CN117604295A - Preparation method of medium-strength damage-resistant tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet - Google Patents
Preparation method of medium-strength damage-resistant tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet Download PDFInfo
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 59
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 46
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 46
- 238000002360 preparation method Methods 0.000 title claims abstract description 11
- 238000000137 annealing Methods 0.000 claims abstract description 25
- 238000001914 filtration Methods 0.000 claims abstract description 13
- 238000003466 welding Methods 0.000 claims abstract description 13
- 239000000463 material Substances 0.000 claims abstract description 12
- 238000000034 method Methods 0.000 claims abstract description 12
- 229910018569 Al—Zn—Mg—Cu Inorganic materials 0.000 claims abstract description 11
- 238000003723 Smelting Methods 0.000 claims abstract description 9
- 238000005266 casting Methods 0.000 claims abstract description 9
- 238000007872 degassing Methods 0.000 claims abstract description 9
- 238000003801 milling Methods 0.000 claims abstract description 5
- 238000010008 shearing Methods 0.000 claims abstract description 5
- 238000005303 weighing Methods 0.000 claims abstract description 5
- 238000005097 cold rolling Methods 0.000 claims abstract description 4
- 229910045601 alloy Inorganic materials 0.000 claims description 60
- 239000000956 alloy Substances 0.000 claims description 60
- 239000011572 manganese Substances 0.000 claims description 36
- 239000007789 gas Substances 0.000 claims description 16
- 239000000155 melt Substances 0.000 claims description 16
- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical compound [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 claims description 12
- WPPDFTBPZNZZRP-UHFFFAOYSA-N aluminum copper Chemical compound [Al].[Cu] WPPDFTBPZNZZRP-UHFFFAOYSA-N 0.000 claims description 12
- -1 aluminum manganese Chemical compound 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 12
- 239000011777 magnesium Substances 0.000 claims description 11
- 229910052749 magnesium Inorganic materials 0.000 claims description 11
- 238000004321 preservation Methods 0.000 claims description 9
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 8
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 8
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 8
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 8
- 239000001257 hydrogen Substances 0.000 claims description 8
- 229910052739 hydrogen Inorganic materials 0.000 claims description 8
- 239000002904 solvent Substances 0.000 claims description 8
- 239000010936 titanium Substances 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 5
- ZAMOUSCENKQFHK-UHFFFAOYSA-N Chlorine atom Chemical compound [Cl] ZAMOUSCENKQFHK-UHFFFAOYSA-N 0.000 claims description 4
- 229910052786 argon Inorganic materials 0.000 claims description 4
- 239000000919 ceramic Substances 0.000 claims description 4
- 239000000460 chlorine Substances 0.000 claims description 4
- 229910052801 chlorine Inorganic materials 0.000 claims description 4
- 238000001816 cooling Methods 0.000 claims description 4
- 238000005098 hot rolling Methods 0.000 claims description 4
- 239000011701 zinc Substances 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 238000004519 manufacturing process Methods 0.000 claims 3
- 238000005096 rolling process Methods 0.000 abstract description 3
- 238000010586 diagram Methods 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000001514 detection method Methods 0.000 description 2
- 238000001887 electron backscatter diffraction Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 230000010287 polarization Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
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- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
- B22D1/002—Treatment with gases
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D7/00—Casting ingots, e.g. from ferrous metals
- B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23P—METAL-WORKING NOT OTHERWISE PROVIDED FOR; COMBINED OPERATIONS; UNIVERSAL MACHINE TOOLS
- B23P15/00—Making specific metal objects by operations not covered by a single other subclass or a group in this subclass
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- 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
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- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
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- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
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- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—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 copper as the next major constituent
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Abstract
A method for preparing a medium-strength damage-resistant tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet. It belongs to an aluminum-clad thinThe field of board preparation. The method comprises the following steps: weighing materials; smelting, namely a converter to obtain an aluminum alloy melt; two-stage degassing and two-stage filtering, and casting; homogenizing annealing, milling a surface, sawing, welding a skin material, performing hot finish rolling and cold rolling on the cast ingot; annealing a finished product; roll straightening, shearing or sawing finished products. The intermediate-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet prepared in the invention has K in T42 state app The value can reach 90MPa m 1/2 ～110MPa·m 1/2 The strength Cv value is 1.0% -3.0%, meets the product standard requirements, solves the neck problem of industrial preparation of Al-Zn-Mg-Cu aluminum alloy O-state thin plates, has the characteristics of medium strength and high damage tolerance, and can provide a new material for the fuselage frame, control surface and the like of a large civil aircraft.
Description
Technical Field
The invention belongs to the field of preparation of aluminum clad sheets, and particularly relates to a preparation method of an intermediate-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet.
Background
Al-Cu-Mg-Mn aluminum alloy aluminum clad sheet material for the aviation field is used for the positions of a frame, a control surface and the like of a large civil aircraft. With the development of aerospace field application, higher requirements are put on the performance of the Al-Cu-Mg-Mn aluminum clad sheet. The research of the middle-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet suitable for civil aircraft is almost zero, and related work is less to be carried out according to the design of civil aircraft and the airworthiness requirement, so that the middle-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet meeting the airworthiness requirement of the civil aircraft is urgently needed to be developed, the technical problems of industrialized average fire, rolling and finished product annealing processes and performance and tissue matching of the industrialized Al-Cu-Mg-Mn aluminum alloy aluminum clad sheet are solved, and the product quality of the civil Al-Cu-Mg-Mn aluminum alloy aluminum clad sheet is improved.
Disclosure of Invention
The invention aims to solve the technical problems and provide a preparation method of an intermediate-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet.
A preparation method of a medium-strength damage-resistant tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet comprises the following steps:
1. the weight percentage of elements is as follows: si less than or equal to 0.50%, fe less than or equal to 0.30%, cu:4.3 to 4.9 percent of Mn:0.4 to 1.0 percent of Mg:1.3 to 1.7 percent of Zn:0.1 to 0.15 percent of Ti:0.02 to 0.04 percent, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurity and the balance of Al, and weighing aluminum ingot, magnesium ingot, zinc ingot, aluminum copper intermediate alloy, aluminum manganese intermediate alloy and aluminum titanium intermediate alloy for remelting;
2. adding the aluminum ingot, the magnesium ingot, the zinc ingot, the aluminum copper intermediate alloy, the aluminum manganese intermediate alloy and the aluminum titanium intermediate alloy which are weighed in the first step into a smelting furnace, smelting at 700-760 ℃, covering the melt with a powdery No. 2 solvent, and transferring the melt to a heat preservation furnace when the temperature of the melt is 710-760 ℃ to obtain an aluminum alloy melt;
3. introducing Ar gas and Ar-Cl into the aluminum alloy melt 2 Performing double-stage degassing on the mixed gas, performing double-stage filtration, starting casting on an on-line AlTi5B1 wire, and simultaneously measuring hydrogen at a launder until the casting is finished, thereby obtaining an alloy cast ingot, wherein the hydrogen content is less than or equal to 0.15ml/100 gAl;
4. heating the alloy ingot at 485-495 ℃ for 18-25 h to finish homogenizing annealing treatment of the ingot, then carrying out face milling, sawing and skin welding treatment, carrying out finish hot rolling at 290-330 ℃, and then carrying out cold rolling to obtain an Al-Zn-Mg-Cu aluminum alloy sheet with the finished product thickness of 1.6-6.35 mm;
5. and carrying out finished annealing on the Al-Zn-Mg-Cu aluminum alloy sheet to obtain a finished annealed sheet, and carrying out roll straightening, finished shearing or sawing treatment to obtain the medium-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet.
Further, the aluminum-copper intermediate alloy in the first step is AlCu40 intermediate alloy; the aluminum-manganese intermediate alloy is an AlMn10 intermediate alloy, and the aluminum-titanium intermediate alloy is an AlTi6 intermediate alloy.
Further, the dosage of the powdery 2# solvent in the second step accounts for 0.1 to 0.3 percent of the total mass of the melt.
Further, the gas flow rate of the two-stage degassing in the third step is 0.5m 3 /h～1.5m 3 And/h, the time is 30-50 min.
Further, ar-Cl as described in step three 2 The mixed gas is 95% high purity argon mixed with 5% high purity chlorine.
Further, in step three, the two-stage filtration: a30 ppi+50ppi ceramic filter sheet was used for filtration.
Further, the amount of the AlTi5B1 filaments in the third step: the amount of Ti element added was 0.005wt% based on the total weight of the aluminum alloy melt.
Further, in the fourth step, the skin material welding treatment is as follows: adopting 1230 alloy as an aluminum-clad skin material; the welding adopts a riveting mode.
Further, annealing the finished product in the fifth step: the annealing temperature is carried out according to the AMS2772 standard, the heat preservation is carried out for 2 to 3 hours, the annealing temperature is cooled to 180 to 210 ℃ along with the furnace, and then the annealing temperature is discharged from the furnace for air cooling.
The invention has the beneficial effects that:
the intermediate-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet prepared in the invention has K in T42 state app The value can reach 90MPa m 1/2 ～110MPa·m 1/2 The strength Cv value is 1.0% -3.0%, meets the product standard requirements, solves the problem of industrialized preparation of the damage tolerance Al-Zn-Mg-Cu aluminum alloy O state sheet, has the characteristics of medium strength and high damage tolerance, and can provide a new material for the fuselage frame, control surface and the like of a large civil aircraft.
The invention is suitable for preparing the intermediate damage tolerance Al-Zn-Mg-Cu aluminum alloy O-state aluminum clad sheet.
Drawings
FIG. 1 is a polarization structure diagram of a medium-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet prepared in the implementation;
FIG. 2 is an EBSD tissue map of the T42 state of a medium strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-clad aluminum sheet prepared in the practice.
Detailed Description
The technical scheme of the invention is not limited to the specific embodiments listed below, and also includes any combination of the specific embodiments.
The first embodiment is as follows: the preparation method of the medium-strength damage-resistant tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet in the embodiment comprises the following steps of:
1. the weight percentage of elements is as follows: si less than or equal to 0.50%, fe less than or equal to 0.30%, cu:4.3 to 4.9 percent of Mn:0.4 to 1.0 percent of Mg:1.3 to 1.7 percent of Zn:0.1 to 0.15 percent of Ti:0.02 to 0.04 percent, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurity and the balance of Al, and weighing aluminum ingot, magnesium ingot, zinc ingot, aluminum copper intermediate alloy, aluminum manganese intermediate alloy and aluminum titanium intermediate alloy for remelting;
2. adding the aluminum ingot, the magnesium ingot, the zinc ingot, the aluminum copper intermediate alloy, the aluminum manganese intermediate alloy and the aluminum titanium intermediate alloy which are weighed in the first step into a smelting furnace, smelting at 700-760 ℃, covering the melt with a powdery No. 2 solvent, and transferring the melt to a heat preservation furnace when the temperature of the melt is 710-760 ℃ to obtain an aluminum alloy melt;
3. introducing Ar gas and Ar-Cl into the aluminum alloy melt 2 Performing double-stage degassing on the mixed gas, performing double-stage filtration, starting casting on an on-line AlTi5B1 wire, and simultaneously measuring hydrogen at a launder until the casting is finished, thereby obtaining an alloy cast ingot, wherein the hydrogen content is less than or equal to 0.15ml/100 gAl;
4. heating the alloy ingot at 485-495 ℃ for 18-25 h to finish homogenizing annealing treatment of the ingot, then carrying out face milling, sawing and skin welding treatment, carrying out finish hot rolling at 290-330 ℃, and then carrying out cold rolling to obtain an Al-Zn-Mg-Cu aluminum alloy sheet with the finished product thickness of 1.6-6.35 mm;
5. and carrying out finished annealing on the Al-Zn-Mg-Cu aluminum alloy sheet to obtain a finished annealed sheet, and carrying out roll straightening, finished shearing or sawing treatment to obtain the medium-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet.
The second embodiment is as follows: the first difference between the present embodiment and the specific embodiment is that in the first step, the weight percentage of the elements is as follows: si less than or equal to 0.50%, fe less than or equal to 0.30%, cu:4.5%, mn:0.6%, mg:1.5%, zn:0.12%, ti:0.03 percent, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurity and the balance of Al. Other steps and parameters are the same as in the first embodiment.
And a third specific embodiment: the first difference between the present embodiment and the specific embodiment is that the aluminum-copper intermediate alloy in the first step is an AlCu40 intermediate alloy; the aluminum-manganese intermediate alloy is an AlMn10 intermediate alloy, and the aluminum-titanium intermediate alloy is an AlTi6 intermediate alloy. Other steps and parameters are the same as in the first embodiment.
The specific embodiment IV is as follows: the first difference between the present embodiment and the specific embodiment is that the amount of the powdery 2# solvent in the second step is 0.1 to 0.3% of the total mass of the melt. Other steps and parameters are the same as in the first embodiment.
Fifth embodiment: the difference between the present embodiment and the specific embodiment is that the gas flow rate of the two-stage degassing in the third step is 0.5m 3 /h～1.5m 3 And/h, the time is 30-50 min. Other steps and parameters are the same as in the first embodiment.
Specific embodiment six: the present embodiment differs from the specific embodiment in that Ar-Cl is described in the third step 2 The mixed gas is 95% high purity argon mixed with 5% high purity chlorine. Other steps and parameters are the same as in the first embodiment.
Seventh embodiment: the first difference between this embodiment and the specific embodiment is that the two-stage filtration in the third step: a30 ppi+50ppi ceramic filter sheet was used for filtration. Other steps and parameters are the same as in the first embodiment.
Eighth embodiment: the first difference between this embodiment and the specific embodiment is that the amount of the AlTi5B1 filaments in the third step: the amount of Ti element added was 0.005wt% based on the total weight of the aluminum alloy melt. Other steps and parameters are the same as in the first embodiment.
Detailed description nine: the first difference between the present embodiment and the specific embodiment is that in the fourth step, the skin material welding process is as follows: adopting 1230 alloy as an aluminum-clad skin material; the welding adopts a riveting mode. Other steps and parameters are the same as in the first embodiment.
Detailed description ten: the first difference between this embodiment and the specific embodiment is that in the fifth step, the finished product is annealed: the annealing temperature is carried out according to the AMS2772 standard, the heat preservation is carried out for 2 to 3 hours, the annealing temperature is cooled to 180 to 210 ℃ along with the furnace, and then the annealing temperature is discharged from the furnace for air cooling. Other steps and parameters are the same as in the first embodiment.
The beneficial effects of the invention are verified by the following examples:
examples:
a method for preparing a medium-strength damage-resistant tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet comprises the following steps:
1. the weight percentage of elements is as follows: si less than or equal to 0.50%, fe less than or equal to 0.30%, cu:4.5%, mn:0.6%, mg:1.5%, zn:0.12%, ti:0.03 percent, less than or equal to 0.05 percent of single impurities, less than or equal to 0.15 percent of total impurities and the balance of Al, and weighing aluminum ingots, magnesium ingots, zinc ingots, aluminum-copper intermediate alloys, aluminum-manganese intermediate alloys and aluminum-titanium intermediate alloys for remelting;
2. adding the aluminum ingot, the magnesium ingot, the zinc ingot, the aluminum copper intermediate alloy, the aluminum manganese intermediate alloy and the aluminum titanium intermediate alloy which are weighed in the first step into a smelting furnace, smelting at 720 ℃, covering the melt with a powdery No. 2 solvent, and transferring the melt to a heat preservation furnace when the temperature of the melt is 710-760 ℃ to obtain an aluminum alloy melt;
3. introducing Ar gas and Ar-Cl into the aluminum alloy melt 2 Performing double-stage degassing on the mixed gas, performing double-stage filtration, starting casting on an on-line AlTi5B1 wire, and simultaneously measuring hydrogen at a launder until the casting is finished, thereby obtaining an alloy cast ingot, wherein the hydrogen content is less than or equal to 0.15ml/100 gAl;
4. heating the alloy ingot at 490 ℃ for 22 hours to finish homogenization annealing treatment of the ingot, then carrying out face milling, sawing and skin welding treatment, carrying out finish hot rolling at 320 ℃, and carrying out sub-rolling to obtain an Al-Zn-Mg-Cu aluminum alloy sheet with the finished product thickness of 4.0 mm;
5. and carrying out finished annealing on the Al-Zn-Mg-Cu aluminum alloy sheet to obtain a finished annealed sheet, and carrying out roll straightening, finished shearing or sawing treatment to obtain the medium-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet.
In the implementation, the aluminum-copper intermediate alloy in the first step is AlCu40 intermediate alloy; the aluminum-manganese intermediate alloy is an AlMn10 intermediate alloy, and the aluminum-titanium intermediate alloy is an AlTi6 intermediate alloy.
In the second step of this embodiment, the amount of the powdery solvent 2# is 0.2% of the total mass of the melt.
The gas flow rate of the two-stage degassing in the third step of the implementation is 1m 3 And/h, the time is 40min.
Ar-Cl as described in step three of this embodiment 2 The mixed gas is 95% high purity argon mixed with 5% high purity chlorine.
In the present embodiment, the two-stage filtration is as described in step three: a30 ppi+50ppi ceramic filter sheet was used for filtration.
The amount of the AlTi5B1 filaments in the third step of the implementation: the amount of Ti element added was 0.005wt% based on the total weight of the aluminum alloy melt.
In the fourth step of this embodiment, the skin material welding treatment is as follows: adopting 1230 alloy as an aluminum-clad skin material; the welding adopts a riveting mode.
In the fifth step of the implementation, annealing the finished product: the annealing temperature is carried out according to the AMS2772 standard, the heat preservation is carried out for 2 hours, the annealing temperature is cooled to 200 ℃ along with the furnace, and then the annealing temperature is discharged from the furnace for air cooling.
The medium-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet obtained in the embodiment is sampled to carry out T42 heat treatment response test, the solid solution temperature is carried out according to AMS2772, the heat preservation time is 45min, and natural parking is carried out for more than or equal to 96h; then performance detection is carried out, and K in T42 state app The value can reach 100MPa m 1/2 Intensity Cv value is 2.0%; after the detection is qualified, the moderate-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet prepared in the implementation can be packaged.
The polarizing structure diagram (see fig. 1) of the medium-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet obtained in the embodiment shows that the crystal grains are recrystallized structures, and the structure assurance is provided for the subsequent sheet deformation treatment.
The EBSD structure diagram (see fig. 2) of the T42 state of the medium-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-clad aluminum sheet obtained in this example shows that the T42 state grains are completely recrystallized, and the average grain size of the equivalent diameter is about 27 μm, so as to ensure good plasticity.
Claims (10)
1. The preparation method of the medium-strength damage-resistant tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet is characterized by comprising the following steps of:
1. the weight percentage of elements is as follows: si less than or equal to 0.50%, fe less than or equal to 0.30%, cu:4.3 to 4.9 percent of Mn:0.4 to 1.0 percent of Mg:1.3 to 1.7 percent of Zn:0.1 to 0.15 percent of Ti:0.02 to 0.04 percent, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurity and the balance of Al, and weighing aluminum ingot, magnesium ingot, zinc ingot, aluminum copper intermediate alloy, aluminum manganese intermediate alloy and aluminum titanium intermediate alloy for remelting;
2. adding the aluminum ingot, the magnesium ingot, the zinc ingot, the aluminum copper intermediate alloy, the aluminum manganese intermediate alloy and the aluminum titanium intermediate alloy which are weighed in the first step into a smelting furnace, smelting at 700-760 ℃, covering the melt with a powdery No. 2 solvent, and transferring the melt to a heat preservation furnace when the temperature of the melt is 710-760 ℃ to obtain an aluminum alloy melt;
3. introducing Ar gas and Ar-Cl into the aluminum alloy melt 2 Performing double-stage degassing on the mixed gas, performing double-stage filtration, starting casting on an on-line AlTi5B1 wire, and simultaneously measuring hydrogen at a launder until the casting is finished, thereby obtaining an alloy cast ingot, wherein the hydrogen content is less than or equal to 0.15ml/100 gAl;
4. heating the alloy ingot at 485-495 ℃ for 18-25 h to finish homogenizing annealing treatment of the ingot, then carrying out face milling, sawing and skin welding treatment, carrying out finish hot rolling at 290-330 ℃, and then carrying out cold rolling to obtain an Al-Zn-Mg-Cu aluminum alloy sheet with the finished product thickness of 1.6-6.35 mm;
5. and carrying out finished annealing on the Al-Zn-Mg-Cu aluminum alloy sheet to obtain a finished annealed sheet, and carrying out roll straightening, finished shearing or sawing treatment to obtain the medium-strength damage tolerance Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet.
2. The method for preparing the medium-strength damage-tolerant Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet according to claim 1, wherein the method comprises the following steps of: si less than or equal to 0.50%, fe less than or equal to 0.30%, cu:4.5%, mn:0.6%, mg:1.5%, zn:0.12%, ti:0.03 percent, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurity and the balance of Al.
3. The method for preparing a medium-strength damage-tolerant Al-Cu-Mg-Mn aluminum alloy O-state clad aluminum sheet according to claim 1, wherein the aluminum-copper intermediate alloy in the step one is an AlCu40 intermediate alloy; the aluminum-manganese intermediate alloy is an AlMn10 intermediate alloy, and the aluminum-titanium intermediate alloy is an AlTi6 intermediate alloy.
4. The method for preparing the medium-strength damage-tolerant Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet according to claim 1, wherein the powdery No. 2 solvent is used in an amount of 0.1-0.3% of the total mass of the melt in the second step.
5. The method for producing a medium-strength damage tolerant Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet according to claim 1, wherein the gas flow rate of the two-stage degassing in the third step is 0.5m 3 /h～1.5m 3 And/h, the time is 30-50 min.
6. The method for producing a medium-strength damage tolerant Al-Cu-Mg-Mn aluminum alloy O-clad aluminum sheet according to claim 1, wherein in the third step, ar-Cl is 2 The mixed gas is 95% high purity argon mixed with 5% high purity chlorine.
7. The method for producing a medium-strength damage tolerant Al-Cu-Mg-Mn aluminum alloy O-clad aluminum sheet according to claim 1, wherein in step three, the two-stage filtration is performed: a30 ppi+50ppi ceramic filter sheet was used for filtration.
8. The method for preparing the medium-strength damage-tolerant Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet according to claim 1, wherein the amount of AlTi5B1 wires in the third step is as follows: the amount of Ti element added was 0.005wt% based on the total weight of the aluminum alloy melt.
9. The method for preparing the medium-strength damage-tolerant Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet according to claim 1, wherein the skin welding treatment in the fourth step is as follows: adopting 1230 alloy as an aluminum-clad skin material; the welding adopts a riveting mode.
10. The method for preparing the medium-strength damage-tolerant Al-Cu-Mg-Mn aluminum alloy O-state aluminum clad sheet according to claim 1, wherein in the fifth step, the finished product is annealed: the annealing temperature is carried out according to the AMS2772 standard, the heat preservation is carried out for 2 to 3 hours, the annealing temperature is cooled to 180 to 210 ℃ along with the furnace, and then the annealing temperature is discharged from the furnace for air cooling.
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