CN103993208B - A kind of Al-Mg-Si-Cu-Mn-Er alloy material and preparation method thereof - Google Patents

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

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CN103993208B
CN103993208B CN201410234860.1A CN201410234860A CN103993208B CN 103993208 B CN103993208 B CN 103993208B CN 201410234860 A CN201410234860 A CN 201410234860A CN 103993208 B CN103993208 B CN 103993208B
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alloy
master alloy
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cold rolling
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CN103993208A (en
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陈文琳
吴跃
高妍
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合肥工业大学
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Abstract

The invention discloses a kind of Al-Mg-Si-Cu-Mn-Er alloy material and preparation method thereof, it is characterized in that: in Al-Mg-Si-Cu-Mn alloy material, contain mass percent is the rare earth Er of 0.15%-0.45%.Key of the present invention is to add 0.15%-0.45% rare earth element er in Al-Mg-Si-Cu-Mn alloy, other alloying element contents of appropriate design, and adopt reasonable melting technology and flash set technology, and carry out repeat-rolling and suitable thermal treatment, prepare the Al-Mg-Si-Cu-Mn-Er alloy material that microstructure is evenly tiny; And the material obtained has higher plasticity and intensity, its tensile strength is not less than 388MPa, and unit elongation is 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, and have good solidity to corrosion, be widely used in the field such as aerospace, communications and transportation, be most widely used alloy in light metal, its usage quantity is only second to iron and steel.In fields such as aerospace, ocean, transports, adopting aluminium alloy to replace iron and steel, is a kind of effective ways reducing energy consumption.6xxx line aluminium alloy (Al-Mg-Si alloy) density is little, welding property and corrosion stability is excellent, impelling strength is high and be easy to machine-shaping, is the study hotspot of Materials science worker always.

New millennium, along with the continuous progress of science and technology, in order to adapt to the requirement of each field for the material more aspect over-all properties such as high strength, toughness, antifatigue further, aluminium alloy is needed to have higher over-all properties.But traditional Al-Mg-Si alloy intensity is not high, and plasticity is also to be improved.Now there are some researches show, microalloying of rare earth improves 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 can significantly refined cast structure, raising alloy strength, alloy generation recrystal grain effectively can also be suppressed to grow up, put forward heavy alloyed recrystallization temperature.Meanwhile, Er price comparison is cheap, and in aluminium alloy, add rare earth Er can not increase substantially production cost, is therefore highly suitable in industry and promotes the use of.Al-Mg-Si alloy is a kind of typical commercial aluminum alloy, studies to develop a series of novel rare-earth aluminium alloy containing Er, and is widely used in the numerous areas such as Aeronautics and Astronautics, communications and transportation, have important theory and practice meaning to it.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 intensity and the plasticity of Al-Mg-Si alloy can be improved, meet the demand of the field such as Aeronautics and Astronautics, traffic to high-performance aluminium alloy better.

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 mass percent is the rare earth Er of 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 improving the over-all properties such as the strength of materials and plasticity.Wherein, in Al-Mg-Si-Cu-Mn-Er alloy material, Mg and Si massfraction, than when being 1.73:1, can make alloy after solid solution aging, separate out the Mg of a large amount of disperse in matrix 2si strengthening phase, in the present invention, some is superfluous for Si, can in and the detrimentally affect of Fe etc. in impurity, the Mg of refinement simultaneously 2si particle.Add the Cu of 0.65%-0.72% in alloy, object improves the plasticity of alloy when hot-work, strengthens heat treatment reinforcement effect, improves unit elongation.Add the Mn of 0.18%-0.21% in alloy, object stops the recrystallize of alloy in deformation after unloading process by forming disperse phase, thus improve recrystallization temperature, refinement recrystal grain, improves forming property and the intensity of 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 to be grown 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 metal A l, Al-Mn master alloy, Al-Si master alloy and Al-Cu master alloy to be joined in the crucible being preheated to 280 DEG C as raw material group A that (object of crucible preheating removes moisture, prevent cracking), be heated to 730 DEG C, when constant temperature stays to raw material group A is softening, insulating covering agent (insulating covering agent is oxidized for preventing raw material group A to contact with air, simultaneously also in order to reduce the oxide film of incoming stock group of A) is sprinkled on raw material group A surface; When continuation constant temperature melts completely to raw material group A, obtain melt B;

