CN108220716A - A kind of Al-Mg-Si-Cu-Zr-Er alloys with excellent stamping formabilily and preparation method thereof - Google Patents
A kind of Al-Mg-Si-Cu-Zr-Er alloys with excellent stamping formabilily and preparation method thereof Download PDFInfo
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- 229910001371 Er alloy Inorganic materials 0.000 title claims abstract description 22
- 238000002360 preparation method Methods 0.000 title claims description 9
- 239000000956 alloy Substances 0.000 claims abstract description 145
- 229910052691 Erbium Inorganic materials 0.000 claims abstract description 15
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 14
- 238000005096 rolling process Methods 0.000 claims abstract description 12
- 238000010438 heat treatment Methods 0.000 claims abstract description 10
- 238000005275 alloying Methods 0.000 claims abstract description 7
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 7
- 230000007704 transition Effects 0.000 claims abstract description 7
- 229910045601 alloy Inorganic materials 0.000 claims description 128
- 238000011282 treatment Methods 0.000 claims description 20
- 229910052802 copper Inorganic materials 0.000 claims description 13
- 239000010949 copper Substances 0.000 claims description 13
- 229910052782 aluminium Inorganic materials 0.000 claims description 12
- 229910052710 silicon Inorganic materials 0.000 claims description 12
- 229910052749 magnesium Inorganic materials 0.000 claims description 11
- 229910052748 manganese Inorganic materials 0.000 claims description 11
- 229910052751 metal Inorganic materials 0.000 claims description 11
- 239000002184 metal Substances 0.000 claims description 11
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 11
- 230000032683 aging Effects 0.000 claims description 10
- 238000005097 cold rolling Methods 0.000 claims description 10
- 238000007670 refining Methods 0.000 claims description 10
- 239000000463 material Substances 0.000 claims description 9
- 239000000243 solution Substances 0.000 claims description 9
- 238000000265 homogenisation Methods 0.000 claims description 8
- 238000005098 hot rolling Methods 0.000 claims description 8
- 238000004321 preservation Methods 0.000 claims description 7
- 239000006104 solid solution Substances 0.000 claims description 7
- 239000003795 chemical substances by application Substances 0.000 claims description 6
- 238000010791 quenching Methods 0.000 claims description 6
- 230000000171 quenching effect Effects 0.000 claims description 6
- 229910018134 Al-Mg Inorganic materials 0.000 claims description 5
- 229910018131 Al-Mn Inorganic materials 0.000 claims description 5
- 229910018182 Al—Cu Inorganic materials 0.000 claims description 5
- 229910018467 Al—Mg Inorganic materials 0.000 claims description 5
- 229910018461 Al—Mn Inorganic materials 0.000 claims description 5
- 229910018580 Al—Zr Inorganic materials 0.000 claims description 5
- 238000013019 agitation Methods 0.000 claims description 5
- 229910018125 Al-Si Inorganic materials 0.000 claims description 4
- 229910018520 Al—Si Inorganic materials 0.000 claims description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 3
- 238000001035 drying Methods 0.000 claims description 3
- VHHHONWQHHHLTI-UHFFFAOYSA-N hexachloroethane Chemical compound ClC(Cl)(Cl)C(Cl)(Cl)Cl VHHHONWQHHHLTI-UHFFFAOYSA-N 0.000 claims description 3
- 230000001535 kindling effect Effects 0.000 claims description 3
- 238000003801 milling Methods 0.000 claims description 3
- 238000003756 stirring Methods 0.000 claims description 3
- 238000000137 annealing Methods 0.000 claims description 2
- 238000000034 method Methods 0.000 abstract description 9
- 150000001875 compounds Chemical class 0.000 abstract description 6
- 238000005516 engineering process Methods 0.000 abstract description 6
- 239000013078 crystal Substances 0.000 abstract description 5
- 238000003723 Smelting Methods 0.000 abstract description 3
- 238000013461 design Methods 0.000 abstract description 3
- 230000008569 process Effects 0.000 abstract description 3
- 229910000881 Cu alloy Inorganic materials 0.000 abstract 1
- 229910018594 Si-Cu Inorganic materials 0.000 description 12
- 229910008465 Si—Cu Inorganic materials 0.000 description 12
- 229910000838 Al alloy Inorganic materials 0.000 description 10
- 238000002474 experimental method Methods 0.000 description 10
- 238000012360 testing method Methods 0.000 description 9
- 238000011160 research Methods 0.000 description 6
- 238000001953 recrystallisation Methods 0.000 description 3
- 230000008901 benefit Effects 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 2
- 239000010931 gold Substances 0.000 description 2
- 229910052737 gold Inorganic materials 0.000 description 2
- 239000000314 lubricant Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 1
- 229910019752 Mg2Si Inorganic materials 0.000 description 1
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000001174 ascending effect Effects 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
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- 239000000047 product Substances 0.000 description 1
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- 239000002994 raw material Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000003252 repetitive effect Effects 0.000 description 1
- 230000010076 replication Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
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- 235000015112 vegetable and seed oil Nutrition 0.000 description 1
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- 230000037303 wrinkles Effects 0.000 description 1
Classifications
-
- 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
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- 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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
-
- 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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- 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
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
-
- 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
- C22F1/047—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 magnesium as the next major constituent
Abstract
The invention discloses a kind of Al Mg Si Cu Zr Er alloys with excellent stamping formabilily, the rare earth element er containing mass percent for 0.14% 0.18% transition element Zr and 0.28%~0.32%.The present invention passes through addition Zr, Er element compound into Al Mg Si Cu alloys, rationally design other alloying element contents, and using reasonable smelting technology, flash set technology, and repeat-rolling and suitable heat treatment are carried out, prepare the Al Mg Si Cu Zr Er alloy materials that microscopic structure is uniform, crystal grain is tiny；The alloy material that the present invention is obtained has preferable forming property, elongation percentage δ >=24%, limit drawing coefficient≤0.53；And present invention process process is simple, of low cost, comprehensive performance is superior.
Description
Technical field
The invention belongs to non-ferrous metal technical fields, and in particular to a kind of Al-Mg-Si-Cu-Zr-Er alloys and its preparation
Method.
Background technology
At present, research of the aluminium alloy in auto industry and application are concerned, in energy saving, emission reduction, safe and environment-friendly, easypro
Suitable aspect has significant advantage, and parts of the vehicle body as automobile maximum, weight is about the 30% of automobile total weight, to vehicle
Lightweight is of great significance.Al-Mg-Si-Cu systems alloy has excellent comprehensive as heat-treatable strengthened type aluminium alloy
Can, biggest advantage is that T4 supply of material state (solution hardening+natrual ageing) lower yield strengths are relatively low, is suitble to punch forming,
And after coating baking is carried out, intensity can improve, and sag resistant ability is enhanced, so Al-Mg-Si-Cu systems alloy exists
It is most widely used on body of a motor car.But the forming property of Al-Mg-Si-Cu systems sheet alloy is also unable to reach the level of steel plate,
There is the problem of very big in forming property, easily generate wrinkle, crackle, this is one of Alloyapplication main barrier as this is limited
Hinder, therefore the forming property for how significantly improving Al-Mg-Si-Cu systems alloy becomes one of research hotspot and the difficult point in the field.
People have found through a large number of experiments, can influence alloy by adding the elements such as micro transition group and rare earth
Pick-up behavior, and then the comprehensive performance of aluminium alloy can be significantly improved.Zr is a kind of transition elements, has the work of heterogeneous nuclei
With, be Aluminium Alloys in Common Use ingot casting best alterant, it has also become one of micro alloying element necessary to development high-performance aluminium alloy.
Application of the rare earth element er in aluminium industry shows good prospect with development, this possesses very huge derived from it in the earth's crust
Deposit, microalloying of the Er elements in aluminium alloy study to obtain a large amount of concerns of scientific research personnel.The study found that compound addition
Two or more micro alloying element can preferably play the effect of micro alloying element, and can reduce valuable gold
Belong to the usage amount of element, so as to reduce cost.Have largely in the Al-Mg-Si-Cu researchs for individually adding Zr, Er element at present
Report, and combined microalloying due between each element the mechanism of action it is more complicated, thus it is existing it is a small amount of research be also all
It qualitatively studies, and the relationship between the quantitative element of systematic research and the performance of material is rarely reported.
Invention content
The purpose of the present invention is to provide a kind of novel Al-Mg-Si-Cu-Zr-Er alloys, to which Al- can be improved
The forming property and mechanical property of Mg-Si-Cu systems alloy better meet need of the fields such as auto industry to high-performance aluminium alloy
It asks.
The purpose of the present invention is achieved through the following technical solutions：
The present invention has the Al-Mg-Si-Cu-Zr-Er alloys of excellent stamping formabilily, and feature is：Described
In Al-Mg-Si-Cu-Zr-Er alloys containing mass percent be 0.14%-0.18% transition element Zr and 0.28%~
0.32% rare earth element er.Zr and Er elements are by forming Al3Zr、Al3Er、AL3(Zr, Er) particle refinement crystal grain, it is strong to follow closely
Dislocation and sub boundary are pricked, inhibits the recrystallization of alloy, so as to obtain the Al-Mg-Si-Cu-Zr-Er alloys of function admirable.
Specifically, in the Al-Mg-Si-Cu-Zr-Er alloys, the proportioning of each alloying element by weight percent is：
Microalloying is to improve one of aluminium alloy capability means mostly important with novel aluminum alloy is developed.Wherein, in Al-
In Mg-Si-Cu-Zr-Er alloy materials, Mg and Si mass fractions ratio is less than 1.73, and alloy is precipitated after solid solution aging in matrix
Disperse Mg2Si hardening constituents, in the present invention, the excess silicon of volume, supplement when main function is artificial aging are strengthened, and are conducive to
Precipitation strength enhances tensile strength, meanwhile, the addition of Si can eliminate adverse effects of the Fe to aluminium alloy capability.Add in alloy
Enter 0.28%~0.31% Cu, it is therefore an objective to improve plasticity of the alloy in hot-working, improve the ductility of alloy.Add in alloy
Enter 0.14~0.16% Mn, it is therefore an objective to improve recrystallization temperature, refine recrystal grain, improve the forming property of alloy and strong
Degree.Rare earth Er and 0.14%~0.18% transition group that compound addition mass fraction is 0.28%~0.32% in alloy simultaneously
Element Zr, it is therefore an objective to significantly refine as-cast grain, improve alloy punching forming property, and improve the recrystallization temperature of alloy.
The preparation method of Al-Mg-Si-Cu-Zr-Er alloys of the present invention, includes the following steps：
Step 1：Prepare alloy cast ingot
1a, dispensing：According to the mass percent of Al, Mg, Si, Cu, Mn, Zr, Er, weigh and closed among metal Al, Al-Mg
Gold, Al-Si intermediate alloys, Al-Cu intermediate alloys, Al-Mn intermediate alloys, Al-Zr intermediate alloys and Al-Er intermediate alloys,
As raw material；
1b, fusing：Setting furnace temperature is 300 DEG C first, is added in metal Al in crucible after crucible drying, kindling temperature is extremely
800 DEG C, constant temperature to Al melts, and is then cooled to 780 DEG C, stirs and keep the temperature 10min；
1c, Al-Si intermediate alloys, Al-Cu intermediate alloys, Al-Mn intermediate alloys, Al-Zr intermediate alloys and Al- are added in
Er intermediate alloys, after to be melted, gentle agitation simultaneously continues to keep the temperature 10min, obtains melt；
1d, refining：Furnace temperature is adjusted to add in refining agent C in melt to 750 DEG C2Cl6, by C2Cl6It is immersed in melt to nothing
Gas is emerged, and is skimmed after standing heat preservation 10min；Add in C2Cl6Quality be dispensing gross mass 3%；
1e, Al-Mg intermediate alloys are added in, is steadily pressed into melt bottom and is covered with coverture, treat its fusing
It gentle agitation and skims after keeping the temperature 10min afterwards；
1f, refining agent C is added in again in melt2Cl6, by C2Cl6It is immersed in melt to no gas and emerges, stand and protect
It skims after warm 10min, adds in C2Cl6Quality be dispensing gross mass 3%；Then 710 DEG C are cooled to, stands heat preservation 10min,
It is poured into a mould using water cooled copper mould, obtains alloy cast ingot；
Step 2：After carrying out Homogenization Treatments, rolling deformation, heat treatment successively to the alloy cast ingot, i.e., described in acquisition
Al-Mg-Si-Cu-Zr-Er alloys.
Wherein：
The Homogenization Treatments are that step 1 gained alloy cast ingot is heated to 555 DEG C and keeps the temperature 10h, are then air-cooled to room
Temperature, scale removal and milling face.
The rolling deformation is that the 8mm thickness alloy cast ingot after Homogenization Treatments first is kept the temperature 30min under the conditions of 430 DEG C,
Then multistage hot deformation is carried out, obtains the plank of 4mm thickness, hot rolling total deformation is 50%；It anneals again；It finally carries out again more
Passage cold rolling, cold rolling total deformation are 75%, obtain the sheet alloy of 1mm thickness；The condition of the annealing is：Under the conditions of 430 DEG C
30min is kept the temperature, is subsequently cooled to room temperature.
The heat treatment is that the sheet alloy that will be obtained after rolling deformation carries out solution treatment and natrual ageing successively
Processing；The solution treatment is that sheet alloy is heated to 565 DEG C, keeps the temperature 30min, and then water quenching to room temperature obtains solid solution state
Sheet alloy, quenching shift time are not higher than 30 DEG C no more than 25s, water temperature；The natural aging treatment is will to be dissolved state alloy
Plank is in being placed at room temperature for one week target product Al-Mg-Si-Cu-Zr-Er sheet alloy to get T4 states.
Compared with the prior art, beneficial effects of the present invention are embodied in：
1st, the present invention is by combined microalloying, rationally designs other constituent contents, and using reasonable smelting technology and
Flash set technology prepares the Al-Mg-Si-Cu-Zr-Er alloy materials that microscopic structure is uniform, crystal grain is tiny, and gained material
Material has preferable stamping formabilily and room-temperature mechanical property；
2nd, the present invention is by rational rolling mill practice, the defects of effectively eliminating inside ingot stomata and shrinkage porosite, it is microcosmic on make
Particle size distribution evenly, macroscopically improves the comprehensive performance of alloy；
3rd, alloy preparation process of the present invention and heat treatment mode are simple, and production cost is not high, easily realizes industrialized production.
Description of the drawings
Fig. 1 is drawing experiment mould schematic diagram；
Fig. 2 is the as-cast metallographic structure of alloy cast ingot obtained by each embodiment, and wherein Fig. 2 (a) is cast for Al-Mg-Si-Cu alloys
Ingot tissue, Fig. 2 (b) are Al-Mg-Si-Cu-0.15Zr alloy cast ingot tissues, and Fig. 2 (c) is cast for Al-Mg-Si-Cu-0.3Er alloys
Ingot tissue, Fig. 2 (d) are Al-Mg-Si-Cu-0.15Zr-0.3Er alloy cast ingot tissues；
Fig. 3 is the elongation percentage for the sheet alloy for adding different element species and limit drawing coefficient change curve.
Specific embodiment
Elaborate below in conjunction with the accompanying drawings to the embodiment of the present invention, following embodiments using technical solution of the present invention as
Under the premise of implemented, give detailed embodiment and specific operating process, but protection scope of the present invention is not limited to
Following embodiments.
Embodiment 1
The present embodiment prepares Al-Mg-Si-Cu-0.15Zr alloy materials as follows：
Step 1：Prepare alloy cast ingot
A, dispensing：Dispensing：According to 97.65%Al, 1.1%Mg, 0.65%Si, 0.3%Cu, 0.15%Mn and 0.15%Zr
Mass percent, weigh metal Al, Al-50%Mg intermediate alloy, Al-20%Si intermediate alloys, close among Al-50%Cu
Gold, Al-20%Mn intermediate alloys, Al-10%Zr intermediate alloys carry out dispensing, and dispensing gross mass is 1200g；
1b, fusing：Setting furnace temperature is 300 DEG C first, is added in metal Al in crucible after crucible drying, kindling temperature is extremely
800 DEG C, constant temperature to Al melts, and is then cooled to 780 DEG C, stirs and keep the temperature 10min；
1c, Al-Si intermediate alloys, Al-Cu intermediate alloys, Al-Mn intermediate alloys, Al-Zr intermediate alloys and Al- are added in
Er intermediate alloys, after to be melted, gentle agitation simultaneously continues to keep the temperature 10min, obtains melt；
1d, refining：Furnace temperature is adjusted to add in refining agent C in melt to 750 DEG C2Cl6, by C2Cl6It is immersed in melt to nothing
Gas is emerged, and is skimmed after standing heat preservation 10min；Add in C2Cl6Quality be dispensing gross mass 3%；
1e, Al-Mg intermediate alloys are added in, is steadily pressed into melt bottom and is covered with coverture, treat its fusing
It gentle agitation and skims after keeping the temperature 10min afterwards；
1f, refining agent C is added in again in melt2Cl6, by C2Cl6It is immersed in melt to no gas and emerges, stand and protect
It skims after warm 10min, adds in C2Cl6Quality be dispensing gross mass 3%；Then 710 DEG C are cooled to, stands heat preservation 10min,
It is poured into a mould using water cooled copper mould, obtains alloy cast ingot；
Step 2：Homogenization Treatments
Step 1 gained alloy cast ingot is heated to 555 DEG C and keeps the temperature 10h, is then air-cooled to room temperature, scale removal and milling
Face, control final thickness are 8mm.
Step 3：Rolling deformation
8mm thickness alloy cast ingot after Homogenization Treatments is first kept the temperature into 30min under the conditions of 430 DEG C, then in two roller hot rollings
Hot rolling is carried out on machine, every time working modulus of hot rolling is followed successively by 16.3%, 16.4%, 16.1%, 14.5%, carries out 4 passages heat altogether
It rolls, hot rolling total deformation is 50%, and the plank of 4mm thickness is obtained after hot rolling；Annealed again (30min is kept the temperature under the conditions of 430 DEG C,
It is subsequently cooled to room temperature)；Finally cold rolling is carried out again, every time working modulus of cold rolling is followed successively by 15.0%, 14.7%, 17.2%,
16.7%, 15%, 17.6%, 14.3% and 16.7%, 8 passage cold rollings are carried out altogether, and cold rolling general working rate is 75%, is obtained after cold rolling
Obtain the sheet alloy of 1mm thickness；After 4 passage hot rollings and 8 passage cold rollings, operation of rolling general working rate is 87.5%.
Step 4：Heat treatment
Heat treatment is that the sheet alloy that will be obtained after rolling deformation carries out solution treatment and natural aging treatment successively：
Solution treatment：The sheet alloy that step 3 is obtained is heated to 565 DEG C, keeps the temperature 30min, then water quenching (is shifted
Cooled down into water) to room temperature, solid solution state sheet alloy is obtained, quenching shift time (turns after completing heating from heating furnace
Move on to the time in water) it is not higher than 30 DEG C no more than 25s, water temperature；
Ageing treatment：Will solid solution state sheet alloy in be placed at room temperature for one week to get T4 states Al-Mg-Si-Cu-0.15Zr conjunction
Golden plate material.
To test the mechanical property of Al-Mg-Si-Cu-0.15Zr sheet alloys, room temperature tensile examination is carried out to sheet alloy
It tests, the specific steps are：It is made along alloy sheet feed direction (plate rolling direction), lateral and 45 ° of directions according to national standard GB6397-86
Standard tensile specimen obtains alloy sample.The alloy examination obtained by test on the miniature control electronic universal testers of SANS-100kN
The mechanical property of sample, tensile speed 1mm/min；3 groups of samples of replication are averaged.Gained mechanical performance index：Tension
Intensity σbFor 238Mpa, yield strength σ0.2For 142Mpa, elongation percentage δ be 22.9%, hardenability value n is 0.23, thick anisotropy system
Number r values etc. refer to table 1.
To test Al-Mg-Si-Cu-0.15Zr sheet alloy stamping formabililies, it is real that room temperature drawing is carried out to sheet alloy
It tests, obtains the wall portion under room temperature near alloy material drawing bottom of cup fillet and do not generate the maximum sample for allowing to use during rupture
Diameter Dmax, and calculate limited drawing ratio L.D.R and limit drawing coefficient.The setting of drawing experiment parameter is as follows：
1) experiment is 1mm with sotck thinkness, using vegetable oil as lubricant, is tested using cup drawing.Die size is such as
Shown in Fig. 1, cavity plate and convex mould diameter are respectively 51.6mm, 49.6mm, and cavity plate and punch ratius are 6mm.
2) a diameter of Φ 88, the Al-Mg-Si- of Φ 90, Φ 92, Φ 94, Φ 96, Φ 97, Φ 98, Φ 99, Φ 100 are prepared
Cu-0.15Zr experiment circular blank polyliths.
3) it is 80T open-type inclinable presses to select forcing press.
Drawing experiment the specific steps are：
1) it under the premise of ensuring that press equipment and mold work normally, puts well the blank of different-diameter is ascending
And it numbers.
2) lubricant is smeared on the contact surface of sample and cavity plate.
3) blank center is made to be overlapped with punch-pin center and (two are drawn centered on the center of circle on blank holder and circular blank respectively
The vertical line of item, two crosses overlap, and blank center is overlapped with punch-pin).
4) drawing is carried out with the circle blank of different-diameter successively, until pulling open, repetitive test is done, before record rupture
Blank diameter afterwards.
Drawing experiment gained Al-Mg-Si-Cu-0.15Zr sheet alloy maximum drawing diameters DmaxFor 92mm, Limit Drawing
It is 1.78 than L.D.R, limit drawing coefficient 0.56 refers to table 2.
Embodiment 2
The present embodiment prepares Al-Mg-Si-Cu-0.3Er alloy materials by step same as Example 1, difference lies in：
According to the mass percent of 97.5%Al, 1.1%Mg, 0.65%Si, 0.3%Cu, 0.15%Mn and 0.3%Er in step 1a,
It weighs in metal Al, Al-50%Mg intermediate alloy, Al-20%Si intermediate alloys, Al-50%Cu intermediate alloys, Al-20%Mn
Between alloy and Al-9.92%Er intermediate alloys carry out dispensing, dispensing gross mass is 1200g；
Tensile test at room temperature, resulting force are carried out to Al-Mg-Si-Cu-0.3Er alloy materials by the identical method of embodiment 1
Learn performance indicator：Tensile strength sigmabFor 249Mpa, yield strength σ0.2For 141Mpa, elongation percentage δ be 23.5%, hardenability value n is
0.23, the coefficient of normal anisortopy r values etc. refer to table 1.
Room temperature drawing experiments are carried out to Al-Mg-Si-Cu-0.3Er alloy materials by the identical method of embodiment 1, it is sheets thus obtained
Material maximum drawing diameter DmaxFor 96mm, limited drawing ratio L.D.R is 1.86, and limit drawing coefficient 0.53 refers to table 2.
Embodiment 3
The present embodiment prepares Al-Mg-Si-Cu-0.15Zr-0.3Er alloy materials, area by step same as Example 1
It is not：According to 97.35%Al, 1.1%Mg, 0.65%Si, 0.3%Cu, 0.15%Mn, 0.15Zr and 0.3% in step 1a
The mass percent of Er weighs metal Al, Al-50%Mg intermediate alloy, Al-20%Si intermediate alloys, the conjunction of Al-50%Cu centres
Gold, Al-20%Mn intermediate alloys, Al-10%Zr intermediate alloys and Al-9.92%Er intermediate alloys carry out dispensing, and dispensing is total
Quality is 1200g.
Room temperature tensile examination is carried out to Al-Mg-Si-Cu-0.15Zr-0.3Er alloy materials by the identical method of embodiment 1
It tests, gained mechanical performance index：Tensile strength sigmabFor 260Mpa, yield strength σ0.2It is 25% for 136Mpa, elongation percentage δ, hardening
Index n is 0.24, and the coefficient of normal anisortopy r values etc. refer to table 1.
Room temperature drawing examination is carried out to Al-Mg-Si-Cu-0.15Zr-0.3Er alloy materials by the identical method of embodiment 1
It tests, gained plank maximum drawing diameter DmaxFor 98mm, limited drawing ratio L.D.R is 1.90, limit drawing coefficient 0.52, in detail
It is shown in Table 2.
Comparative example
It is individually added for comparison transition element Zr and rare earth element er and compound addition is to Al-Mg-Si-Cu alloy materials
The influence of performance prepares Al-Mg-Si-Cu-0Zr-0Er alloy materials by mode same as Example 1, differs only in；Step
According to the mass percent of 97.8%Al, 1.1%Mg, 0.65%Si, 0.3%Cu and 0.15%Mn in rapid 1a, weigh metal Al,
Al-50%Mg intermediate alloys, Al-20%Si intermediate alloys, Al-50%Cu intermediate alloys, Al-20%Mn intermediate alloys are matched
Material, dispensing gross mass are 1200g；
Tensile test at room temperature, gained are carried out to Al-Mg-Si-Cu-0Zr-0Er alloy materials by the identical method of embodiment 1
Mechanical performance index：Tensile strength sigmabFor 224Mpa, yield strength σ0.2It is 20.9% for 116Mpa, elongation percentage δ, hardenability value n
It is 0.21, the coefficient of normal anisortopy r values etc. refer to table 1.
Room temperature drawing experiments, gained are carried out to Al-Mg-Si-Cu-0Zr-0Er alloy materials by the identical method of embodiment 1
Plank maximum drawing diameter DmaxFor 90mm, limited drawing ratio L.D.R is 1.74, and limit drawing coefficient 0.57 refers to table 2.
After in embodiments prepared by alloy cast ingot (i.e. after the completion of step 1), in order to determine the alloying component of alloy cast ingot
Whether meet the requirements, composition detection is carried out to all alloy cast ingots using direct-reading spectrometer, test result such as table 3 illustrates this hair
The smelting technology of bright use can prepare the Al-Mg-Si-Cu-Zr-Er alloy cast ingots that ingredient meets design requirement.
Alloy plate T4 state room-temperature mechanical property indexs prepared by 1 present invention of table
Alloy plate T4 state room temperature drawing experiments results prepared by 2 present invention of table
| Specimen coding | Dmax | L.D.R | Limit drawing coefficient |
| Embodiment 1 | Φ92 | 1.78 | 0.56 |
| Embodiment 2 | Φ96 | 1.86 | 0.53 |
| Embodiment 3 | Φ98 | 1.90 | 0.52 |
| Comparative example | Φ91 | 1.74 | 0.57 |
The chemical composition of 3 alloy of table
Alloy cast ingot sample (sample i.e. after the completion of step 1) is taken, in MR5000 type metallography microscope Microscopic observation metallographic groups
It knits, as shown in Figure 2.Fig. 2 (a), (b), (c) and (d) are respectively Al-Mg-Si-Cu-0Zr-0Er alloys, Al-Mg-Si-Cu-
The as-cast metallographic structure of 0.15Zr alloys, Al-Mg-Si-Cu-0.3Er alloys and Al-Mg-Si-Cu-0.15Zr-0.3Er alloys.
As seen from the figure, as-cast grain can significantly be refined by Zr or Er being added in Al-Mg-Si-Cu alloys, as compound addition 0.15%Zr
During with 0.3%Er, the refinement of Al-Mg-Si-Cu As-cast Microstructures is the most apparent.
The mechanical performance index of the alloy material of different addition element is compared, as shown in Table 1, addition Zr or Er can be notable
The intensity and elongation percentage of Al-Mg-Si-Cu alloys are improved, being primarily due to addition Zr or Er can be recrystallized with refining alloy
Tissue, crystal grain refinement can improve intensity and plasticity simultaneously.Different-alloy sheet metal formability index is compared, it can by table 2 and Fig. 3
Know, compound addition 0.15%Zr and 0.3%Er can increase substantially Al-Mg-Si-Cu alloys maximum drawing diameter and the limit is drawn
Deep ratio reduces alloy limit drawing coefficient (the Al-Mg-Si-Cu-Zr-Er alloy a diameter of 98mm of maximum drawing, limited drawing ratio
It is 1.90, limit drawing coefficient 0.52), significantly improve Alloy Forming performance.This is because through solid solution and natural aging treatment
Afterwards, Al-Mg-Si-Cu-0.15Zr-0.3Er alloy structures are uniform, crystal grain is tiny, and intensity index is high, and n values, r values, elongation are big,
Its yield tensile ratio is relatively low, thus forming property is good.
It these are only exemplary embodiment of the present invention, be not intended to limit the invention, all spirit in the present invention
With all any modification, equivalent and improvement made within principle etc., should all be included in the protection scope of the present invention.
Claims (6)
1. a kind of Al-Mg-Si-Cu-Zr-Er alloys with excellent stamping formabilily, it is characterised in that：In the Al-Mg-
Contain the transition element Zr and 0.28%~0.32% that mass percent is 0.14%-0.18% in Si-Cu-Zr-Er alloys
Rare earth element er.
2. Al-Mg-Si-Cu-Zr-Er alloys according to claim 1, it is characterised in that：The Al-Mg-Si-Cu-Zr-
In Er alloys, the proportioning of each alloying element by weight percent is：
3. a kind of preparation method of the Al-Mg-Si-Cu-Zr-Er alloys described in claims 1 or 2, which is characterized in that including with
Lower step：
Step 1：Prepare alloy cast ingot
1a, dispensing：According to the mass percent of Al, Mg, Si, Cu, Mn, Zr, Er, metal Al, Al-Mg intermediate alloy, Al- are weighed
Si intermediate alloys, Al-Cu intermediate alloys, Al-Mn intermediate alloys, Al-Zr intermediate alloys and Al-Er intermediate alloys, as original
Material；
1b, fusing：First setting furnace temperature be 300 DEG C, after crucible drying after by metal Al add in crucible in, kindling temperature to 800 DEG C,
Constant temperature is melted to Al, is then cooled to 780 DEG C, is stirred and keep the temperature 10min；
1c, it adds in Al-Si intermediate alloys, Al-Cu intermediate alloys, Al-Mn intermediate alloys, Al-Zr intermediate alloys and Al-Er
Between alloy, after to be melted, gentle agitation simultaneously continue keep the temperature 10min, obtain melt；
1d, refining：Furnace temperature is adjusted to add in refining agent C in melt to 750 DEG C2Cl6, by C2Cl6It is immersed in melt to no gas and emits
Go out, skim after standing heat preservation 10min；Add in C2Cl6Quality be dispensing gross mass 3%；
1e, Al-Mg intermediate alloys are added in, is steadily pressed into melt bottom and is covered with coverture, it is light after its fusing
It is micro- to stir and skim after keeping the temperature 10min；
1f, refining agent C is added in again in melt2Cl6, by C2Cl6It is immersed in melt to no gas and emerges, stand heat preservation
It skims after 10min, adds in C2Cl6Quality be dispensing gross mass 3%；Then 710 DEG C are cooled to, heat preservation 10min is stood, makes
It is poured into a mould with water cooled copper mould, obtains alloy cast ingot；
Step 2：After carrying out Homogenization Treatments, rolling deformation, heat treatment successively to the alloy cast ingot, that is, obtain the Al-Mg-
Si-Cu-Zr-Er alloys.
4. preparation method according to claim 3, it is characterised in that：
The Homogenization Treatments are that step 1 gained alloy cast ingot is heated to 555 DEG C and keeps the temperature 10h, are then air-cooled to room temperature, go
Descale simultaneously milling face.
5. preparation method according to claim 3, it is characterised in that：
The rolling deformation is that the 8mm thickness alloy cast ingot after Homogenization Treatments first is kept the temperature 30min under the conditions of 430 DEG C, then
Multistage hot deformation is carried out, obtains the plank of 4mm thickness, hot rolling total deformation is 50%；It anneals again；Finally multi-pass is carried out again
Cold rolling, cold rolling total deformation are 75%, obtain the sheet alloy of 1mm thickness；
The condition of the annealing is：30min is kept the temperature under the conditions of 430 DEG C, is subsequently cooled to room temperature.
6. preparation method according to claim 3, it is characterised in that：The heat treatment is will to be obtained after rolling deformation
Sheet alloy carry out solution treatment and natural aging treatment successively；
The solution treatment is that sheet alloy is heated to 565 DEG C, keeps the temperature 30min, and then water quenching to room temperature obtains solid solution state and closes
Golden plate material, quenching shift time are not higher than 30 DEG C no more than 25s, water temperature；
The natural aging treatment be will solid solution state sheet alloy in being placed at room temperature for one week target product Al-Mg- to get T4 states
Si-Cu-Zr-Er sheet alloys.
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