CN115584417B - Aluminum alloy with high strength and high toughness and preparation method thereof - Google Patents
Aluminum alloy with high strength and high toughness and preparation method thereof Download PDFInfo
- Publication number
- CN115584417B CN115584417B CN202211226847.2A CN202211226847A CN115584417B CN 115584417 B CN115584417 B CN 115584417B CN 202211226847 A CN202211226847 A CN 202211226847A CN 115584417 B CN115584417 B CN 115584417B
- Authority
- CN
- China
- Prior art keywords
- alloy
- aluminum
- ingot
- aluminum alloy
- stirring
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 43
- 238000002360 preparation method Methods 0.000 title abstract description 9
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 92
- 239000000956 alloy Substances 0.000 claims abstract description 92
- 230000032683 aging Effects 0.000 claims abstract description 21
- 238000010438 heat treatment Methods 0.000 claims abstract description 20
- 238000005266 casting Methods 0.000 claims abstract description 16
- 239000006104 solid solution Substances 0.000 claims abstract description 13
- 238000005303 weighing Methods 0.000 claims abstract description 13
- 229910017818 Cu—Mg Inorganic materials 0.000 claims abstract description 11
- 229910052802 copper Inorganic materials 0.000 claims abstract description 5
- 238000003756 stirring Methods 0.000 claims description 16
- 239000011777 magnesium Substances 0.000 claims description 14
- 229910052782 aluminium Inorganic materials 0.000 claims description 12
- 239000003795 chemical substances by application Substances 0.000 claims description 12
- -1 aluminum titanium boron Chemical compound 0.000 claims description 11
- 229910052749 magnesium Inorganic materials 0.000 claims description 11
- 238000005096 rolling process Methods 0.000 claims description 11
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 9
- 229910052751 metal Inorganic materials 0.000 claims description 8
- 239000002184 metal Substances 0.000 claims description 8
- 238000007599 discharging Methods 0.000 claims description 7
- 239000010936 titanium Substances 0.000 claims description 7
- 238000002844 melting Methods 0.000 claims description 6
- 230000008018 melting Effects 0.000 claims description 6
- 238000003801 milling Methods 0.000 claims description 5
- 238000010791 quenching Methods 0.000 claims description 4
- 230000000171 quenching effect Effects 0.000 claims description 4
- 238000009966 trimming Methods 0.000 claims description 4
- 238000001816 cooling Methods 0.000 claims description 3
- 238000003825 pressing Methods 0.000 claims description 3
- 238000003723 Smelting Methods 0.000 claims description 2
- 230000007547 defect Effects 0.000 claims description 2
- 229910052719 titanium Inorganic materials 0.000 claims description 2
- 238000000034 method Methods 0.000 abstract description 13
- 238000005098 hot rolling Methods 0.000 abstract description 8
- 239000000243 solution Substances 0.000 description 10
- 238000004321 preservation Methods 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 3
- 230000006911 nucleation Effects 0.000 description 3
- 238000010899 nucleation Methods 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 229910001133 2324 aluminium alloy Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 230000005764 inhibitory process Effects 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 230000018199 S phase Effects 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 238000003754 machining 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
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- 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
- C21D8/0247—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
- 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
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- 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
- 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
- C22F1/04—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
Abstract
An aluminum alloy with high strength and high toughness and a preparation method thereof relate to an aluminum alloy and a preparation method thereof. Solves the problems that the coarsening T phase is generated in the process of uniform fire in the prior Al-Cu-Mg alloy heat treatment process and the processability is poor. The aluminum alloy with high strength and high toughness consists of Cu, mg, mn, ce, ti and the balance Al; the method comprises the following steps: 1. weighing; 2. casting; 3. hot rolling; 4. solid solution; 5. prestretching; 6. aging. The invention is used for preparing the aluminum alloy with high strength and high toughness at the same time.
Description
Technical Field
The invention relates to an aluminum alloy and a preparation method thereof.
