CN112626401B - 2XXX series aluminum alloy and preparation method thereof - Google Patents
2XXX series aluminum alloy and preparation method thereof Download PDFInfo
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Abstract
The invention relates to a 2XXX series aluminum alloy and a preparation method thereof, belongs to the technical field of non-ferrous metal alloys, and solves the problems of low strength and poor toughness of the 2XXX series aluminum alloy in the prior art. The 2XXX series aluminum alloy comprises the following chemical components in percentage by mass: cu: 3.9-4.5%, Mg: 0.5 to 1.0%, Mn: 0.5-1.2%, Si: 0.3-0.8%, Zr: 0.1-0.2 percent of Ti, less than or equal to 0.1 percent of Fe, less than or equal to 0.4 percent of Zn, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurities and the balance of Al. The preparation method of the 2XXX series aluminum alloy comprises the following steps of 1: weighing pure Al, Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy and Al-Zr intermediate alloy as raw materials according to the mass percent of each element; step 2: refining the raw materials to obtain an aluminum alloy smelting solution, and casting into an ingot; and step 3: and homogenizing, forging, carrying out solid solution treatment and aging treatment on the cast ingot in sequence to obtain the 2XXX series aluminum alloy. The invention improves the strength and toughness of the 2XXX series aluminum alloy.
Description
Technical Field
The invention belongs to the technical field of non-ferrous metal alloys, and particularly relates to a 2XXX series aluminum alloy and a preparation method thereof.
Background
The 2XXX series aluminum alloy belongs to the aging-strengthening aluminum alloy with medium strength, has the advantages of low density, high strength, good corrosion resistance and the like, and is widely applied to the fields of aerospace, ocean, automobile, rail transit and the like. The aluminum alloy is used as a first-choice material for light weight, and along with increasingly strict requirements on energy conservation and emission reduction, higher requirements are put forward on the performance of the aluminum alloy.
The main strengthening phase of the Al-Cu-Mg-Si alloy in the 2XXX series aluminum alloy is theta' (Al)2Cu) phase and S' (Al)2CuMg) phase and beta' (Mg)2Si) phase, in order to improve the strength of 2XXX series aluminum alloys, technologists generally focus on the deformation process and heat treatment of 2XXX aluminum alloys, such as various extrusion or forging processes to improve the strength of the material, and study the precipitation strengthening caused by the aluminum alloy by regulating the size and distribution state of the nanoscale precipitation phase in the heat treatment process, thereby improving the strength of the aluminum alloy. However, the toughness of the aluminum alloy is reduced while the strength of the aluminum alloy is improved, and the improvement of the performance of the aluminum alloy by the double measures of optimizing the content of alloy elements in the 2XXX series aluminum alloy and adding other metal elements is not related in the prior art.
Disclosure of Invention
In view of the above analysis, embodiments of the present invention are directed to a 2XXX series aluminum alloy and a preparation method thereof, so as to solve the problems of low strength and poor toughness of the existing 2XXX series aluminum alloy.
The invention is realized by the following technical scheme:
in one aspect, the invention provides a 2XXX series aluminum alloy, wherein the 2XXX series aluminum alloy comprises the following chemical components in percentage by mass: cu: 3.9-4.5%, Mg: 0.5 to 1.0%, Mn: 0.5-1.2%, Si: 0.3-0.8%, Zr: 0.1-0.2 percent of Ti, less than or equal to 0.1 percent of Fe, less than or equal to 0.4 percent of Zn, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurities and the balance of Al.
Further, the chemical components of the 2XXX series aluminum alloy are as follows according to the mass percentage: cu: 4.2-4.3%, Mg: 0.61-0.73%, Mn: 0.76 to 0.86%, Si: 0.34-0.6%, Zr: 0.15-0.2 percent of Ti, less than or equal to 0.1 percent of Fe, less than or equal to 0.4 percent of Zn, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurities and the balance of Al.
Further, the ratio of the content of the Cu element to the content of the Mg element is between 4 and 8.
Further, Al is precipitated from 2XXX series aluminum alloy3Zr, S' phase and S phase, Al3Zr and S' phases are uniformly distributed in the crystal, and the S phase is precipitated in the crystal boundary.
Further, the size of the S phase is 0.2-0.5 um.