The quality optimization sprinkling insulating covering agent on raw material group A surface is 0.5% of batching total mass.(0.5% is optimum value, and experiment proves all can realize in the interval of 0.5%-0.6%)

1c, add Al-Mg master alloy: (690 DEG C is optimum value to be cooled to 690 DEG C, experiment proves all can to realize in the interval of 680 DEG C-700 DEG C), 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, aluminium foil can be used to wrap up and to be pressed into bottom melt B by Al-Mg master alloy rapidly, then with insulating covering agent, melt B is covered, reducing 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 aluminium foil is wrapped, and rapidly Al-Er master alloy is pressed into bottom melt C), sprinkle insulating covering agent, constant temperature melts completely to Al-Er master alloy, obtains melt D;

1e, refining: be cooled to 720 DEG C, add refining agent C in melt D 2cl 6, by C 2cl 6being immersed in emerging without yellow gas in melt D, leaving 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, and experiment proves all can realize in the interval of 0.5%-0.6%) of batching total mass;

1f, cast: the casting mould of use brass material completes the cast to melt D, obtains alloy cast ingot; Adopt the cooling rate of copper casting mould fast, can pass into cold water to improve speed of cooling further when pouring into a mould, casting process wants quick and stable, and rapid solidification can crystal grain thinning, thus improves the performance such as alloy strength and plasticity.

Step 2: Homogenization Treatments is carried out successively to described alloy cast ingot, viscous deformation obtains Al-Mg-Si-Cu-Mn-Er sheet alloy, and then described Al-Mg-Si-Cu-Mn-Er sheet alloy is heat-treated, obtain Al-Mg-Si-Cu-Mn-Er alloy material.

Described Homogenization Treatments is that step 1 gained alloy cast ingot is heated to 550 DEG C and is incubated 11h, and then air cooling is to room temperature.

Described viscous deformation be by Homogenization Treatments after alloy cast ingot under 465 DEG C of conditions, be incubated 30min, then multistage hot deformation is carried out, under 465 DEG C of conditions, 5min is incubated after every time hot rolling, carry out lower a time hot rolling again, 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 terminates, anneal, annealing conditions is: at 415 DEG C, be incubated 2h, and then air cooling is to room temperature; After annealing terminates, then it is cold rolling to carry out multi-pass, and obtain Al-Mg-Si-Cu-Mn-Er sheet alloy, every time working modulus cold rolling 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 defect such as alloy cast ingot internal porosity and shrinkage porosite, on microcosmic, make particle size distribution simultaneously evenly, and reduce the internal stress of alloy cast ingot because of the uneven generation of speed of cooling.If cold rolling altogether n passage, when n is even number, then complete n/2 passage cold rolling after once anneal, and then it is cold rolling to continue lower a time; When n is odd number, then complete (n+1)/2 passage cold rolling after once anneal, 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.Cold rolling carry out half passage after, the object of carrying out annealing prevents the cold rolling accumulation strain of multi-pass excessive, causes work hardening phenomenon serious, bring difficulty to follow-up cold rolling processing.

Described thermal treatment is that the Al-Mg-Si-Cu-Mn-Er sheet alloy obtained after viscous deformation is carried out 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, sheet alloy after acquisition 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, and insulation 8h, then air cooling is to room temperature, obtains Al-Mg-Si-Cu-Mn-Er alloy material.

Preferably, skim after step 1b completes, and then carry out step 1c;

First skim after step 1c completes, and then carry out step 1d;

First skim after step 1d completes, and then carry out step 1e;

First skim after step 1e completes, 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 the Al-Mg-Si-Cu-Mn-Er alloy material that microstructure is evenly tiny, and gained alloy material has higher intensity and plasticity;

2, the present invention is by rational rolling technology, realizes large plastometric set, effectively eliminates the defect such as inside ingot pore and shrinkage porosite, on microcosmic, make particle size distribution simultaneously evenly, thus put forward heavy alloyed over-all properties;

3, reasonable offer process of the present invention and heat treatment mode are simply, and production cost is not high, easily realizes suitability for industrialized production.