Background
The aluminum alloy has the advantages of higher specific strength, low density, good machining performance, lower cost and the like, and is widely applied to various social fields, but the poor matching property of the strength and the toughness of the aluminum alloy always restricts the application scene of the aluminum alloy. The strength of the Al-Cu-Mg alloy is enough to meet most application scenes, but the pursuit of industry on cost still has higher requirements on the workability of the aluminum alloy, and the higher heat treatment temperature and longer heat treatment time in the common Al-Cu-Mg alloy heat treatment process can lead to coarsening of a T phase generated in the process of homogenizing fire, the T phase is basically one of strengthening phases in the aluminum alloy, the yield strength of the alloy can be improved, but the combination of the T phase and a matrix after coarsening is uneven, the difference of mechanical properties of the T phase and the matrix is detailed, the cooperative deformability of the T phase and the matrix is poor when the alloy is deformed, cracks are generated at the interface of the two phases, so that the toughness and the plasticity of the alloy are influenced, and the workability of the Al-Cu-Mg alloy is poor.
Disclosure of Invention
The invention aims to solve the problem that a coarsened T phase is generated in the process of homogenizing fire in the conventional Al-Cu-Mg alloy heat treatment process and the problem of poor processing performance, and further provides an aluminum alloy with high strength and high toughness and a preparation method thereof.
The aluminum alloy with high strength and high toughness consists of Cu 3.5-4.3 wt%, mg 0.4-0.8 wt%, mn 0.3-0.7 wt%, ce 0.3-0.5 wt%, ti 0.02-0.04 wt% and Al for the rest.
The preparation method of the aluminum alloy with high strength and high toughness comprises the following steps:
1. weighing:
weighing high-precision pure aluminum ingot, pure magnesium ingot, alCu alloy, alMn alloy, alCE alloy and aluminum titanium boron refiner according to the mass percentage of 3.5% -4.3%, 0.4% -0.8%, 0.3% -0.7% of Mn, 0.3% -0.5% of Ce, 0.02% -0.04% of Ti and the balance Al, and then weighing a No. 2 covering agent;
2. casting:
melting the weighed high-precision pure aluminum ingot, pure magnesium ingot, alCu alloy, alMn alloy and AlCE alloy, then adding an aluminum titanium boron refiner and a No. 2 covering agent, and finally stirring, standing, deslagging, casting and homogenizing to obtain a homogenized cast ingot;
3. and (3) hot rolling:
heating the homogenized cast ingot, and then hot-rolling to obtain a rolled alloy plate;
4. solid solution:
trimming the rolled alloy plate, performing solution treatment for 100-120 min, and finally discharging and water quenching to obtain a solution alloy plate;
5. prestretching:
stretching the solid solution alloy plate to obtain an alloy plate;
6. aging:
naturally aging the alloy plate for 700-1000 hours to obtain the aluminum alloy with high strength and high toughness.
The beneficial effects of the invention are as follows:
1. compared with the common 2324 aluminum alloy, the prepared aluminum alloy plate has the advantages that Ce element is added into the alloy, the effects of grain refinement, recrystallization inhibition, solid solution strengthening and the like are achieved, and the strength of the plate is improved, and meanwhile, the tensile property is good.
2. According to the invention, a large number of dislocation is introduced into the alloy through hot rolling and pre-stretching treatment, a large number of nucleation sites are provided for the formation of the precipitated phase in the subsequent natural aging process, the precipitation of the second phase is accelerated, so that the precipitated phase in the alloy is uniformly distributed and has smaller size, and therefore, the strength of the alloy is not reduced due to natural aging, but is improved.
3. According to the invention, the alloy strength is improved by reducing the heating and heat preservation time (only 100-120 min for solution treatment) and long-time natural aging in the heat treatment process, so that the energy is saved, and meanwhile, the influence of the heating and heat preservation on coarsening of the alloy precipitated phase T phase in the solution aging period is reduced, so that the toughness of the alloy is improved.
4. According to the method for simultaneously improving the strength and toughness of the aluminum alloy, the tensile strength of the prepared Al-Cu-Mg alloy plate is 459-476 MPa, the yield strength is 354-367 MPa, and the elongation is 15.4-16.8%.
