finally obtain containing nascent rich manganese phase Al
15mn
3si
2, Al
15mn
3si
2the three-phase eutectic of+α-Al+Si and Al
15mn
3si
2+ α-Al+Si+ θ (CuAl
2) four mutually eutectiferous alloys.
Example 1: a kind of thermal treatment process of eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy, each weight percentages of components of described heat-resisting aluminium alloy is as follows: silicon 12%, copper 4%, manganese 1.2%, strontium 0.02-0.03%, and aluminium is surplus; Make to process with the following method: (1) by this heat-resisting aluminium alloy workpiece at 480 ~ 525 DEG C of isothermal holding 5 ~ 20h; (2) immediately quench treatment is carried out by heat-resisting aluminium alloy workpiece immersion 20 ~ 65 DEG C of water after process; (3) by the Al alloy parts ageing treatment 6h at 165 DEG C after quenching.Fig. 2 shows when the solution treatment time is identical, and the micro-vickers hardness of α-Al matrix, with the raising first increases and then decreases of solid solubility temperature, reaches maximum value between 495 ~ 510 DEG C.This is due to when solid solubility temperature is lower, and strengthening phase fully solid solution can not enter matrix, and the change of silicon phase morphology is little; When solid solubility temperature is higher, there is obvious alligatoring in silicon grain, grain boundaries melts, and demonstrates overheated tendency.
Example 2: a kind of thermal treatment process of eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy, makes to process with the following method: (1) by this heat-resisting aluminium alloy workpiece at 480 DEG C of isothermal holding 5h; (2) immediately quench treatment is carried out by heat-resisting aluminium alloy workpiece immersion 20 ~ 65 DEG C of water after process; (3) by the Al alloy parts ageing treatment 6h at 165 DEG C after quenching.Treated alloy tensile strength at 150 DEG C and 250 DEG C reaches 172MPa, 137MPa respectively.
Example 3: a kind of thermal treatment process of eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy, makes to process with the following method: (1) by this heat-resisting aluminium alloy workpiece at 510 DEG C of isothermal holding 5h; (2) immediately quench treatment is carried out by heat-resisting aluminium alloy workpiece immersion 20 ~ 65 DEG C of water after process; (3) by the Al alloy parts ageing treatment 6h at 165 DEG C after quenching.Treated alloy tensile strength at 150 DEG C and 250 DEG C reaches 223MPa, 192MPa respectively.
Example 4: a kind of thermal treatment process of eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy, makes to process with the following method: (1) by this heat-resisting aluminium alloy workpiece at 510 DEG C of isothermal holding 15h; (2) immediately quench treatment is carried out by heat-resisting aluminium alloy workpiece immersion 20 ~ 65 DEG C of water after process; (3) by the Al alloy parts ageing treatment 6h at 165 DEG C after quenching.Treated alloy tensile strength at 150 DEG C and 250 DEG C reaches 201MPa, 132MPa respectively.
Example 5: a kind of thermal treatment process of eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy, makes to process with the following method: (1) by this heat-resisting aluminium alloy workpiece at 525 DEG C of isothermal holding 20h; (2) immediately quench treatment is carried out by heat-resisting aluminium alloy workpiece immersion 20 ~ 65 DEG C of water after process; (3) by the Al alloy parts ageing treatment 6h at 165 DEG C after quenching.Treated alloy tensile strength at 150 DEG C and 250 DEG C reaches 179MPa, 141MPa respectively.
Claims (2)
1. a thermal treatment process for eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy, is characterized in that: described heat-resisting aluminium alloy composition is as follows by weight percentage: silicon 10.0-13.0%, copper 3.0-4.5%, manganese 0.8-2.5%, strontium 0.02-0.03%, aluminium is surplus, and described thermal treatment process is as follows:
S1) solution treatment: by described heat-resisting aluminium alloy workpiece heat to 480 ~ 525 DEG C and isothermal holding 5 ~ 20h, heat-resisting aluminium alloy workpiece Precipitation is as the Al of 100 ~ 200 nanosizeds of heat-resisting phase
15mn
3si
2phase and Al
20mn
3cu
2phase particle, and be distributed in Al matrix grain, eutectic copper-rich phase θ (CuAl
2) generating portion is dissolved, residual θ (CuAl
2) there is granulating and alligatoring mutually;
S2) quench treatment: immediately workpiece is immersed in 20 ~ 65 DEG C of water and carry out quench treatment;
S3) ageing treatment: by the heat-resisting aluminium alloy workpiece ageing treatment 4-6h at 160-180 DEG C after quenching, has separated out in heat-resisting aluminium alloy workpiece as promoting alloy hardening main phases precipitated and having needle-like the θ " (CuAl of consistent directivity
2) phase.