Accompanying drawing explanation

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 the change curve of tensile property with Er content of alloy.

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 prepares 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 prepare burden, batching total mass is 1300g;

1b, fusing: first metal 1142.5gAl, 25gAl-Mn master alloy, 71.4gAl-Si master alloy and 18.2gAl-Cu master alloy are joined in the crucible being 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 aluminium foil is wrapped, and rapidly Al-Er master alloy is pressed into bottom melt C), sprinkle 6.5 insulating covering agents, constant temperature melts completely to 19.7gAl-9.92%Er master alloy, skims, and obtains melt D;

1e, refining: be cooled to 720 DEG C, add 6.5gC in melt D 2cl 6, by C 2cl 6being immersed in emerging without yellow gas in melt D, then leaving standstill insulation 20min; Then skim;

1f, cast: the casting mould of use brass material completes the cast to melt D, obtains the Al-Mg-Si-Cu-Mn-0.15Er alloy cast ingot that 10mm is thick.

Step 2: alloy ingot casting carries out Homogenization Treatments, Homogenization Treatments condition is: homogenization temperature 550 DEG C, soaking time 11h, air cooling is to room temperature.

Step 3: viscous deformation

By the alloy cast ingot scale removal after Homogenization Treatments and milling face, control final thickness is 8mm, under 465 DEG C of conditions, be 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 the alloy cast ingot scale removal after Homogenization Treatments and milling face, control final thickness is 8mm, 30min is incubated under 465 DEG C of conditions, then on two roller hot rollss, hot rolling is carried out, heating (being incubated 5min under 465 DEG C of conditions) is first melted down after every time hot rolling, carry out lower a time hot rolling again, 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 5 passage hot rollings altogether, hot rolling general working rate is 62.5%, and after hot rolling, alloy cast ingot thickness is 3mm; Anneal after hot rolling, the condition of annealing is: be warming up to 415 DEG C, insulation 2h, and air cooling is to room temperature; Cold rolling again after annealing, as shown in Figure 1, every time working modulus cold rolling is followed successively by 10%, 11.1%, 12.5%, 14.3%, 16.7%, 20% and 16.7%, and it is cold rolling to carry out 7 passages altogether, and cold rolling general working rate is 66.7%, and cold rolling rear alloy cast ingot thickness is 1mm; Cold rolling carry out 4 passages after once anneal, and then it is cold rolling to carry out the 5th passage, and annealing conditions is: be warming up to 415 DEG C, insulation 2h, and 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: Al-Mg-Si-Cu-Mn-0.15Er sheet alloy step 3 obtained is heated to 555 DEG C, insulation 45min, then shrend (namely transfer in water and cool) is to room temperature, and quenching shift time (transferring to the time water after namely completing heating from process furnace) is not more than 25s;

4b, ageing treatment: be warming up to 175 DEG C, insulation 8h, then air cooling is 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, carry out tensile test at room temperature to it, concrete steps are: after cold rolling, and 1mm sheet alloy is made standard tensile specimen according to GB GB6397-86, and then carry out step 4, obtain alloy sample.The miniature control electronic universal tester of SANS-100kN is tested the mechanical property of gained alloy sample, and draw speed is 1mm/min; Replication 3 alloy samples 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 prepares Al-Mg-Si-Cu-Mn-0.3Er alloy material by the step identical with embodiment 1, difference is the mass percent according to 97.3%Al, 0.9%Mg, 0.6%Si, 0.7%Cu, 0.2%Mn and 0.3%Er in step 1a, 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 prepare burden, batching total mass is 1300g;

The method identical by embodiment 1 carries out tensile test at room temperature to Al-Mg-Si-Cu-Mn-0.3Er alloy material, gained mechanical performance index: tensile strength is 402MPa, and yield strength is 378MPa, and unit elongation is 26.27%, refers to table 1.

Embodiment 3

The present embodiment prepares Al-Mg-Si-Cu-Mn-0.45Er alloy material by the step identical with embodiment 1, difference is the mass percent according to 97.15%Al, 0.9%Mg, 0.6%Si, 0.7%Cu, 0.2%Mn and 0.45%Er in step 1a, 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 prepare burden, batching total mass is 1300g;

The method identical by embodiment 1 carries out tensile test at room temperature to Al-Mg-Si-Cu-Mn-0.45Er alloy material, gained mechanical performance index: tensile strength is 394MPa, and yield strength is 369MPa, and unit elongation is 24.48%, refers to table 1.

Comparative example

For contrast rare earth Er is on the impact of Al-Mg-Si-Cu-Mn alloy property, Al-Mg-Si-Cu-Mn-0Er alloy material is prepared 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 do not carry out step 1d add Al-Er master alloy.The method identical by embodiment 1 carries out tensile test at room temperature to Al-Mg-Si-Cu-Mn-0Er alloy material, and gained mechanical performance index is: tensile strength is 363MPa, and yield strength is 318MPa, and unit elongation is 19.7%, refers to table 1.

In embodiments after alloy cast ingot preparation (after namely step 1 completes), in order to determine whether the alloying constituent of alloy cast ingot meets the demands, LEEMANSPEC-E type inductively coupled plasma atomic emission spectrometer is adopted to carry out composition detection to all alloy cast ingots, test result, in table 1, illustrates the Al-Mg-Si-Cu-Er alloy cast ingot that melting technology that the present invention adopts can be prepared composition and meets design requirement.

Get alloy cast ingot sample (namely step 1 complete after sample), 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, in Al-Mg-Si-Cu-Mn alloy, add rare earth Er can remarkable refined cast structure, and when adding 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 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%) by a relatively large margin.When 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, when Er content is 0.3%, intensity reaches maximum value, and plasticity is also close to maximum value, namely the tensile strength of 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 strengthening effect of Al-Mg-Si-Cu-Mn alloy mainly from the refinement of Er to as-cast structure, and suppresses alloy generation recrystal grain to be grown up due to the interpolation of Er, is formed and enriches substructure tissue, thus realizes substructure and strengthen.

The chemical composition of table 1 alloy and mechanical performance index

Claims (4)

1. a preparation method for Al-Mg-Si-Cu-Mn-Er alloy material, is characterized in that:
Described Al-Mg-Si-Cu-Mn-Er alloy material be in Al-Mg-Si-Cu-Mn alloy material containing mass percent be the rare earth Er of 0.15%-0.45%; In described Al-Mg-Si-Cu-Mn-Er alloy material, each alloying element by the proportioning of mass percent is:
The preparation method of described Al-Mg-Si-Cu-Mn-Er alloy material carries 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 being 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 melts completely to Al-Er master alloy, obtain melt D;
1e, refining: be cooled to 720 DEG C, add refining agent C in melt D 2cl 6, by C 2cl 6being immersed in emerging without yellow gas in melt D, then leaving standstill insulation 20min; Add C 2cl 6quality be batching total mass 0.5%;
1f, cast: the casting mould of use brass material completes the cast to melt D, obtains alloy cast ingot;
Step 2: Homogenization Treatments is carried out successively to described alloy cast ingot, viscous deformation obtains Al-Mg-Si-Cu-Mn-Er sheet alloy, and then described Al-Mg-Si-Cu-Mn-Er sheet alloy is heat-treated, obtain Al-Mg-Si-Cu-Mn-Er alloy material;
Described viscous deformation be by Homogenization Treatments after alloy cast ingot under 465 DEG C of conditions, be incubated 30min, then multistage hot deformation is carried out, under 465 DEG C of conditions, 5min is incubated after every time hot rolling, carry out lower a time hot rolling again, 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 terminates, anneal, annealing conditions is: under 415 DEG C of conditions, be incubated 2h, and then air cooling is to room temperature;
After annealing terminates, then it is cold rolling to carry out multi-pass, and obtain Al-Mg-Si-Cu-Mn-Er sheet alloy, every time working modulus cold rolling is 10%-20%, and cold rolling general working rate is 60%-70%.
2. preparation method according to claim 1, is characterized in that:
Described Homogenization Treatments is that step 1 gained alloy cast ingot is heated to 550 DEG C and is incubated 11h, and then air cooling is to room temperature.
3. preparation method according to claim 1, is characterized in that: described thermal treatment is that the Al-Mg-Si-Cu-Mn-Er sheet alloy obtained after viscous deformation is carried out 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, sheet alloy after acquisition 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, and insulation 8h, then air cooling is to room temperature, obtains Al-Mg-Si-Cu-Mn-Er alloy material.
4. preparation method according to claim 1, is characterized in that: establish cold rolling altogether n passage, when n is even number, then complete n/2 passage cold rolling after once anneal, and then it is cold rolling to continue lower a time; When n is odd number, then complete (n+1)/2 passage cold rolling after once anneal, 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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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
CN107022726B (en) * 2017-04-28 2019-03-12 重庆市科学技术研究院 A method of almag as-cast grain of the refinement 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