Drawings
FIG. 1 is a microscopic TEM photograph of an aluminum alloy scale 1 μm prepared in example one and having both high strength and high toughness;
FIG. 2 is a microscopic TEM photograph of a rolled alloy sheet ruler 500nm prepared in the first step of the example;
FIG. 3 is a T-phase microscopic TEM photograph of an aluminum alloy having both high strength and high toughness prepared in example one;
fig. 4 is a drawing graph of an aluminum alloy having both high strength and high toughness prepared in example one.
Detailed Description
The first embodiment is as follows: the aluminum alloy with high strength and high toughness comprises, by mass, 3.5% -4.3% of Cu, 0.4% -0.8% of Mg, 0.3% -0.7% of Mn, 0.3% -0.5% of Ce, 0.02% -0.04% of Ti and the balance of Al.
The beneficial effects of this embodiment are:
1. compared with the common 2324 aluminum alloy, the prepared aluminum alloy plate has the advantages that Ce element is added into the alloy, the effects of grain refinement, recrystallization inhibition, solid solution strengthening and the like are achieved, the strength of the plate is improved, and meanwhile, the tensile property is good.
2. According to the embodiment, a large number of dislocation is introduced into the alloy through hot rolling and pre-stretching treatment, a large number of nucleation sites are provided for the formation of a precipitated phase in the subsequent natural aging process, the precipitation of a second phase is accelerated, the precipitated phase in the alloy is uniformly distributed, and the alloy has a smaller size, so that the strength of the alloy is not reduced due to natural aging, but is improved.
3. According to the embodiment, the alloy strength is improved by reducing the heating and heat preservation time (only 100-120 min in solution treatment) and long-time natural aging in the heat treatment process, so that the energy is saved, and meanwhile, the influence of the heating and heat preservation on coarsening of the alloy precipitated phase T phase in the solution aging period is reduced, so that the toughness of the alloy is improved.
4. According to the method for improving the strength and toughness of the aluminum alloy simultaneously, the tensile strength of the prepared Al-Cu-Mg alloy plate is 459-476 MPa, the yield strength is 354-367 MPa, and the elongation is 15.4-16.8%.
The second embodiment is as follows: the first difference between this embodiment and the specific embodiment is that: the total mass percentage of impurities in the aluminum alloy with high strength and high toughness is less than 0.05 percent. The other is the same as in the first embodiment.
And a third specific embodiment: the preparation method of the aluminum alloy with high strength and high toughness in the embodiment comprises the following steps:
1. weighing:
weighing high-precision pure aluminum ingot, pure magnesium ingot, alCu alloy, alMn alloy, alCE alloy and aluminum titanium boron refiner according to the mass percentage of 3.5% -4.3%, 0.4% -0.8%, 0.3% -0.7% of Mn, 0.3% -0.5% of Ce, 0.02% -0.04% of Ti and the balance Al, and then weighing a No. 2 covering agent;
2. casting:
melting the weighed high-precision pure aluminum ingot, pure magnesium ingot, alCu alloy, alMn alloy and AlCE alloy, then adding an aluminum titanium boron refiner and a No. 2 covering agent, and finally stirring, standing, deslagging, casting and homogenizing to obtain a homogenized cast ingot;
3. and (3) hot rolling:
heating the homogenized cast ingot, and then hot-rolling to obtain a rolled alloy plate;
4. solid solution:
trimming the rolled alloy plate, performing solution treatment for 100-120 min, and finally discharging and water quenching to obtain a solution alloy plate;
5. prestretching:
stretching the solid solution alloy plate to obtain an alloy plate;
6. aging:
naturally aging the alloy plate for 700-1000 hours to obtain the aluminum alloy with high strength and high toughness.
The purity of the high-precision pure aluminum ingot and the pure magnesium ingot in the step one is 99.99 percent.