2. the thermal treatment process of eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy as claimed in claim 1, is characterized in that, described eutectic class Al-Si-Cu-Mn heat-resisting aluminium alloy is the alloy adopting following preparation method to obtain, and described preparation method is:
S101): by aluminium silicon master alloy, red copper, aluminium manganese master alloy and crystallization silico briquette heat fused, formed the mass percent of element silicon between 10.0 ~ 13.0%, the mass percent of copper 3.0 ~ 4.5%, the alloy melt of mass percent between 0.8 ~ 2.5% of manganese element;
S102): the hexachloroethane adding melt quality 0.06% when alloy melt being heated to 710 ~ 730 DEG C carries out refining, leave standstill after 10 minutes, adding Al, Sr mass ratio is that the Al-Sr master alloy of 9:1 carries out Metamorphism treatment, be incubated 30 minutes, carry out chemical constituents determination, make the mass percent content of strontium Sr in the alloy melt after adding Al-Sr master alloy be 0.02-0.03%;
S103): carry out vacuum subsequently and leave standstill 30-60 minute, reheat and be poured in metal die after 710 ~ 730 DEG C, solidify and form nascent rich manganese phase Al in the alloy
15mn
3si
2, Al
15mn
3si
2the three-phase eutectic of+α-Al+Si and Al
15mn
3si
2+ α-Al+Si+ θ (CuAl
2) four phase eutectics, finally obtain containing nascent rich manganese phase Al
15mn
3si
2, Al
15mn
3si
2the three-phase eutectic of+α-Al+Si and Al
15mn
3si
2+ α-Al+Si+ θ (CuAl
2) four mutually eutectiferous alloys.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108441722A (en) * | 2018-05-22 | 2018-08-24 | 南通鸿劲金属铝业有限公司 | A kind of corrosion resistance eutectic Al-base alloy material |
| CN109468499A (en) * | 2018-11-26 | 2019-03-15 | 齐鲁工业大学 | A kind of the Al-Si-Cu-Mg-Zn cast alloy materials and its aging technique of high-strength and high ductility |
| CN111763837A (en) * | 2020-06-29 | 2020-10-13 | 东南大学 | Method for refining hypereutectic aluminum-silicon alloy primary silicon phase |
| CN113789453A (en) * | 2021-08-17 | 2021-12-14 | 东南大学 | Method for improving high-temperature strength of heat-resistant aluminum alloy through Mn microalloying |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010255013A (en) * | 2009-04-21 | 2010-11-11 | Sumitomo Light Metal Ind Ltd | Clad material of aluminum alloy for heat exchanger and method for manufacturing the same |
| CN102747256A (en) * | 2012-06-19 | 2012-10-24 | 东南大学 | Aluminum-silicon based aluminum section and preparation technology thereof |
| CN103074556A (en) * | 2012-12-20 | 2013-05-01 | 南昌大学 | Method for solution aging treatment on rare earth-Al alloy |
| CN103526085A (en) * | 2013-11-01 | 2014-01-22 | 邹平宏皓工业型材科技有限公司 | Wear-proof aluminum alloy |
-
2015
- 2015-12-29 CN CN201511009957.3A patent/CN105483577A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010255013A (en) * | 2009-04-21 | 2010-11-11 | Sumitomo Light Metal Ind Ltd | Clad material of aluminum alloy for heat exchanger and method for manufacturing the same |
| CN102747256A (en) * | 2012-06-19 | 2012-10-24 | 东南大学 | Aluminum-silicon based aluminum section and preparation technology thereof |
| CN103074556A (en) * | 2012-12-20 | 2013-05-01 | 南昌大学 | Method for solution aging treatment on rare earth-Al alloy |
| CN103526085A (en) * | 2013-11-01 | 2014-01-22 | 邹平宏皓工业型材科技有限公司 | Wear-proof aluminum alloy |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108441722A (en) * | 2018-05-22 | 2018-08-24 | 南通鸿劲金属铝业有限公司 | A kind of corrosion resistance eutectic Al-base alloy material |
| CN109468499A (en) * | 2018-11-26 | 2019-03-15 | 齐鲁工业大学 | A kind of the Al-Si-Cu-Mg-Zn cast alloy materials and its aging technique of high-strength and high ductility |
| CN111763837A (en) * | 2020-06-29 | 2020-10-13 | 东南大学 | Method for refining hypereutectic aluminum-silicon alloy primary silicon phase |
| CN113789453A (en) * | 2021-08-17 | 2021-12-14 | 东南大学 | Method for improving high-temperature strength of heat-resistant aluminum alloy through Mn microalloying |
| CN113789453B (en) * | 2021-08-17 | 2023-08-01 | 东南大学 | Method for improving high-temperature strength of heat-resistant aluminum alloy through Mn microalloying |
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Application publication date: 20160413 |