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04160131A (en) * 1990-10-23 1992-06-03 Kobe Steel Ltd Al-mg-si alloy plate excellent in strength and formability, and its manufacture
US5507888A (en) * 1993-03-18 1996-04-16 Aluminum Company Of America Bicycle frames and aluminum alloy tubing therefor and methods for their production
JPH11189837A (en) * 1997-12-25 1999-07-13 Aisin Keikinzoku Co Ltd Free cutting aluminum alloy
JP2000054049A (en) * 1998-08-07 2000-02-22 Mitsubishi Alum Co Ltd Aluminum-magnesium-silicon alloy extruded shape material for side member excellent in collapse characteristic and its production
CN101245429A (en) * 2008-03-21 2008-08-20 北京工业大学 Al-Mg-Si-Mn alloy with Er added
CN102061410A (en) * 2011-01-25 2011-05-18 沈阳工业大学 Al-Mg-Si alloy sheet and manufacturing method thereof
CN102732760A (en) * 2012-07-19 2012-10-17 湖南大学 Aluminum alloy plate for automobile bodies
CN103484728A (en) * 2013-08-26 2014-01-01 天津金轮自行车集团有限公司 Aluminum alloy for bicycle frame tube and preparation method thereof

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04160131A (en) * 1990-10-23 1992-06-03 Kobe Steel Ltd Al-mg-si alloy plate excellent in strength and formability, and its manufacture
US5507888A (en) * 1993-03-18 1996-04-16 Aluminum Company Of America Bicycle frames and aluminum alloy tubing therefor and methods for their production
JPH11189837A (en) * 1997-12-25 1999-07-13 Aisin Keikinzoku Co Ltd Free cutting aluminum alloy
JP2000054049A (en) * 1998-08-07 2000-02-22 Mitsubishi Alum Co Ltd Aluminum-magnesium-silicon alloy extruded shape material for side member excellent in collapse characteristic and its production
CN101245429A (en) * 2008-03-21 2008-08-20 北京工业大学 Al-Mg-Si-Mn alloy with Er added
CN102061410A (en) * 2011-01-25 2011-05-18 沈阳工业大学 Al-Mg-Si alloy sheet and manufacturing method thereof
CN102732760A (en) * 2012-07-19 2012-10-17 湖南大学 Aluminum alloy plate for automobile bodies
CN103484728A (en) * 2013-08-26 2014-01-01 天津金轮自行车集团有限公司 Aluminum alloy for bicycle frame tube and preparation method thereof

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
Ag和Er对Al-Mg-Si-Cu合金组织性能的影响;刘伟哲;《中国优秀硕士学位论文全文数据库 工程科技Ⅰ辑》;20120615(第06期);第13-14页,表2.1 *

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