The specific embodiment IV is as follows: the third difference between this embodiment and the third embodiment is that: the aluminum titanium boron refiner in the first step is AlTi5B1. The other is the same as in the third embodiment.
Fifth embodiment: this embodiment differs from the third or fourth embodiment in that: the homogenization treatment in the second step is specifically performed according to the following steps: homogenizing for 20-24 h at 490-510 ℃ of ingot casting temperature, discharging, air cooling to room temperature, and finally milling the surface. The others are the same as in the third or fourth embodiment.
Specific embodiment six: this embodiment differs from one of the third to fifth embodiments in that: the heating treatment in the third step is specifically to keep the temperature for 2 to 3 hours under the condition that the furnace temperature is 580 to 600 ℃. The others are the same as in embodiments three to five.
Seventh embodiment: this embodiment differs from one of the third to sixth embodiments in that: the hot rolling in the third step is specifically carried out according to the following steps: and rolling under the conditions that the metal temperature is 380-440 ℃, the total rolling deformation is 40-60%, the rolling passes are 10-15, and the pressing amount of each pass is 4-10%, so as to obtain the rolled alloy plate. The others are the same as in embodiments three to six.
Eighth embodiment: this embodiment differs from one of the third to seventh embodiments in that: the thickness of the rolled alloy plate in the third step is 27 mm-31 mm. The others are the same as in embodiments three to seven.
Detailed description nine: this embodiment differs from one of the third to eighth embodiments in that: the solution treatment in the fourth step is specifically carried out according to the following steps: and (3) preserving the temperature for 100-120 min under the condition that the metal temperature is 500-520 ℃. The others are the same as in embodiments three to eight.
Detailed description ten: this embodiment differs from one of the third to ninth embodiments in that: and step five, the prestretching amount in the stretching treatment is 1.8-2.2%. The others are the same as in embodiments three to nine.
The following examples are used to verify the benefits of the present invention:
embodiment one:
an aluminum alloy with high strength and high toughness at the same time consists of, by mass, 4.2% of Cu, 0.7% of Mg, 0.43% of Mn, 0.3% of Ce, 0.03% of Ti and the balance of Al.
The total mass percentage of impurities in the aluminum alloy with high strength and high toughness is less than 0.05 percent.
The preparation method of the aluminum alloy with high strength and high toughness comprises the following steps:
1. weighing:
weighing high-precision pure aluminum ingots, pure magnesium ingots, alCu40 alloy, alMn10 alloy, alCE20 alloy and aluminum titanium boron refiner according to the mass percentage of 4.2 percent of Cu, 0.7 percent of Mg, 0.43 percent of Mn, 0.3 percent of Ce, 0.03 percent of Ti and the balance of Al, and then weighing a No. 2 covering agent;
2. casting:
melting the weighed high-precision pure aluminum ingot, pure magnesium ingot, alCu40 alloy, alMn10 alloy and AlCE20 alloy, then adding an aluminum titanium boron refiner and a No. 2 covering agent, and finally stirring, standing, deslagging and casting to obtain an Al-Cu-Mg aluminum alloy ingot;
3. homogenizing:
homogenizing the Al-Cu-Mg aluminum alloy ingot for 20 hours under the condition that the temperature of the ingot is 490 ℃, discharging the ingot, air-cooling to room temperature, and finally milling the surface to obtain a homogenized ingot;
4. rolling:
heating the homogenized cast ingot, and then rolling under the conditions that the metal temperature is 380-440 ℃, the total rolling deformation is 50%, the rolling passes are 10, and the pressing amount of each pass is 5%, so as to obtain a rolled alloy plate;
5. solid solution:
trimming the rolled alloy plate, heating to the metal temperature of 500 ℃, preserving heat for 120min under the condition that the metal temperature is 500 ℃, and finally discharging and quenching to obtain a solid solution alloy plate;
6. prestretching:
stretching the solid solution alloy plate to obtain an alloy plate;
7. aging:
and naturally aging the alloy plate for 1000 hours to obtain the aluminum alloy with high strength and high toughness.
