CN113444941A - Method for improving strength of 2024-T3 board - Google Patents
Method for improving strength of 2024-T3 board Download PDFInfo
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- CN113444941A CN113444941A CN202110679508.9A CN202110679508A CN113444941A CN 113444941 A CN113444941 A CN 113444941A CN 202110679508 A CN202110679508 A CN 202110679508A CN 113444941 A CN113444941 A CN 113444941A
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- 238000000034 method Methods 0.000 title claims abstract description 21
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 30
- 238000005097 cold rolling Methods 0.000 claims abstract description 19
- 238000005098 hot rolling Methods 0.000 claims abstract description 17
- 238000010438 heat treatment Methods 0.000 claims abstract description 16
- 239000006104 solid solution Substances 0.000 claims abstract description 16
- 238000005266 casting Methods 0.000 claims abstract description 10
- 230000032683 aging Effects 0.000 claims abstract description 9
- 238000000265 homogenisation Methods 0.000 claims abstract description 9
- 239000000463 material Substances 0.000 claims abstract description 8
- 238000002360 preparation method Methods 0.000 claims abstract description 5
- 238000005520 cutting process Methods 0.000 claims abstract description 4
- 239000000243 solution Substances 0.000 claims description 10
- 238000005096 rolling process Methods 0.000 claims description 9
- 239000002994 raw material Substances 0.000 claims description 8
- 229910045601 alloy Inorganic materials 0.000 claims description 6
- 239000000956 alloy Substances 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 6
- 238000003801 milling Methods 0.000 claims description 6
- 238000007599 discharging Methods 0.000 claims description 4
- 238000010791 quenching Methods 0.000 claims description 4
- 230000000171 quenching effect Effects 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 238000001816 cooling Methods 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 238000004321 preservation Methods 0.000 claims description 3
- 239000007921 spray Substances 0.000 claims description 3
- 229910052725 zinc Inorganic materials 0.000 claims description 3
- 238000003723 Smelting Methods 0.000 claims description 2
- 238000009749 continuous casting Methods 0.000 claims description 2
- 238000007872 degassing Methods 0.000 claims description 2
- 238000001914 filtration Methods 0.000 claims description 2
- 238000004806 packaging method and process Methods 0.000 claims description 2
- 238000004513 sizing Methods 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 abstract description 4
- 239000002245 particle Substances 0.000 abstract description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract 1
- 229910052782 aluminium Inorganic materials 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 14
- 238000012360 testing method Methods 0.000 description 3
- 238000009826 distribution Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 229910001250 2024 aluminium alloy Inorganic materials 0.000 description 1
- 229910017818 Cu—Mg Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 238000006467 substitution reaction Methods 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
- C22C21/12—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
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- 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
- 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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- 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
- C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Metal Rolling (AREA)
Abstract
The invention relates to a method for improving the strength of a 2024-T3 plate, belonging to the field of aluminum profile production. The method comprises the steps of material preparation, casting, homogenization, saw cutting, heating, hot rolling, solid solution, natural standing, cold rolling and natural aging; wherein in the hot rolling step, the maximum reduction amount is controlled to be 50-60 mm; controlling the natural parking time to be 12-16 h; the cold rolling reduction rate is controlled to be 1.5-2.5%. The aluminum alloy plate is hot rolled by adopting small passes and large reduction, the second phase particles are fully crushed, the natural standing time between the solid solution and cold rolling processes is controlled, and the aluminum alloy plate with higher transverse strength is produced by controlling the cold rolling reduction and the cold rolling passes after the standing time.
Description
Technical Field
The invention belongs to the field of aluminum alloy processing, and relates to 5052 aluminum alloy with high bending performance and a preparation method thereof.
Background
2024 aluminum alloy is Al-Cu-Mg series high strength and hard aluminum alloy, and is widely applied to military and civil industries due to good comprehensive properties of high strength, high toughness, heat resistance, low specific gravity and the like. 2024 the conventional state is T3, and the conventional process flow is: ingot casting, heating, hot rolling, solid solution, stretching and natural aging.
The traditional 2024-T3 thick plate production adopts a multi-pass and small-reduction hot rolling mode, the second phase with a thick core part cannot be fully crushed, and the re-dissolution cannot be fully carried out in a solid solution stage; after solution quenching, the alloy is stretched by 1.5% to 3% to increase the strength of the alloy, and although stretching can increase the strength of the alloy, the transverse deformation is small, so that the transverse strength is increased to a limited extent.
Disclosure of Invention
In view of the above, the present invention is directed to a method for improving the strength of 2024-T3 board, so as to solve the disadvantages of the current 2024-T3 board production process.
In order to achieve the purpose, the invention provides the following technical scheme:
a method for improving the strength of 2024-T3 plates comprises the following steps:
s1, material preparation: preparing an aluminum alloy raw material according to the following alloy elements and mass percentages, wherein Si is less than or equal to 0.08%, Fe is less than or equal to 0.15%, and Cu: 4.4-4.7%, Mn: 0.5-0.7%, Mg: 1.3-1.6%, Cr is less than or equal to 0.05%, Zn is less than or equal to 0.06%, Ti: 0.018-0.032%, less than or equal to 0.05% of single impurity, less than or equal to 0.15% of impurity in total, and the balance of Al;
s2, casting: adding the prepared aluminum alloy raw material into a semi-continuous casting furnace to be cast into an aluminum alloy ingot;
s3, homogenizing: carrying out homogenization heat treatment on the cast aluminum alloy ingot, wherein the homogenization temperature is 490-500 ℃, and the heat preservation time is 15-25 h;
s4, sawing: cutting the head and the tail of the homogenized aluminum alloy cast ingot, and milling a surface crust layer by using a milling machine;
s5, heating: heating the sawed aluminum alloy ingot in a heating furnace to the furnace gas temperature of 420-460 ℃, preserving heat for 2-6 h, and discharging;
s6, hot rolling: hot rolling the heated aluminum alloy ingot into a plate, wherein the maximum rolling reduction is 50-60 mm;
s7, solid solution: carrying out solution treatment on the plate in a roller hearth furnace, wherein the solution degree is (496 +/-3) DEG C (120+200) min;
s8, natural parking: naturally standing the plate after the solid solution for 12-16 h;
s9, cold rolling: the naturally parked plate is subjected to one-time cold rolling on a rolled piece according to the longitudinal reduction rate of 1.5-2.5% to obtain the finished product thickness;
s10, natural aging: and naturally aging the cold-rolled plate for 96 h.
Further, in step S2, the prepared aluminum alloy raw material is added into a semicontinuous casting furnace to produce an aluminum alloy ingot through the procedures of smelting, slagging-off, degassing, standing, filtering and casting.
Further, in step S3, after the homogenization heat treatment, air cooling is performed for 4-8 hours.
Further, in step S7, spray quenching is performed after solid solution.
Further, the method also comprises the following steps:
s11, sizing: and sawing the naturally aged plate by using a precision saw to length, checking and packaging.
Furthermore, the yield strength of the finished plate is 336-352 MPa, and the tensile strength is 470-481 MPa.
The invention has the beneficial effects that:
(1) for the production of 2024-T3 plates, the hot rolling in the prior art adopts a multi-pass and small reduction (less than or equal to 35mm) mode, the second phase with a large core part can not be completely crushed, and the solid solution stage can not be fully dissolved, so that the final strength is not high. The method adopts a mode of few passes and large reduction, the maximum reduction is controlled to be 50-60 mm, and the second phase is fully crushed under the condition of ensuring that the hot rolled plate blank is not over-burnt, so that the second phase is more easily re-dissolved to a matrix in the subsequent solid solution stage.
(2) In the prior art, 1.5-3% of stretching is carried out after solid solution, so that the purposes of eliminating internal stress and improving mechanical property are achieved, the stretching is unidirectional deformation, and the transverse strength is not obviously contributed. The invention replaces drawing with cold rolling, and the cold rolling reduction rate is controlled to be 1.5-3%; under the same deformation rate, the transverse yield strength is greatly improved. This is because components in the longitudinal and thickness directions are generated during the cold rolling, and the internal metal is compressed to generate a transverse flow, and a slight widening deformation is generated in the transverse direction, so that the work strengthening is generated, and the transverse tensile strength and yield strength are improved to different degrees.
(3) The supersaturated solid solution can form a nano-scale precipitated phase when being parked at room temperature, the size and the distribution of the precipitated phase can influence the final performance, and the size and the distribution of the precipitated phase are related to the natural parking time. If the natural standing time is too short, the precipitated phase cannot form a large number of effective nucleation particles, and the final strength after cold deformation is lower; the natural standing time is too long, the second phase is separated out too much, the size is too large, the driving force of the natural aging after cold deformation is insufficient, the strength is reduced, and the final plasticity is reduced. The method controls the natural standing time to be 12-16 h, and produces the transverse high-strength plate.
Additional advantages, objects, and features of the invention will be set forth in part in the description which follows and in part will become apparent to those having ordinary skill in the art upon examination of the following or may be learned from practice of the invention. The objectives and other advantages of the invention may be realized and attained by the means of the instrumentalities and combinations particularly pointed out hereinafter.
Detailed Description
The embodiments of the present invention are described below with reference to specific embodiments, and other advantages and effects of the present invention will be easily understood by those skilled in the art from the disclosure of the present specification. The invention is capable of other and different embodiments and of being practiced or of being carried out in various ways, and its several details are capable of modification in various respects, all without departing from the spirit and scope of the present invention.
Example 1:
a method for improving the strength of 2024-T3 plates comprises the following steps:
s1, material preparation: preparing an aluminum alloy raw material according to the following alloy elements and mass percentages, wherein Si is less than or equal to 0.08%, Fe is less than or equal to 0.15%, and Cu: 4.4-4.7%, Mn: 0.5-0.7%, Mg: 1.3-1.6%, Cr is less than or equal to 0.05%, Zn is less than or equal to 0.06%, Ti: 0.018-0.032%, less than or equal to 0.05% of single impurity, less than or equal to 0.15% of impurity in total, and the balance of Al;
s2, casting: adding the prepared aluminum alloy raw material into a semicontinuous casting furnace to cast into an aluminum alloy ingot with the specification of 450mm multiplied by 1580mm multiplied by 4500 mm;
s3, homogenizing: carrying out homogenization heat treatment on the cast aluminum alloy ingot, wherein the homogenization temperature is 490-500 ℃, the heat preservation time is 15-25 h, and discharging and air cooling are carried out for 4-8 h;
s4, sawing: cutting the head and the tail of the homogenized aluminum alloy cast ingot, and milling a surface crust layer by using a milling machine;
s5, heating: heating the sawed aluminum alloy ingot in a heating furnace to the furnace gas temperature of 420-460 ℃, preserving heat for 2-6 h, and discharging;
s6, hot rolling: hot rolling the heated aluminum alloy ingot into a plate, wherein the maximum rolling reduction is 50-60 mm;
s7, solid solution: carrying out solution treatment on the plate in a roller hearth furnace, wherein the solution treatment system is (496 +/-3) DEG C (120+200) min, and then carrying out spray quenching;
s8, natural parking: naturally standing the plate after solid solution for 12 hours;
s9, cold rolling: the naturally parked plate is cold-rolled on a rolled piece by one time according to the longitudinal 1.5 percent reduction rate to form the finished product thickness;
s10, natural aging: and naturally aging the cold-rolled plate for 96 h.
Example 2:
the main difference between example 2 and example 1 is that: the cold rolling reduction is controlled at 2%.
Example 3:
the main difference between example 3 and example 1 is that: the natural standing time is 14h, and the cold rolling reduction rate is 2.2 percent.
Example 4:
example 4 differs from example 1 mainly in that: the natural standing time is 16h, and the cold rolling reduction rate is 2.5 percent.
Comparative example 1:
the main difference between comparative example 1 and example 1 is that: in step S6, the maximum rolling reduction in hot rolling is 28 to 30 mm. In step S8, the vehicle is parked for 1 h. In step S9, the sheet is subjected to tensile deformation of 1.5% in the longitudinal direction, instead of cold rolling.
Comparative example 2:
the main difference between comparative example 2 and example 1 is that: in step S6, the maximum rolling reduction in hot rolling is 28 to 30 mm. In step S8, the vehicle is parked for 6 h. In step S9, the sheet is deformed by 2% of tension in the longitudinal direction, instead of being cold-rolled.
Comparative example 3:
the main difference between comparative example 3 and example 1 is that: in step S6, the maximum rolling reduction in hot rolling is 28 to 30 mm. In step S8, the vehicle is parked for 14 h. In step S9, the sheet material is deformed by 2.2% of tension in the longitudinal direction, instead of being cold-rolled.
Comparative example 4:
the main difference between comparative example 4 and example 1 is that: in step S6, the maximum rolling reduction in hot rolling is 28 to 30 mm. In step S8, the vehicle is parked for 16 h. In step S9, the sheet material is deformed by 2.5% of tension in the longitudinal direction, instead of being cold-rolled.
Comparative example 5:
the main difference between comparative example 6 and example 1 is that: in step S6, the maximum rolling reduction in hot rolling is 28 to 30 mm. In step S8, the vehicle is parked for 8 h. In step S9, the sheet material is deformed by 2.5% of tension in the longitudinal direction, instead of being cold-rolled.
The test standards of examples and comparative examples were conducted in accordance with ASTM B557, LT to tensile specimen sampling position at the center of the width of the sheet material at thickness 1/4, and mechanical test results are shown in Table 1.
TABLE 1 results of mechanical testing of examples 1-4 and comparative examples 1-5
From the comparative example results it can be seen that: under the conditions of small rolling reduction and stretching, the LT yield strength in the transverse direction is 323.5-335 MPa, and the tensile strength is 459-467 MPa. According to the invention, the large reduction (the maximum reduction is 50-60 mm), the natural standing time is controlled to be 12-16 h, the cold rolling processing rate is controlled to be 1.5-2.5%, the plate with better comprehensive mechanical property is obtained, the yield strength is 336-352 MPa, the tensile strength is 470-481 MPa, and compared with a comparative example, the plate strength is improved.
The results show that the plate with the tensile property higher than that of the plate obtained by the prior art by adopting a hot rolling mode with the pass large reduction (50-60 mm), controlling the natural standing time to be 12-16 h and the cold rolling reduction rate to be 1.5-2.2% is obtained.
Finally, the above embodiments are only intended to illustrate the technical solutions of the present invention and not to limit the present invention, and although the present invention has been described in detail with reference to the preferred embodiments, it will be understood by those skilled in the art that modifications or equivalent substitutions may be made on the technical solutions of the present invention without departing from the spirit and scope of the technical solutions, and all of them should be covered by the claims of the present invention.