In another aspect, the present invention provides a method for preparing a 2XXX series aluminum alloy, for preparing the 2XXX series aluminum alloy described above, comprising the steps of:
step 1: weighing pure Al, Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy and Al-Zr intermediate alloy as raw materials according to the mass percent of each element;
step 2: refining the raw materials to obtain an aluminum alloy smelting solution, and casting into an ingot;
and step 3: and carrying out homogenization treatment, forging, solution treatment and aging treatment on the cast ingot in sequence to obtain the 2XXX series aluminum alloy.
Further, in step 2, the refining step comprises:
step 21: melting pure Al at 700-750 ℃;
step 22: sequentially adding an Al-Cu intermediate alloy, an Al-Si intermediate alloy, an Al-Mn intermediate alloy, an Al-Mg intermediate alloy, a covering agent and a refining agent, and carrying out primary smelting to obtain primary smelting liquid;
step 23: adding Al-Zr intermediate alloy into the primary smelting liquid for secondary smelting to obtain secondary smelting liquid.
Further, in the step 23, the secondary smelting liquid is kept standing for 0.5-1 h at 690-710 ℃.
Further, in step 2, casting into an ingot comprises: and casting the obtained aluminum alloy smelting liquid at 710-730 ℃, under the water pressure of 0.02-0.05 MPa and at the speed of 40-60 mm/min to obtain an as-cast ingot with the diameter of 130-170 mm and the length of 400-800 mm.
Further, in the step 3, the homogenization treatment temperature is 480-530 ℃, and the time is 12-24 hours.
Further, in step 3, after the homogenizing treatment, before the forging, the method further comprises:
machining the cast ingot in the homogenized and annealed state to obtain a round bar with the diameter of 120-160 mm and the length of 300-700 mm, heating the machined round bar to 450-480 ℃, and preserving heat for 2-4 hours.
Further, in the step 3, the forging temperature is 450-480 ℃, and the deformation is 70-90%.
Further, in the step 3, the forging speed is 1-10 mm/s.
Further, in the step 3, the temperature of the solution treatment is 500-540 ℃ and the time is 1-2 h.
Further, in step 3, the steel sheet is taken out of the furnace and cooled by water after the solution treatment.
Further, in the step 3, the aging treatment temperature is 150-190 ℃ and the time is 6-24 h.
Compared with the prior art, the invention can at least realize one of the following beneficial effects:
1. according to the invention, the Cu participates in the S' phase (Al) of the strengthening phase by accurately adjusting the content of Cu to be 3.9-4.5%2CuMg), effectively improvesThe hardness and the strength of the 2XXX series aluminum alloy, and simultaneously, the industrial application requirements can be met, the industrial low cost can be effectively reduced, and the requirements of light-weight application can be met.
2. According to the invention, through the component design of the 2XXX series aluminum alloy, the contents of Mg and Si are accurately adjusted from the aspects of dispersion strengthening and fine grain strengthening, the content of Mg is 0.5-1.0%, the content of Si is 0.3-0.8%, so that a strengthening phase S phase is generated in the 2XXX series aluminum alloy as far as possible, the size of the S phase is 0.2-0.5 um, and the tensile strength of the 2XXX series aluminum alloy after natural aging and artificial aging is improved.
3. The invention introduces Zr element into 2XXX series aluminum alloy to refine the as-cast structure of the alloy, and Zr is Al3Constituent element of Zr, Al3The precipitation of Zr can refine the grain structure, achieve the effect of fine grain strengthening, and improve the comprehensive performance of the 2XXX series aluminum alloy.
4. The 2XXX series aluminum alloy ingot prepared by the method is subjected to homogenization, forging, solution treatment and aging treatment in sequence, the room-temperature tensile strength of the obtained alloy material is 520-550 MPa, the yield strength is 350-370 MPa, and the elongation after fracture is 15-20%.
5. The 2XXX series aluminum alloy and the preparation method thereof provided by the invention have the advantages of simple operation, obvious strength improvement effect, shortened production period and practical application value in industrial production, and the aluminum alloy material prepared by the invention can be widely applied to heavy forgings, thick plates, airplane structural members, wheels, truck frames, suspension system parts and the like.
In the invention, the technical schemes can be combined with each other to realize more preferable combination schemes. Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objectives and other advantages of the invention will be realized and attained by the structure particularly pointed out in the written description and drawings.
Drawings
The drawings are only for purposes of illustrating particular embodiments and are not to be construed as limiting the invention, wherein like reference numerals are used to designate like parts throughout.
FIG. 1 is a microscopic SEM image of a 2XXX series aluminum alloy specimen of example 1 without homogenization treatment;
FIG. 2 is a microscopic SEM image of a 2XXX series aluminum alloy sample of example 1 after homogenization treatment;
FIG. 3 is a microscopic TEM image of an aged 2XXX series aluminum alloy sample of example 1;
FIG. 4 is a microscopic TEM image of the aged 2XXX series aluminum alloy sample of example 1 (II).
Detailed Description
The accompanying drawings, which are incorporated in and constitute a part of this application, illustrate preferred embodiments of the invention and together with the description, serve to explain the principles of the invention and not to limit the scope of the invention.
The invention provides a 2XXX series aluminum alloy, which comprises the following chemical components in percentage by mass: cu: 3.9-4.5%, Mg: 0.5 to 1.0%, Mn: 0.5-1.2%, Si: 0.3-0.8%, Zr: 0.1-0.2 percent of Ti, less than or equal to 0.1 percent of Fe, less than or equal to 0.4 percent of Zn, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurities and the balance of Al.
Further, the 2XXX series aluminum alloy comprises the following chemical components in percentage by mass: cu: 4.2-4.3%, Mg: 0.61-0.73%, Mn: 0.76 to 0.86%, Si: 0.34-0.6%, Zr: 0.15-0.2 percent of Ti, less than or equal to 0.1 percent of Fe, less than or equal to 0.4 percent of Zn, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurities and the balance of Al.
The effect of the elements in the 2XXX series aluminium alloy is as follows:
cu: in Al-Cu-Mg aluminum alloys, Cu is mainly responsible for participating in the strengthening phase theta' phase (Al)2Cu) and S' phase (Al)2CuMg), and if the amount of Cu atoms added is too large, the excessive Cu atoms will bond with Fe atoms in the alloy to form coarse precipitated phase Al7Cu2Fe, the precipitated phase being a brittle phase, the presence of which imparts a large degree of fracture toughness to the alloyThe degree is reduced, and the precipitated phase is easy to cause overburning during solution treatment, so that the mechanical property and the corrosion resistance of the alloy are reduced. In addition, the addition of excessive Cu element to the alloy increases the alloy density, and does not meet the requirement of weight reduction of automobiles. Therefore, the Cu content of the 2XXX series aluminum alloy provided by the invention is selected to be within the range of 3.9-4.5%.
Mg: mg is a component element of a precipitation strengthening phase S phase in the Al-Cu-Mg alloy, and can improve the tensile strength and the yield strength of the Al-Cu-Mg alloy after natural aging and artificial aging, but the addition of Mg can also reduce the elongation of the alloy. When the content of Mg element is lower, the main precipitation phase during alloy aging is theta' phase; when the mass fraction of Mg is more than 0.2 percent and the mass fraction of Si is less than 0.6 percent, an S phase can be formed in the alloy; when the Si content is large, Mg atoms are all bonded with Si, and Mg is precipitated in the alloy2A Si phase. Therefore, the Mg content of the 2XXX series aluminum alloy provided by the invention is selected to be within the range of 0.5-1.0%.
Mn: the Mn element is added mainly to eliminate the harmful effect of Fe, and the existence of Mn can improve the corrosion resistance of the alloy. After the microalloy element Mn is added into the alloy, the recrystallization temperature of the alloy is obviously improved, so that the alloy is difficult to recrystallize in the hot processing process of the alloy, such as hot rolling. The Mn content of the 2XXX series aluminum alloy provided by the invention is selected within the range of 0.5-1.2%.
Si: an appropriate amount of Si element is added, and a fine GPB region with uniform distribution containing Si is precipitated in The matrix at The initial stage of The aging treatment, which is called as The Si-modified GPB (GPB region improved by Si). Due to the existence of the GPB area, the S phase precipitated in the aging treatment process of the alloy is smaller in size and more dispersed in distribution. Therefore, the Si content of the 2XXX series aluminum alloy provided by the invention is selected to be within the range of 0.3-0.8%.
Zr: zr can refine the as-cast structure of the alloy, produce fine-grain strengthening effect and improve the forming performance of the material. While Zr is Al3Constituent element of Zr, Al3The precipitation of Zr can refine the grain structure, achieve the function of fine grain strengthening and improve the comprehensive performance of the material. The Zr content of the 2XXX series aluminum alloy provided by the invention is selected0.1-0.2%.
Further, in the present invention, Al is precipitated from the 2XXX series aluminum alloy3Zr, S' phase and S phase, Al3Zr and S' phases are uniformly distributed in the crystal, and the S phase is precipitated in the crystal boundary.
Al3The precipitation of Zr can refine the grain structure, achieve the effect of fine grain strengthening, improve the comprehensive performance of the material, simultaneously, S' phase dispersed and uniformly distributed in the aluminum alloy and S phase precipitated at the grain boundary have good strengthening effect, and can improve the mechanical property of the aluminum alloy.
In another aspect, the present invention provides a method for preparing a 2XXX series aluminum alloy, comprising the steps of:
step 1: weighing pure Al, Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy and Al-Zr intermediate alloy as raw materials according to the mass percent of each element;
step 2: refining the raw materials to obtain an aluminum alloy smelting solution, and casting the aluminum alloy smelting solution into an ingot;
melting pure Al at 700-750 ℃, sequentially adding an Al-Cu intermediate alloy, an Al-Si intermediate alloy, an Al-Mn intermediate alloy, an Al-Mg intermediate alloy, a covering agent and a refining agent, carrying out primary melting to obtain a primary molten liquid, then adding an Al-Zr intermediate alloy, carrying out secondary melting to obtain a secondary molten liquid, and cooling and standing for 0.5-1 h at the temperature of 690-710 ℃. And then, casting the obtained aluminum alloy smelting liquid at 710-730 ℃, under the water pressure of 0.02-0.05 MPa and at the speed of 40-60 mm/min to obtain an as-cast ingot with the diameter of 130-170 mm and the length of 400-800 mm.
It is noted that in the process of primary smelting, in order to reduce Mg burning loss, Al-Mg master alloy is added finally. The secondary smelting is to add Zr which is a rare element and further refine the aluminum alloy.
And step 3: carrying out homogenization, forging, solution treatment and aging treatment on the cast ingot in sequence to obtain the 2XXX series aluminum alloy;
and (3) carrying out homogenizing annealing treatment on the cast ingot at 480-530 ℃, keeping the temperature for 12-24 h, and cooling in the air after discharging.
It should be noted that, in order to eliminate or reduce component segregation, dendritic structure and low melting point non-equilibrium eutectic phase in the ingot and to make solute atoms inside and outside the crystal uniformly distributed, the homogenization treatment temperature in the preparation method of the 2XXX series aluminum alloy provided by the invention is 480-530 ℃, and the time is 12-24 h.
And machining the ingot in the homogenized and annealed state to obtain a round bar with the diameter of 120-160 mm and the length of 300-700 mm. And heating the machined round bar to 450-480 ℃, and preserving heat for 2-4 hours. Heating the die to 450-480 ℃, and forging and pressing the round rod at a forging and pressing speed of 1-10 mm/s, wherein the deformation of the round rod is 70-90%.
The forging pressure is reduced as much as possible under the condition that the alloy grains are not grown, the equipment can be tested, the energy is saved, and the defects of holes, inclusion and the like in the alloy in the deformation process are reduced, wherein the forging temperature is 450-480 ℃, and the deformation is 70-90% in the preparation method of the 2XXX series aluminum alloy.
Heating the obtained forged and pressed ingot to 500-540 ℃, carrying out solution treatment, keeping the temperature for 1-2 h, and discharging and cooling with water. And then, heating the water-cooled cast ingot to 150-190 ℃, and carrying out aging treatment for 6-24 h to obtain the 2XXX series aluminum alloy.
Example 1
The 2XXX series aluminum alloy comprises the following chemical components in percentage by mass: cu: 4.2 percent; mg: 0.73 percent; mn: 0.86 percent; si: 0.34 percent; zr: 0.15 percent; ti is less than or equal to 0.1 percent; fe is less than or equal to 0.4 percent; zn is less than or equal to 0.1 percent; the content of single impurity is less than or equal to 0.05 percent; the total impurity is less than or equal to 0.15 percent; the balance being Al.
In this embodiment, the preparation method of the 2XXX series aluminum alloy includes the steps of:
step 1: weighing pure Al, Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy and Al-Zr intermediate alloy as raw materials according to the mass percent of each element;
step 2: melting pure Al at 740 ℃, sequentially adding Al-Cu intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy, Al-Mg intermediate alloy, expanded perlite and hexachloroethane, carrying out primary melting to obtain primary molten liquid, then adding Al-Zr intermediate alloy for secondary melting to obtain secondary molten liquid, and standing the secondary molten liquid at 690 ℃ for 0.5 h. Casting the obtained aluminum alloy smelting solution at 720 ℃, the water pressure of 0.03MPa and the speed of 50mm/min to obtain an as-cast ingot with the diameter of 150mm and the length of 500 mm;
and step 3: carrying out homogenizing annealing treatment on the cast ingot at 480 ℃ for 12h, and cooling in air after discharging. The ingot in the homogenized annealed state was subjected to machining treatment to obtain a round bar having a diameter of 146mm and a length of 400 mm. Heating the machined round bar to 460 ℃, and preserving heat for 3 hours. The die was heated to 470 ℃ and the round bar was forged at a forging rate of 1mm/s, and the amount of deformation of the round bar was 80%. Heating the obtained forged and pressed ingot to 520 ℃, carrying out solid solution treatment for 2h, discharging and cooling by water. And then, heating the water-cooled cast ingot to 160 ℃, and carrying out aging treatment for 12h to obtain the 2XXX series aluminum alloy.
Example 2
A2 XXX series aluminum alloy is prepared from the following element components in percentage by mass: cu: 4.5 percent; mg: 0.61%; mn: 0.76 percent; si: 0.6 percent; zr: 0.15 percent; ti is less than or equal to 0.1 percent; fe is less than or equal to 0.4 percent; zn is less than or equal to 0.1 percent; the content of single impurity is less than or equal to 0.05 percent; the total impurity is less than or equal to 0.15 percent; the balance being Al.
In this embodiment, the preparation method of the 2XXX series aluminum alloy includes the steps of:
step 1: weighing pure Al, Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy and Al-Zr intermediate alloy as raw materials according to the mass percent of each element;
step 2: melting pure Al at 740 ℃, sequentially adding Al-Cu intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy, Al-Mg intermediate alloy, expanded perlite and hexachloroethane, carrying out primary melting to obtain primary molten liquid, then adding Al-Zr intermediate alloy for secondary melting to obtain secondary molten liquid, and standing the secondary molten liquid at 700 ℃ for 0.5 h. Casting the obtained aluminum alloy smelting solution at 720 ℃, the water pressure of 0.03MPa and the speed of 50mm/min to obtain an as-cast ingot with the diameter of 150mm and the length of 500 mm;
and step 3: carrying out homogenizing annealing treatment on the cast ingot at 520 ℃, keeping the temperature for 12h, and cooling in the air after the cast ingot is taken out of the furnace. The ingot in the homogenized annealed state was subjected to machining treatment to obtain a round bar having a diameter of 146mm and a length of 400 mm. Heating the machined round bar to 460 ℃, and preserving heat for 3 hours. The die was heated to 470 ℃ and the round bar was forged at a forging rate of 1mm/s, and the amount of deformation of the round bar was 80%. Heating the obtained forged and pressed ingot to 520 ℃, carrying out solid solution treatment for 2h, discharging and cooling by water. And then, heating the water-cooled cast ingot to 170 ℃, and carrying out aging treatment for 12h to obtain the 2XXX series aluminum alloy.
Example 3
A2 XXX series aluminum alloy is prepared from the following element components in percentage by mass: cu: 4.0 percent; mg: 1.0 percent; mn: 0.76 percent; si: 0.6 percent; zr: 0.15 percent; ti is less than or equal to 0.1 percent; fe is less than or equal to 0.4 percent; zn is less than or equal to 0.1 percent; the content of single impurity is less than or equal to 0.05 percent; the total impurity is less than or equal to 0.15 percent; the balance being Al.
In this embodiment, the preparation method of the 2XXX series aluminum alloy includes the steps of:
step 1: weighing pure Al, Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy and Al-Zr intermediate alloy as raw materials according to the mass percent of each element;
step 2: melting pure Al at 740 ℃, sequentially adding Al-Cu intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy, Al-Mg intermediate alloy, expanded graphite and hexachloroethane, carrying out primary melting to obtain primary melting liquid, then adding Al-Zr intermediate alloy for secondary melting to obtain secondary melting liquid, and standing the secondary melting liquid at 710 ℃ for 1 h. Casting the obtained aluminum alloy smelting solution at 720 ℃, the water pressure of 0.03MPa and the speed of 50mm/min to obtain an as-cast ingot with the diameter of 150mm and the length of 500 mm;
and step 3: carrying out homogenizing annealing treatment on the cast ingot at 520 ℃, keeping the temperature for 12h, and cooling in the air after the cast ingot is taken out of the furnace. The ingot in the homogenized annealed state was subjected to machining treatment to obtain a round bar having a diameter of 146mm and a length of 400 mm. Heating the machined round bar to 460 ℃, and preserving heat for 3 hours. The die was heated to 470 ℃ and the round bar was forged at a forging rate of 1mm/s, and the amount of deformation of the round bar was 80%. Heating the obtained forging-pressed ingot to 540 ℃, carrying out solid solution treatment, keeping the temperature for 2 hours, discharging and cooling by water. And then, heating the water-cooled cast ingot to 180 ℃, and carrying out aging treatment for 12h to obtain the 2XXX series aluminum alloy.
A scanning electron microscope is adopted to observe a microstructure of the 2XXX series aluminum alloy in the embodiment before homogenization treatment, as shown in figure 1, alloy grains are uniform and fine and are approximately in an equiaxial shape, a large amount of unbalanced eutectic structures exist in grain boundaries, EDS (electron-dispersive spectroscopy) analysis shows that a second phase with thicker white color mainly consists of Al, Cu and Mg and a small amount of Si and Fe elements, and serious dendrite segregation exists, and homogenization treatment is required.
When the microstructure of the 2XXX series aluminum alloy after homogenization treatment in the example is observed by using a scanning electron microscope, as shown in fig. 2, the second phase with a slender rod shape at the grain boundary is greatly reduced, and the second phase with a block shape or a strip shape at the grain boundary intersection is completely crushed and partially dissolved in the matrix, so that a good homogenization effect is obtained.
The microstructure of the 2XXX series aluminum alloy in the examples was observed using a TECNAIG220 transmission electron microscope. As can be seen from FIG. 3, Al3Zr and S' phases are uniformly precipitated and distributed. As can be seen from FIG. 4, the S phase is discontinuously distributed at the grain boundary, and the size of the S phase is 0.2-0.5 um.
TABLE 1 comparison of Performance of 2XXX series aluminum alloys of the prior art and the present invention
| Examples | Tensile strength (MPa) | Yield strength (MPa) | Elongation after Break (%) |
| 1 | 526 | 350 | 19 |
| 2 | 539 | 366 | 17.5 |
| 3 | 540 | 363 | 20 |
| Prior Art | ≤495 | 290～410 | ≤12 |
Table 1 shows the comparison of the properties of the 2XXX series aluminum alloys in the prior art and the invention, and it can be seen from Table 1 that the 2XXX series aluminum alloys in examples 1-3 have a tensile strength of 526 to 540MPa, a yield strength of 350 to 366MPa, and an elongation after fracture of 17.5 to 20%. In the prior art, the tensile strength of the 2XXX series aluminum alloy is below 495MPa, the yield strength is 290-410 MPa, and the elongation after fracture is below 12%. The strength and toughness of the 2XXX series aluminum alloy prepared by the method are obviously improved.
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any changes or substitutions that can be easily conceived by those skilled in the art within the technical scope of the present invention are included in the scope of the present invention.
Claims (9)
1. The 2XXX series aluminum alloy is characterized by comprising the following chemical components in percentage by mass: cu: 4.2-4.3%, Mg: 0.61-0.73%, Mn: 0.76 to 0.86%, Si: 0.34-0.6%, Zr: 0.15-0.2 percent of Ti, less than or equal to 0.1 percent of Fe, less than or equal to 0.4 percent of Zn, less than or equal to 0.05 percent of single impurity, less than or equal to 0.15 percent of total impurities and the balance of Al; the ratio of the content of the Cu element to the content of the Mg element is between 4 and 8;
the 2XXX series aluminum alloy is prepared by the following preparation method:
step 1: weighing pure Al, Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy and Al-Zr intermediate alloy as raw materials according to the mass percent of each element;
step 2: refining the raw materials to obtain an aluminum alloy smelting solution, and casting into an ingot;
and step 3: carrying out homogenization treatment, forging, solution treatment and aging treatment on the cast ingot in sequence to obtain the 2XXX series aluminum alloy;
in the step 2, the refining step comprises:
step 21: melting pure Al at 700-750 ℃;
step 22: sequentially adding an Al-Cu intermediate alloy, an Al-Si intermediate alloy, an Al-Mn intermediate alloy, an Al-Mg intermediate alloy, a covering agent and a refining agent, and carrying out primary smelting to obtain primary smelting liquid;
step 23: adding Al-Zr intermediate alloy into the primary smelting liquid for secondary smelting to obtain secondary smelting liquid;
in the step 3, the forging temperature is 450-480 ℃, and the deformation is 70-90%;
precipitating Al from the 2XXX series aluminum alloy3Zr, S' phase and S phase, Al3Zr and S' phases are uniformly distributed in the crystal, and the S phase is precipitated in the crystal boundary; the size of the S phase is 0.2-0.5 um.
2. The 2XXX series aluminum alloy of claim 1, wherein the Cu: 4.2 percent; mg: 0.73 percent; mn: 0.86 percent; si: 0.34 percent; zr: 0.15 percent; ti is less than or equal to 0.1 percent; fe is less than or equal to 0.4 percent; zn is less than or equal to 0.1 percent; the content of single impurity is less than or equal to 0.05 percent; the total impurity is less than or equal to 0.15 percent; the balance being Al.
3. The 2XXX series aluminum alloy of claim 1, wherein the S phase is present in an interrupted distribution at the grain boundaries.
4. A method of producing a 2XXX series aluminum alloy, for use in producing the 2XXX series aluminum alloy of any of claims 1-3, the steps comprising:
step 1: weighing pure Al, Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Si intermediate alloy, Al-Mn intermediate alloy and Al-Zr intermediate alloy as raw materials according to the mass percent of each element;
step 2: refining the raw materials to obtain an aluminum alloy smelting solution, and casting into an ingot;
and step 3: carrying out homogenization treatment, forging, solution treatment and aging treatment on the cast ingot in sequence to obtain the 2XXX series aluminum alloy;
in the step 2, the refining step comprises:
step 21: melting pure Al at 700-740 ℃;
step 22: sequentially adding an Al-Cu intermediate alloy, an Al-Si intermediate alloy, an Al-Mn intermediate alloy, an Al-Mg intermediate alloy, a covering agent and a refining agent, and carrying out primary smelting to obtain primary smelting liquid;
step 23: adding Al-Zr intermediate alloy into the primary smelting liquid for secondary smelting to obtain secondary smelting liquid;
in the step 3, the homogenization treatment temperature is 480-530 ℃, and the time is 12-24 hours; the forging temperature is 450-470 ℃, and the deformation is 70-90%; the solution treatment temperature is 500-540 ℃, and the time is 1-2 h; the aging treatment temperature is 150-190 ℃, and the time is 6-24 h.
5. The method of claim 4, wherein in step 2, the refining step comprises:
step 21: melting pure Al at 740 ℃;
step 22: sequentially adding an Al-Cu intermediate alloy, an Al-Si intermediate alloy, an Al-Mn intermediate alloy, an Al-Mg intermediate alloy, a covering agent and a refining agent, and carrying out primary smelting to obtain primary smelting liquid;
step 23: adding Al-Zr intermediate alloy into the primary smelting liquid for secondary smelting to obtain secondary smelting liquid.
6. The method of claim 4, wherein the homogenization treatment temperature in step 3 is 480-520 ℃ and the time is 12-24 hours.
7. The method of claim 4, wherein in step 3, the forging temperature is 450-470 ℃ and the deformation is 70-80%.
8. The method of claim 4, wherein in step 3, the solution treatment temperature is 520-540 ℃ and the time is 1-2 hours.
9. The method for preparing a 2XXX series aluminum alloy according to claim 4, wherein the aging treatment temperature in step 3 is 160-190 ℃ for 6-24 h.
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