The mass percentage of Cu in the AlCu40 alloy in the first step is 40%; the mass percentage of Mn in the AlMn10 alloy in the first step is 10%; the mass percentage of Ce in the AlCE20 alloy in the first step is 20%; the aluminum titanium boron refiner in the first step is AlTi5B1; the No. 2 covering agent in the step one is KCl (40%) +MgCl 2 (45％)+BaCl 2 (15％)。
The mass ratio of the No. 2 covering agent to the total mass of Cu, mg, mn, ce, ti and Al in the step one is 0.004:1.
The melting in the second step is specifically smelting for 20min under the condition that the furnace temperature is 750 ℃; stirring, standing, deslagging and casting, wherein the stirring, standing, deslagging and casting are carried out according to the following steps: stirring for 3min at 750 ℃ and stirring speed of 100rpm, standing for 10min after stirring, repeating stirring and standing for 2 times, deslagging at 700-720 ℃, and casting.
And step three, milling the surface until the surface has no obvious defect.
The heating treatment in the fourth step is specifically to keep the temperature for 2 hours under the condition that the furnace temperature is 600 ℃.
The thickness of the rolled alloy plate in the fourth step is 28mm.
The amount of pretension during the stretching treatment in the sixth step was 2%.
And (3) carrying out room temperature tensile mechanical test on the aluminum alloy with high strength and high toughness prepared in the first embodiment, wherein the tensile rate is 5mm/min, and the aluminum alloy with high strength and high toughness prepared in the first embodiment is obtained after stretch breaking, wherein the tensile strength is 471MPa, the yield strength is 362MPa, and the elongation is 16.8%.
FIG. 1 is a microscopic TEM photograph of an aluminum alloy scale 1 μm prepared in example one and having both high strength and high toughness; in the alloy structure, fine points, linear structures and a small amount of spherical precipitated phases are observed in the alloy structure according to fig. 1, and the precipitated phases are respectively a T phase (a large rod shape) precipitated in a homogeneous fire process and an S phase (a tiny point shape) and a theta phase (a tiny rod shape) precipitated in a natural aging process;
FIG. 2 is a microscopic TEM photograph of a rolled alloy sheet ruler 500nm prepared in the first step of the example; FIG. 3 is a T-phase microscopic TEM photograph of an aluminum alloy having both high strength and high toughness prepared in example one; the round bar-shaped T phase near the grain boundary inside the alloy can be observed by the graph in FIG. 2, the size of the T phase is about 300 nm-400 nm, the graph in FIG. 3 is a microscopic photograph of the T phase precipitated in the internal homogeneous fire process of the alloy after natural aging treatment, the size of the T phase is 300 nm-400 nm, and the influence on coarsening of the T phase by adopting solution treatment in a shorter time and natural aging for a long time is not obvious; the T phase can also be used as nucleation sites for the rest of the precipitated phases in the subsequent natural aging process.
FIG. 4 is a drawing of an aluminum alloy with both high strength and high toughness prepared in example one; the tensile strength of the alloy is 471MPa, the yield strength is 362MPa, and the elongation is 16.8%.
