CN103993208A - Al-Mg-Si-Cu-Mn-Er alloy material and preparation method thereof - Google Patents

Al-Mg-Si-Cu-Mn-Er alloy material and preparation method thereof Download PDF

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CN103993208A
CN103993208A CN201410234860.1A CN201410234860A CN103993208A CN 103993208 A CN103993208 A CN 103993208A CN 201410234860 A CN201410234860 A CN 201410234860A CN 103993208 A CN103993208 A CN 103993208A
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CN103993208B (en
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陈文琳
吴跃
高妍
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Hefei University of Technology
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Hefei University of Technology
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Abstract

The invention discloses an Al-Mg-Si-Cu-Mn-Er alloy material and a preparation method thereof. The alloy material is characterized by containing rare earth Er of which the mass percentage is 0.15%-0.45%. According to the alloy material and the preparation method disclosed by the invention, since rare earth Er of which the mass percentage is 0.15%-0.45% is added into the Al-Mg-Si-Cu-Mn alloy material, the contents of other alloying elements are reasonably designed, and a reasonable melting process and rapid solidification technology are adopted and repeated rolling and a suitable heat treatment are carried out, and thus the Al-Mg-Si-Cu-Mn-Er alloy material with uniform and fine microstructure is prepared; the obtained material has the advantages of relatively high plasticity and strength, tensile strength not less than 388MPa and elongation not less than 24%.

Description

A kind of Al-Mg-Si-Cu-Mn-Er alloy material and preparation method thereof
Technical field
The invention belongs to non-ferrous metal technical field, be specifically related to a kind of Al-Mg-Si-Cu-Mn-Er alloy material and preparation method thereof
Background technology
Aluminium alloy density is low, intensity is high, be easy to processing, has good solidity to corrosion, is widely used in the field such as aerospace, communications and transportation, is most widely used alloy in light metal, and its usage quantity is only second to iron and steel.In fields such as aerospace, ocean, transports, adopt aluminium alloy to replace iron and steel, be a kind of effective ways that reduce energy consumption.Density is little for 6xxx line aluminium alloy (Al-Mg-Si alloy), welding property and corrosion stability is good, impelling strength is high and be easy to machine-shaping, is Materials science worker's study hotspot always.
New millennium, along with the continuous progress of science and technology, in order further to adapt to each field for the more requirement of the aspect over-all properties such as high strength, toughness, antifatigue of material, need aluminium alloy to there is higher over-all properties.But traditional Al-Mg-Si alloy strength is not high, and plasticity is also to be improved.Now there are some researches show, microalloying of rare earth is to improve one of aluminium alloy capability and the of paramount importance means of development of new aluminium alloy.Rare earth element er can form A1 in Al-Mg and Al-Zn-Mg alloy 3er phase, A1 3er phase and Al matrix coherence, its strengthening mechanism mainly contains refined crystalline strengthening, precipitation strength and substructure strengthening etc.In Al-Mg alloy and Al-Zn-Mg alloy, add Er not only significantly refined cast structure, raising alloy strength, can also effectively suppress alloy generation recrystal grain and grow up, put forward heavy alloyed recrystallization temperature.Meanwhile, Er price comparison is cheap, adds rare earth Er and can not increase substantially production cost in aluminium alloy, is therefore highly suitable in industry and promotes the use of.Al-Mg-Si alloy is a kind of typical commercial aluminum alloy, it is studied to develop a series of novel rare-earth aluminium alloys containing Er, and be widely used in the numerous areas such as Aeronautics and Astronautics, communications and transportation, has important theory and practice meaning.But relevant Al-Mg-Si-Cu-Mn-Er alloy there is not yet any report so far.
Summary of the invention
The object of the present invention is to provide a kind of novel Al-Mg-Si-Cu-Mn-Er alloy, to improving intensity and the plasticity of Al-Mg-Si alloy, meet better the demand of the field such as Aeronautics and Astronautics, traffic to high-performance aluminium alloy.
Object of the present invention is achieved through the following technical solutions:
Al-Mg-Si-Cu-Mn-Er alloy material of the present invention, its feature is: in Al-Mg-Si-Cu-Mn alloy material, contain the rare earth Er that mass percent is 0.15%-0.45%.
Al-Mg-Si-Cu-Mn-Er alloy material of the present invention, its feature is also: each alloying element by the proportioning of mass percent is:
Microalloying is the effective way that improves the over-all propertieies such as the strength of materials and plasticity.Wherein, in Al-Mg-Si-Cu-Mn-Er alloy material, when Mg and Si massfraction ratio are 1.73:1, can make alloy after solid solution aging, in matrix, separate out the Mg of a large amount of disperses 2si strengthening phase, in the present invention, some surplus of Si, can in and the detrimentally affect of Fe etc. in impurity, the Mg of refinement simultaneously 2si particle.In alloy, add the Cu of 0.65%-0.72%, object is to improve the plasticity of alloy in the time of hot-work, strengthens heat treatment reinforcement effect, improves unit elongation.In alloy, add the Mn of 0.18%-0.21%, object is to stop the recrystallize of alloy in deformation after unloading process by forming disperse phase, thereby improves recrystallization temperature, refinement recrystal grain, forming property and the intensity of raising Al-Mg-Si-Cu-Mn-Er alloy.Meanwhile, add the Er of 0.15%-0.45% in alloy, object is remarkable refined cast structure, improves alloy strength, and effectively suppresses alloy generation recrystal grain and grow up, and puies forward heavy alloyed recrystallization temperature.
The preparation method of Al-Mg-Si-Cu-Mn-Er alloy material of the present invention, its feature is to operate as follows:
Step 1: prepare alloy cast ingot
1a, batching: according to the mass percent of Al, Mg, Si, Cu, Mn and Er, take metal A l, Al-Mg master alloy, Al-Si master alloy, Al-Cu master alloy, Al-Mn master alloy and Al-Er master alloy, as batching;
1b, fusing: first join using metal A l, Al-Mn master alloy, Al-Si master alloy and Al-Cu master alloy as raw material group A in the crucible that is preheated to 280 DEG C that (object of crucible preheating is to remove moisture, prevent cracking), be heated to 730 DEG C, when constant temperature stays to raw material group A is softening, sprinkle insulating covering agent (insulating covering agent is for preventing that raw material group A from contacting and being oxidized with air, simultaneously also in order to reduce the oxide film of incoming stock group of A) on raw material group A surface; When continuation constant temperature melts completely to raw material group A, obtain melt B;
The quality optimization that sprinkles insulating covering agent on raw material group A surface is 0.5% of batching total mass.(0.5% is optimum value, experimental results show that in the interval of 0.5%-0.6% and all can realize)
1c, add Al-Mg master alloy: (690 DEG C is optimum value to be cooled to 690 DEG C, experimental results show that in the interval of 680 DEG C-700 DEG C and all can realize), in melt B, add Al-Mg master alloy, be stirred to Al-Mg master alloy and melt completely, obtain melt C; For preventing the scaling loss of Al-Mg master alloy, can use aluminium foil parcel and rapidly Al-Mg master alloy is pressed into melt B bottom, then melt B be covered with insulating covering agent, reduce the scaling loss of magnesium;
1d, add Al-Er master alloy: be warming up to 750 DEG C, add Al-Er master alloy (for reducing the scaling loss of rare earth Er, Al-Er alloy is wrapped with aluminium foil, and rapidly Al-Er master alloy is pressed into bottom melt C), sprinkle insulating covering agent, constant temperature to Al-Er master alloy melts completely, obtains melt D;
1e, refining: be cooled to 720 DEG C, in melt D, add refining agent C 2cl 6, by C 2cl 6be immersed in melt D and extremely emerge without yellow gas, leave standstill insulation 20min (make the abundant refining of melt D, improve the purity of melt D); C 2cl 6quality optimization be 0.5% (0.5% for optimum value, experimental results show that in the interval of 0.5%-0.6% and all can realize) of batching total mass;
1f, cast: use the casting mould of brass material to complete the cast to melt D, obtain alloy cast ingot; Adopt the cooling rate of copper casting mould fast, in the time of cast, can pass into cold water further to improve speed of cooling, casting process is wanted quick and stable, and rapid solidification can crystal grain thinning, thereby improves the performances such as alloy strength and plasticity.
Step 2: described alloy cast ingot is carried out to homogenizing processing, viscous deformation acquisition Al-Mg-Si-Cu-Mn-Er sheet alloy successively, and then described Al-Mg-Si-Cu-Mn-Er sheet alloy is heat-treated, obtain Al-Mg-Si-Cu-Mn-Er alloy material.
Described homogenizing processing is that step 1 gained alloy cast ingot is heated to 550 DEG C and be incubated 11h, and then air cooling is to room temperature.
Described viscous deformation is that alloy cast ingot after treatment homogenizing is incubated to 30min under 465 DEG C of conditions, then carry out multi-pass hot rolling, after every time hot rolling, under 465 DEG C of conditions, be incubated 5min, carry out again lower a time hot rolling, the working modulus of every time hot rolling is no more than 25%, and the general working rate of hot rolling is at 60%-70%; After hot rolling finishes, to anneal, annealing conditions is: at 415 DEG C, be incubated 2h, then air cooling is to room temperature; After annealing finishes, then it is cold rolling to carry out multi-pass, obtains Al-Mg-Si-Cu-Mn-Er sheet alloy, and cold rolling every time working modulus is 10%-20%, and cold rolling general working rate is 60%-70%.Repeatedly the object of rolling is: realize large plastometric set, inclusion is smashed, effectively eliminate the defects such as alloy cast ingot internal porosity and shrinkage porosite, on microcosmic, make particle size distribution more even, and reduce the internal stress of alloy cast ingot because of the inhomogeneous generation of speed of cooling simultaneously.If cold rolling altogether n passage, in the time that n is even number, once anneal after cold rolling completing n/2 passage, and then it is cold rolling to continue lower a time; In the time that n is odd number, once anneal after cold rolling completing (n+1)/2 passage, and then it is cold rolling to continue lower a time; Annealing conditions is: under 415 DEG C of conditions, be incubated 2h, then air cooling is to room temperature.Carry out after half passage cold rolling, the object of annealing is to prevent that the cold rolling accumulation strain of multi-pass is excessive, causes work hardening phenomenon serious, brings difficulty to follow-up cold rolling processing.
Described thermal treatment is that the Al-Mg-Si-Cu-Mn-Er sheet alloy obtaining after viscous deformation is carried out to solution treatment and ageing treatment successively;
Described solution treatment is that Al-Mg-Si-Cu-Mn-Er sheet alloy is heated to 555 DEG C, insulation 45min, and then shrend is to room temperature, obtains sheet alloy after solid solution, and quenching shift time is not more than 25s;
Described ageing treatment is that sheet alloy after solid solution is warming up to 175 DEG C, insulation 8h, and then air cooling, to room temperature, obtains Al-Mg-Si-Cu-Mn-Er alloy material.
Preferably, after step 1b completes, skim, and then carry out step 1c;
After step 1c completes, first skim, and then carry out step 1d;
After step 1d completes, first skim, and then carry out step 1e;
After step 1e completes, first skim, and then carry out step 1f.
In addition, in preparation process, can constantly there is scum silica frost to produce, can repeatedly skim, to reduce impurity in melt.
Compared with the prior art, beneficial effect of the present invention is embodied in:
1, the present invention is by rare earth Er element microalloying, the content of other element of appropriate design, and adopt reasonable melting technology and flash set technology, prepare evenly tiny Al-Mg-Si-Cu-Mn-Er alloy material of microstructure, and gained alloy material has higher intensity and plasticity;
2, the present invention, by rational rolling technology, realizes large plastometric set, effectively eliminates the defects such as inside ingot pore and shrinkage porosite, makes particle size distribution more even, thereby put forward heavy alloyed over-all properties on microcosmic simultaneously;
3, alloy preparation process of the present invention and heat treatment mode are simple, and production cost is not high, easily realizes suitability for industrialized production.
Brief description of the drawings
Fig. 1 is every time working modulus schematic diagram of the Al-Mg-Si-Cu-Mn-Er alloy material operation of rolling of the present invention;
Fig. 2 is Al-Mg-Si-Cu-Mn-Er alloy material operation of rolling general working rate schematic diagram of the present invention;
Fig. 3 is the as-cast metallographic structure of each embodiment gained alloy cast ingot, wherein Fig. 3 (a) is Al-Mg-Si-Cu-Mn-0Er alloy cast ingot, Fig. 3 (b) is Al-Mg-Si-Cu-Mn-0.15Er alloy cast ingot, Fig. 3 (c) is Al-Mg-Si-Cu-Mn-0.3Er alloy cast ingot, and Fig. 3 (d) is Al-Mg-Si-Cu-Mn-0.45Er alloy cast ingot;
Fig. 4 is that the tensile property of alloy is with the change curve of Er content.
Specific embodiment
Below in conjunction with embodiment, the present invention is further described, and following embodiment is illustrative, is not determinate, can not limit protection scope of the present invention with following embodiment.
Embodiment 1
The present embodiment is prepared Al-Mg-Si-Cu-Mn-0.15Er alloy material as follows:
Step 1: prepare alloy cast ingot
1a, batching: according to the mass percent of 97.45%Al, 0.9%Mg, 0.6%Si, 0.7%Cu, 0.2%Mn and 0.15%Er, take 1142.5g metal A l (purity is 99.99%), 23.2gAl-50.38%Mg master alloy, 71.4gAl-10.92%Si master alloy, 25gAl-10.4%Mn master alloy, 18.2gAl-50.02%Cu master alloy and 19.7gAl-9.92%Er master alloy and prepare burden, batching total mass is 1300g;
1b, fusing: first metal 1142.5g Al, 25g Al-Mn master alloy, 71.4g Al-Si master alloy and 18.2g Al-Cu master alloy are joined in the crucible that is preheated to 280 DEG C as raw material group A, be heated to 730 DEG C, when constant temperature stays to raw material group A is softening (the present embodiment is 5 minutes), sprinkle 6.5g insulating covering agent on raw material group A surface; When continuation constant temperature melts completely to raw material group A, then skim, obtain melt B;
1c, add Al-Mg master alloy: be cooled to 690 DEG C, in melt B, add 23.2gAl-50.38%Mg master alloy, be stirred to 23.2gAl-50.38%Mg master alloy and melt completely, then skim, obtain melt C;
1d, add Al-Er master alloy: be warming up to 750 DEG C, add 19.7gAl-9.92%Er master alloy (for reducing the scaling loss of rare earth Er, Al-Er master alloy is wrapped with aluminium foil, and rapidly Al-Er master alloy is pressed into bottom melt C), sprinkle 6.5 insulating covering agents, constant temperature to 19.7gAl-9.92%Er master alloy melts completely, skims, and obtains melt D;
1e, refining: be cooled to 720 DEG C, in melt D, add 6.5g C 2cl 6, by C 2cl 6be immersed in melt D and extremely emerge without yellow gas, then leave standstill insulation 20min; Then skim;
1f, cast: use the casting mould of brass material to complete the cast to melt D, obtain the thick Al-Mg-Si-Cu-Mn-0.15Er alloy cast ingot of 10mm.
Step 2: alloy ingot casting carries out homogenizing processing, homogenizing treatment condition are: 550 DEG C of homogenization temperatures, soaking time 11h, air cooling is to room temperature.
Step 3: viscous deformation
By alloy cast ingot scale removal after treatment homogenizing and milling face, control final thickness is 8mm, under 465 DEG C of conditions, is incubated 30min, then on two roller hot rollss, is first hot-rolled down to 3mm and is cold-rolled to 1mm again, obtains Al-Mg-Si-Cu-Mn-0.15Er sheet alloy; Concrete steps are: by alloy cast ingot scale removal after treatment homogenizing and milling face, control final thickness is 8mm, under 465 DEG C of conditions, be incubated 30min, then on two roller hot rollss, carry out hot rolling, after every time hot rolling, first melt down heating (being incubated 5min under 465 DEG C of conditions), carry out again lower a time hot rolling, as shown in Figure 1, every time working modulus of hot rolling is followed successively by 23.5%, 19.9%, 16.3%, 14.6% and 16.6%, carry out altogether 5 passage hot rollings, hot rolling general working rate is 62.5%, and after hot rolling, alloy cast ingot thickness is 3mm; After hot rolling, anneal, the condition of annealing is: be warming up to 415 DEG C, and insulation 2h, air cooling is to room temperature; Cold rolling again after annealing, as shown in Figure 1, cold rolling every time working modulus is followed successively by 10%, 11.1%, 12.5%, 14.3%, 16.7%, 20% and 16.7%, carries out altogether 7 passages cold rolling, and cold rolling general working rate is 66.7%, and cold rolling rear alloy cast ingot thickness is 1mm; Once anneal after 4 passages cold rolling carrying out, and then it is cold rolling to carry out the 5th passage, annealing conditions is: be warming up to 415 DEG C, and insulation 2h, air cooling is to room temperature; Cold rolling rear acquisition Al-Mg-Si-Cu-Mn-Er sheet alloy.Fig. 2 is operation of rolling general working rate schematic diagram, as seen from the figure through 5 passage hot rollings and 7 passages cold rolling after, operation of rolling general working rate is 87.5%.
Step 4: Al-Mg-Si-Cu-Mn-0.15Er sheet alloy is heat-treated
4a, solution treatment: the Al-Mg-Si-Cu-Mn-0.15Er sheet alloy that step 3 is obtained is heated to 555 DEG C, insulation 45min, then to room temperature, quenching shift time (transferring to the time water from process furnace after completing heating) is not more than 25s in shrend (transfer in water carry out cooling);
4b, ageing treatment: be warming up to 175 DEG C, insulation 8h, then air cooling, to room temperature, obtains Al-Mg-Si-Cu-Mn-0.15Er alloy material.
For the mechanical property of test Al-Mg-Si-Cu-0.15Er alloy material, it is carried out to tensile test at room temperature, and concrete steps are: after cold rolling, 1mm sheet alloy is made to standard tensile sample according to GB GB6397-86, and then carry out step 4, obtain alloy sample.The mechanical property of testing gained alloy sample on the miniature control electronic universal tester of SANS-100kN, draw speed is 1mm/min; 3 alloy samples of replication are also averaged, and gained mechanical performance index is: tensile strength is 388MPa, and yield strength is 357MPa, and unit elongation is 26.36%, refers to table 1.
Embodiment 2
The present embodiment is prepared Al-Mg-Si-Cu-Mn-0.3Er alloy material by the step identical with embodiment 1, difference is in step 1a according to the mass percent of 97.3%Al, 0.9%Mg, 0.6%Si, 0.7%Cu, 0.2%Mn and 0.3%Er, take 1122.8g metal A l (purity is 99.99%), 23.2gAl-50.38%Mg master alloy, 71.4gAl-10.92%Si master alloy, 25gAl-10.4%Mn master alloy, 18.2gAl-50.02%Cu master alloy and 39.4gAl-9.92%Er master alloy and prepare burden, batching total mass is 1300g;
By the method that embodiment 1 is identical, Al-Mg-Si-Cu-Mn-0.3Er alloy material is carried out to tensile test at room temperature, gained mechanical performance index: tensile strength is 402MPa, yield strength is 378MPa, and unit elongation is 26.27%, refers to table 1.
Embodiment 3
The present embodiment is prepared Al-Mg-Si-Cu-Mn-0.45Er alloy material by the step identical with embodiment 1, difference is in step 1a according to the mass percent of 97.15%Al, 0.9%Mg, 0.6%Si, 0.7%Cu, 0.2%Mn and 0.45%Er, take 1103.1g metal A l (purity is 99.99%), 23.2gAl-50.38%Mg master alloy, 71.4gAl-10.92%Si master alloy, 25gAl-10.4%Mn master alloy, 18.2gAl-50.02%Cu master alloy and 59.1gAl-9.92%Er master alloy and prepare burden, batching total mass is 1300g;
By the method that embodiment 1 is identical, Al-Mg-Si-Cu-Mn-0.45Er alloy material is carried out to tensile test at room temperature, gained mechanical performance index: tensile strength is 394MPa, yield strength is 369MPa, and unit elongation is 24.48%, refers to table 1.
Comparative example
For the impact of contrast rare earth Er on Al-Mg-Si-Cu-Mn alloy property, prepare Al-Mg-Si-Cu-Mn-0Er alloy material by the mode identical with embodiment 1, difference is only according to 97.6%Al, 0.9%Mg, 0.6%Si, the mass percent of 0.7%Cu and 0.2%Mn, take 1162.2g metal A l (purity is 99.99%), 23.2gAl-50.38%Mg master alloy, 71.4gAl-10.92%Si master alloy, 25gAl-10.4%Mn master alloy and 18.2gAl-50.02%Cu master alloy, batching total mass is 1300g, and that does not carry out step 1d adds Al-Er master alloy.By the method that embodiment 1 is identical, Al-Mg-Si-Cu-Mn-0Er alloy material is carried out to tensile test at room temperature, gained mechanical performance index is: tensile strength is 363MPa, and yield strength is 318MPa, and unit elongation is 19.7%, refers to table 1.
After each embodiment interalloy ingot casting preparation (being after step 1 completes), for whether the alloying constituent of determining alloy cast ingot meets the demands, adopt LEEMAN SPEC-E type inductively coupled plasma atomic emission spectrometer to carry out composition detection to all alloy cast ingots, test result, in table 1, illustrates that the melting technology of the present invention's employing can be prepared the Al-Mg-Si-Cu-Er alloy cast ingot that composition meets design requirement.
Get alloy cast ingot sample (being the sample after step 1 completes), in the metallographic structure of MR5000 type metallography microscope Microscopic observation.Fig. 3 (a), 3 (b), 3 (c) and 3 (d) are respectively the as-cast metallographic structure of Al-Mg-Si-Cu-Mn-0Er alloy, Al-Mg-Si-Cu-Mn-0.15Er alloy, Al-Mg-Si-Cu-Mn-0.3Er alloy and Al-Mg-Si-Cu-Mn-0.45Er alloy.As seen from the figure, add significantly refined cast structure of rare earth Er in Al-Mg-Si-Cu-Mn alloy, and add when 0.3%Er, the refinement of Al-Mg-Si-Cu-Mn As-cast Microstructure is the most obvious.
Contrast the mechanical performance index of the alloy material of different Er content, test result as shown in Figure 4.As shown in Figure 4, add rare earth Er and can improve by a relatively large margin Al-Mg-Si-Cu-Mn strength of alloy, yield strength and plasticity (Al-Mg-Si-Cu-Mn strength of alloy is 363MPa, and yield strength is 318MPa, and unit elongation is 19.7%).In the time that Er content is 0.15%-0.45%, the intensity of Al-Mg-Si-Cu-Mn-Er alloy and plasticity are all higher than Al-Mg-Si-Cu-Mn alloy, in the time that Er content is 0.3%, intensity reaches maximum value, and plasticity also approaches maximum value, the tensile strength that is Al-Mg-Si-Cu-Mn-0.3Er alloy is 402MPa, and yield strength is 378MPa, and unit elongation is 26.27%.Here rare earth Er is to the mainly refinement to as-cast structure from Er of the strengthening effect of Al-Mg-Si-Cu-Mn alloy, and grows up because the interpolation of Er suppresses alloy generation recrystal grain, forms and enriches substructure tissue, strengthens thereby realize substructure.
The chemical composition of table 1 alloy and mechanical performance index

Claims (7)

1. an Al-Mg-Si-Cu-Mn-Er alloy material, is characterized in that: in Al-Mg-Si-Cu-Mn alloy material, contain the rare earth Er that mass percent is 0.15%-0.45%.
2. Al-Mg-Si-Cu-Mn-Er alloy material according to claim 1, is characterized in that: in described Al-Mg-Si-Cu-Mn-Er alloy material, each alloying element by the proportioning of mass percent is:
3. a preparation method for the Al-Mg-Si-Cu-Mn-Er alloy material described in claim 1 or 2, is characterized in that carrying out as follows:
Step 1: prepare alloy cast ingot
1a, batching: according to the mass percent of Al, Mg, Si, Cu, Mn and Er, take metal A l, Al-Mg master alloy, Al-Si master alloy, Al-Cu master alloy, Al-Mn master alloy and Al-Er master alloy, as batching;
1b, fusing: first metal A l, Al-Mn master alloy, Al-Si master alloy and Al-Cu master alloy are joined in the crucible that is preheated to 280 DEG C as raw material group A, be heated to 730 DEG C, when constant temperature stays to raw material group A is softening, sprinkle insulating covering agent on raw material group A surface; When continuation constant temperature melts completely to raw material group A, obtain melt B;
1c, add Al-Mg master alloy: be cooled to 690 DEG C, in melt B, add Al-Mg master alloy, be stirred to Al-Mg master alloy and melt completely, obtain melt C;
1d, add Al-Er master alloy: be warming up to 750 DEG C, add Al-Er master alloy, sprinkle insulating covering agent, constant temperature to Al-Er master alloy melts completely, obtain melt D;
1e, refining: be cooled to 720 DEG C, in melt D, add refining agent C 2cl 6, by C 2cl 6be immersed in melt D and extremely emerge without yellow gas, then leave standstill insulation 20min; Add C 2cl 6quality be batching total mass 0.5%;
1f, cast: use the casting mould of brass material to complete the cast to melt D, obtain alloy cast ingot;
Step 2: described alloy cast ingot is carried out to homogenizing processing, viscous deformation acquisition Al-Mg-Si-Cu-Mn-Er sheet alloy successively, and then described Al-Mg-Si-Cu-Mn-Er sheet alloy is heat-treated, obtain Al-Mg-Si-Cu-Mn-Er alloy material.
4. preparation method according to claim 3, is characterized in that:
Described homogenizing processing is that step 1 gained alloy cast ingot is heated to 550 DEG C and be incubated 11h, and then air cooling is to room temperature.
5. preparation method according to claim 3, is characterized in that:
Described viscous deformation is that alloy cast ingot after treatment homogenizing is incubated to 30min under 465 DEG C of conditions, then carry out multi-pass hot rolling, after every time hot rolling, under 465 DEG C of conditions, be incubated 5min, carry out again lower a time hot rolling, the working modulus of every time hot rolling is no more than 25%, and the general working rate of hot rolling is at 60%-70%;
After hot rolling finishes, to anneal, annealing conditions is: under 415 DEG C of conditions, be incubated 2h, then air cooling is to room temperature;
After annealing finishes, then it is cold rolling to carry out multi-pass, obtains Al-Mg-Si-Cu-Mn-Er sheet alloy, and cold rolling every time working modulus is 10%-20%, and cold rolling general working rate is 60%-70%.
6. preparation method according to claim 3, is characterized in that: described thermal treatment is that the Al-Mg-Si-Cu-Mn-Er sheet alloy obtaining after viscous deformation is carried out to solution treatment and ageing treatment successively;
Described solution treatment is that Al-Mg-Si-Cu-Mn-Er sheet alloy is heated to 555 DEG C, insulation 45min, and then shrend is to room temperature, obtains sheet alloy after solid solution, and quenching shift time is not more than 25s;
Described ageing treatment is that sheet alloy after solid solution is warming up to 175 DEG C, insulation 8h, and then air cooling, to room temperature, obtains Al-Mg-Si-Cu-Mn-Er alloy material.
7. preparation method according to claim 3, is characterized in that: establish cold rolling altogether n passage, in the time that n is even number, once anneal after cold rolling completing n/2 passage, and then it is cold rolling to continue lower a time; In the time that n is odd number, once anneal after cold rolling completing (n+1)/2 passage, and then it is cold rolling to continue lower a time;
Annealing conditions is: at 415 DEG C, be incubated 2h, then air cooling is to room temperature.
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CN105803278A (en) * 2016-04-08 2016-07-27 董超超 Novel high-strength corrosion-resistant aluminum alloy door and window
CN105838949A (en) * 2016-04-08 2016-08-10 董超超 Novel high-strength corrosion-resistant electrical connector element
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CN105861895A (en) * 2016-04-08 2016-08-17 董超超 Novel high-strength corrosion-resistant building curtain wall framework
CN105886864A (en) * 2016-04-08 2016-08-24 董超超 Novel high-strength anticorrosion aluminum alloy high-voltage vacuum power distribution cabinet
CN106399781A (en) * 2016-12-05 2017-02-15 合肥工业大学 Novel high-strength corrosion-resistant rare earth aluminum alloy material and preparation method
CN107022726A (en) * 2017-04-28 2017-08-08 重庆市科学技术研究院 A kind of method for refining the almag as-cast grain containing Er
CN107587013A (en) * 2017-07-28 2018-01-16 宁波华源精特金属制品有限公司 A kind of right end socket
CN112941347A (en) * 2021-01-27 2021-06-11 北京工业大学 Al-Mg-Si-Cu-Er alloy for low-sensitivity aging process and preparation process
CN115198151A (en) * 2022-07-21 2022-10-18 栋梁铝业有限公司 Aluminum alloy for automobile and preparation method thereof

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WO2017124823A1 (en) * 2016-01-21 2017-07-27 江苏盐电阀门有限公司 Three-way check valve
CN105734371A (en) * 2016-04-08 2016-07-06 董超超 Novel high-strength corrosion-resistant aluminum alloy pipeline
CN105886864A (en) * 2016-04-08 2016-08-24 董超超 Novel high-strength anticorrosion aluminum alloy high-voltage vacuum power distribution cabinet
CN105803279A (en) * 2016-04-08 2016-07-27 董超超 Novel high-strength corrosion-resistant solar cell frame
CN105803278A (en) * 2016-04-08 2016-07-27 董超超 Novel high-strength corrosion-resistant aluminum alloy door and window
CN105838949A (en) * 2016-04-08 2016-08-10 董超超 Novel high-strength corrosion-resistant electrical connector element
CN105838948A (en) * 2016-04-08 2016-08-10 董超超 Novel high-strength corrosion-resistant electric vehicle shell
CN105861895A (en) * 2016-04-08 2016-08-17 董超超 Novel high-strength corrosion-resistant building curtain wall framework
CN105734370A (en) * 2016-04-08 2016-07-06 董超超 Novel high-strength corrosion-resistant data recorder
CN105714167A (en) * 2016-04-08 2016-06-29 董超超 Novel high-strength and corrosion-resisting outer wall insulating decorative plate
CN106399781A (en) * 2016-12-05 2017-02-15 合肥工业大学 Novel high-strength corrosion-resistant rare earth aluminum alloy material and preparation method
CN106399781B (en) * 2016-12-05 2018-03-16 合肥工业大学 A kind of high-strength corrosion-resisting rare earth aluminum alloy material and preparation method
CN107022726A (en) * 2017-04-28 2017-08-08 重庆市科学技术研究院 A kind of method for refining the almag as-cast grain containing Er
CN107587013A (en) * 2017-07-28 2018-01-16 宁波华源精特金属制品有限公司 A kind of right end socket
CN112941347A (en) * 2021-01-27 2021-06-11 北京工业大学 Al-Mg-Si-Cu-Er alloy for low-sensitivity aging process and preparation process
CN115198151A (en) * 2022-07-21 2022-10-18 栋梁铝业有限公司 Aluminum alloy for automobile and preparation method thereof
CN115198151B (en) * 2022-07-21 2023-08-18 栋梁铝业有限公司 Aluminum alloy for automobiles and preparation method thereof

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