Claims (6)
1. A method for improving the strength of 2024-T3 boards is characterized in that: the method comprises the following steps:
s1, material preparation: preparing an aluminum alloy raw material according to the following alloy elements and mass percentages, wherein Si is less than or equal to 0.08%, Fe is less than or equal to 0.15%, and Cu: 4.4-4.7%, Mn: 0.5-0.7%, Mg: 1.3-1.6%, Cr is less than or equal to 0.05%, Zn is less than or equal to 0.06%, Ti: 0.018-0.032%, less than or equal to 0.05% of single impurity, less than or equal to 0.15% of impurity in total, and the balance of Al;
s2, casting: adding the prepared aluminum alloy raw material into a semi-continuous casting furnace to be cast into an aluminum alloy ingot;
s3, homogenizing: carrying out homogenization heat treatment on the cast aluminum alloy ingot, wherein the homogenization temperature is 490-500 ℃, and the heat preservation time is 15-25 h;
s4, sawing: cutting the head and the tail of the homogenized aluminum alloy cast ingot, and milling a surface crust layer by using a milling machine;
s5, heating: heating the sawed aluminum alloy ingot in a heating furnace to the furnace gas temperature of 420-460 ℃, preserving heat for 2-6 h, and discharging;
s6, hot rolling: hot rolling the heated aluminum alloy ingot into a plate, wherein the maximum rolling reduction is 50-60 mm;
s7, solid solution: carrying out solution treatment on the plate in a roller hearth furnace, wherein the solution degree is (496 +/-3) DEG C (120+200) min;
s8, natural parking: naturally standing the plate after the solid solution for 12-16 h;
s9, cold rolling: the naturally parked plate is subjected to one-time cold rolling on a rolled piece according to the longitudinal reduction rate of 1.5-2.5% to obtain the finished product thickness;
s10, natural aging: and naturally aging the cold-rolled plate for 96 h.
2. The method for improving the strength of the 2024-T3 panel according to claim 1, wherein: in step S2, the prepared aluminum alloy raw material is added into a semicontinuous casting furnace to produce an aluminum alloy ingot through the working procedures of smelting, slagging-off, degassing, standing, filtering and casting.
3. The method for improving the strength of the 2024-T3 panel according to claim 1, wherein: in step S3, after the homogenization heat treatment, air cooling is carried out for 4-8 h.
4. The method for improving the strength of the 2024-T3 panel according to claim 1, wherein: in step S7, spray quenching is performed after solid solution.
5. The method for improving the strength of the 2024-T3 panel according to claim 1, wherein: further comprising the steps of:
s11, sizing: and sawing the naturally aged plate by using a precision saw to length, checking and packaging.
6. The method for improving the strength of the 2024-T3 panel according to claim 1, wherein: the yield strength of the finished plate is 336-352 MPa, and the tensile strength is 470-481 MPa.
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| Application Number | Priority Date | Filing Date | Title |
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| CN202110679508.9A CN113444941A (en) | 2021-06-18 | 2021-06-18 | Method for improving strength of 2024-T3 board |
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| Application Number | Priority Date | Filing Date | Title |
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| CN202110679508.9A CN113444941A (en) | 2021-06-18 | 2021-06-18 | Method for improving strength of 2024-T3 board |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114752831A (en) * | 2022-03-24 | 2022-07-15 | 中南大学 | High-strength corrosion-resistant aluminum alloy and preparation method and application thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4490189A (en) * | 1982-04-13 | 1984-12-25 | Aluminium Pechiney | Method of manufacturing stamped-out or forged parts made of aluminum alloys |
| CN103981410A (en) * | 2014-05-27 | 2014-08-13 | 中南大学 | High damage-resistant aluminium alloy and preparation method thereof |
| CN110952011A (en) * | 2019-11-22 | 2020-04-03 | 天津忠旺铝业有限公司 | 2-series high-damage-tolerance aluminum alloy plate and preparation method thereof |
-
2021
- 2021-06-18 CN CN202110679508.9A patent/CN113444941A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4490189A (en) * | 1982-04-13 | 1984-12-25 | Aluminium Pechiney | Method of manufacturing stamped-out or forged parts made of aluminum alloys |
| CN103981410A (en) * | 2014-05-27 | 2014-08-13 | 中南大学 | High damage-resistant aluminium alloy and preparation method thereof |
| CN110952011A (en) * | 2019-11-22 | 2020-04-03 | 天津忠旺铝业有限公司 | 2-series high-damage-tolerance aluminum alloy plate and preparation method thereof |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114752831A (en) * | 2022-03-24 | 2022-07-15 | 中南大学 | High-strength corrosion-resistant aluminum alloy and preparation method and application thereof |
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