Claims (1)
1. The aluminum alloy with high strength and high toughness is characterized by comprising, by mass, 4.2% of Cu, 0.7% of Mg, 0.43% of Mn, 0.3% of Ce, 0.03% of Ti and the balance of Al;
the aluminum alloy with high strength and high toughness is prepared by the following steps:
1. weighing:
weighing high-precision pure aluminum ingots, pure magnesium ingots, alCu40 alloy, alMn10 alloy, alCE20 alloy and aluminum titanium boron refiner according to the mass percentage of 4.2 percent of Cu, 0.7 percent of Mg, 0.43 percent of Mn, 0.3 percent of Ce, 0.03 percent of Ti and the balance of Al, and then weighing a No. 2 covering agent;
2. casting:
melting the weighed high-precision pure aluminum ingot, pure magnesium ingot, alCu40 alloy, alMn10 alloy and AlCE20 alloy, then adding an aluminum titanium boron refiner and a No. 2 covering agent, and finally stirring, standing, deslagging and casting to obtain an Al-Cu-Mg aluminum alloy ingot;
3. homogenizing:
homogenizing the Al-Cu-Mg aluminum alloy ingot for 20 hours under the condition that the temperature of the ingot is 490 ℃, discharging the ingot, air-cooling to room temperature, and finally milling the surface to obtain a homogenized ingot;
4. rolling:
heating the homogenized cast ingot, and then rolling under the conditions that the metal temperature is 380-440 ℃, the total rolling deformation is 50%, the rolling passes are 10, and the pressing amount of each pass is 5%, so as to obtain a rolled alloy plate;
5. solid solution:
trimming the rolled alloy plate, heating to the metal temperature of 500 ℃, preserving heat for 120min under the condition that the metal temperature is 500 ℃, and finally discharging and quenching to obtain a solid solution alloy plate;
6. prestretching:
stretching the solid solution alloy plate to obtain an alloy plate;
7. aging:
naturally aging the alloy plate for 1000 hours to obtain the aluminum alloy with high strength and high toughness;
the mass percentage of Cu in the AlCu40 alloy in the first step is 40%; the mass percentage of Mn in the AlMn10 alloy in the first step is 10%; the mass percentage of Ce in the AlCE20 alloy in the first step is 20%; the aluminum titanium boron refiner in the first step is AlTi5B1; the No. 2 covering agent in the step one is KCl (40%) +MgCl 2 (45％)+BaCl 2 (15％)；
The mass ratio of the No. 2 covering agent to the total mass of Cu, mg, mn, ce, ti and Al in the step one is 0.004:1;
the melting in the second step is specifically smelting for 20min under the condition that the furnace temperature is 750 ℃; stirring, standing, deslagging and casting, wherein the stirring, standing, deslagging and casting are carried out according to the following steps: stirring for 3min at 750 ℃ and stirring speed of 100rpm, standing for 10min after stirring, then repeatedly stirring and standing for 2 times, deslagging at 700-720 ℃, and finally casting;
the milling of the surface in the third step is performed until no obvious defect exists on the surface;
the heating treatment in the fourth step is to keep the temperature for 2 hours under the condition that the furnace temperature is 600 ℃;
the thickness of the rolled alloy plate in the fourth step is 28mm;
the amount of pretension during the stretching treatment in the sixth step was 2%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211226847.2A CN115584417B (en) | 2022-10-09 | 2022-10-09 | Aluminum alloy with high strength and high toughness and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211226847.2A CN115584417B (en) | 2022-10-09 | 2022-10-09 | Aluminum alloy with high strength and high toughness and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115584417A CN115584417A (en) | 2023-01-10 |
| CN115584417B true CN115584417B (en) | 2023-11-10 |
Family
ID=84779264
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211226847.2A Active CN115584417B (en) | 2022-10-09 | 2022-10-09 | Aluminum alloy with high strength and high toughness and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115584417B (en) |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106591649A (en) * | 2016-12-14 | 2017-04-26 | 沈阳工业大学 | High-strength Al-Cu-Mg-Mn-Er wrought aluminum alloy and preparation method thereof |
| CN106978555A (en) * | 2016-11-28 | 2017-07-25 | 佛山市尚好门窗有限责任公司 | A kind of shock resistance aluminum alloy materials |
| CN109136697A (en) * | 2018-08-28 | 2019-01-04 | 兰州飞行控制有限责任公司 | A kind of high intensity aluminum bronze line aluminium alloy |
| 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 |
| CN113373356A (en) * | 2021-06-21 | 2021-09-10 | 哈尔滨工程大学 | Al-Zn-Mg-Cu-Re aluminum alloy and preparation method thereof |
| CN114574740A (en) * | 2020-12-02 | 2022-06-03 | 通用汽车环球科技运作有限责任公司 | Aluminum alloy for casting and additive manufacturing of engine components for high temperature applications |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2121997B2 (en) * | 2007-03-14 | 2016-08-24 | Aleris Aluminum Koblenz GmbH | Ai-cu alloy product suitable for aerospace application |
| EP3821051B1 (en) * | 2018-10-31 | 2023-05-10 | Novelis Koblenz GmbH | Method of manufacturing a 2x24-series aluminium alloy plate product having improved fatigue failure resistance |
-
2022
- 2022-10-09 CN CN202211226847.2A patent/CN115584417B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106978555A (en) * | 2016-11-28 | 2017-07-25 | 佛山市尚好门窗有限责任公司 | A kind of shock resistance aluminum alloy materials |
| CN106591649A (en) * | 2016-12-14 | 2017-04-26 | 沈阳工业大学 | High-strength Al-Cu-Mg-Mn-Er wrought aluminum alloy and preparation method thereof |
| CN109136697A (en) * | 2018-08-28 | 2019-01-04 | 兰州飞行控制有限责任公司 | A kind of high intensity aluminum bronze line aluminium alloy |
| 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 |
| CN114574740A (en) * | 2020-12-02 | 2022-06-03 | 通用汽车环球科技运作有限责任公司 | Aluminum alloy for casting and additive manufacturing of engine components for high temperature applications |
| CN113373356A (en) * | 2021-06-21 | 2021-09-10 | 哈尔滨工程大学 | Al-Zn-Mg-Cu-Re aluminum alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN115584417A (en) | 2023-01-10 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP3194742B2 (en) | Improved lithium aluminum alloy system | |
| EP0610006A1 (en) | Superplastic aluminum alloy and process for producing same | |
| CN112063883B (en) | Aluminum bronze and preparation method thereof | |
| EP1945825A1 (en) | Al-cu-mg alloy suitable for aerospace application | |
| CN112626401B (en) | 2XXX series aluminum alloy and preparation method thereof | |
| CN112626386B (en) | High-strength corrosion-resistant Al-Mg-Si-Cu aluminum alloy and preparation method and application thereof | |
| CN110592444A (en) | 700-doped 720 MPa-strength heat-resistant high-intergranular corrosion-resistant aluminum alloy and preparation method thereof | |
| CN112391562B (en) | Aluminum alloy and preparation method thereof | |
| CN111492074A (en) | Improved method for producing aluminium-copper-lithium alloy plates for the production of aircraft fuselages | |
| CN111020321B (en) | Al-Cu series casting alloy suitable for forging processing and preparation method thereof | |
| CN100482834C (en) | Easily-workable magnesium alloy and method for preparing same | |
| CN113373356B (en) | Al-Zn-Mg-Cu-Re aluminum alloy and preparation method thereof | |
| CN112522552B (en) | Corrosion-resistant aluminum alloy and preparation method and application thereof | |
| CN111471901B (en) | Aluminium-manganese alloy and its production method | |
| JP7184257B2 (en) | Aluminum alloy material, manufacturing method thereof, and impeller | |
| CN112626384A (en) | Aluminum alloy with medium strength and high plasticity as well as preparation method and application thereof | |
| CN115584417B (en) | Aluminum alloy with high strength and high toughness and preparation method thereof | |
| CN108796318B (en) | High-strength and high-toughness near-eutectic aluminum-silicon-copper-magnesium alloy and preparation method thereof | |
| CN114369776B (en) | Method for improving strength of (Ce + Yb) composite modified hypoeutectic Al-Si-Mg-Cu-Cr alloy | |
| CN112646997B (en) | Scandium-containing ultrahigh-strength aluminum alloy for aerospace and manufacturing method thereof | |
| CN115449683A (en) | Magnesium alloy and preparation method thereof | |
| CN112322947B (en) | High-strength plastic Al-Mg-Si-Zn alloy for automobile and preparation method thereof | |
| CN114686735A (en) | Wrought aluminum alloy with gradient structure and preparation method thereof | |
| CN117821813B (en) | Aluminum alloy material for auxiliary frame of automobile and preparation method | |
| CN115478197B (en) | Complex-phase reinforced aluminum alloy based on 2xxx series aluminum alloy and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |