CN114990392B - High-performance and high-temperature-resistant Al-Mg-Si aluminum alloy and preparation method thereof - Google Patents
High-performance and high-temperature-resistant Al-Mg-Si aluminum alloy and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a high-performance and high-temperature-resistant Al-Mg-Si series aluminum alloy and a preparation method thereof, wherein the aluminum alloy comprises the following components in percentage by mass: mg:0.91-1.10%; si:1.21 to 1.4 percent; mn:0 to 0.2 percent; zr:0 to 0.2 percent; ag:0 to 0.05 percent; the total amount of inevitable impurities is less than or equal to 0.20 percent; the balance being Al. The preparation method of the aluminum alloy comprises the following steps: smelting, casting and rolling, homogenizing, cold rolling, solid solution and artificial aging. The Al-Mg-Si aluminum alloy obtained by the invention has higher mechanical property, can keep higher mechanical property under the condition of long-term high temperature, and has long service life.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy preparation, and particularly relates to a high-performance and high-temperature-resistant Al-Mg-Si series aluminum alloy and a preparation method thereof.
Background
The Al-Mg-Si series (6 series) aluminum alloy has the characteristics of low density, excellent processing performance, mechanical performance, high corrosion resistance and the like, and is the most extensive and indispensable non-ferrous metal structural material in the manufacturing of parts in the field of transportation. With the increasing demand of aluminum alloys in the field of automotive applications, higher requirements are put forward on the performance and working environment of aluminum alloys.
The major automobile manufacturers at home and abroad set corresponding standards for the long-term thermal stability of the respective automobile aluminum alloy products. The standard requirements of the aluminum alloy applied to the parts around the automobile engine at present are as follows: after heating for 1000h at 150 ℃, the yield strength is more than or equal to 305MPa. However, after the Al-Mg-Si series aluminum alloy section produced by the prior art is heated for 1000 hours at 150 ℃, the yield strength is usually 250-275MPa.
For example, patent CN111014332B discloses a "6-series high alloy composition with high long-term thermal stability and preparation method" the 6-series aluminum alloy disclosed in the patent comprises the following components in percentage by mass: si:0.65%, fe:0.10%, cu:0.08%, mn:0.23%, mg:0.58%, V:0.09%; cr:0.17 percent; ti:0.07 percent; sum of unavoidable impurities: 0.03 percent; the balance being Al. The preparation method of the aluminum alloy comprises the following steps: smelting, homogenizing, extruding, quenching, stretching and straightening and two-stage artificial aging. The yield strength of the alloy is 278MPa, and after the alloy is heated at 150 ℃ for 1000 hours, the yield strength is reduced to 251MPa, and the yield strength is reduced by 27MPa. In a journal paper entitled "precision screening and mechanical properties in 6082 aluminum alloy long-term thermal exposure" published by Li et al, the selected material is commercial 6082 aluminum alloy, and the mass percentages of the components are as follows: si:1.19%, mg:0.75%, mn:0.68%, fe:0.18%, cr:0.048%, zn:0.032%, cu:0.027%, ti:0.025% and the balance of Al. After the commercial 6082 aluminum alloy is subjected to solid solution, quenching and artificial aging, the yield strength can reach-330 MPa, but after the commercial 6082 aluminum alloy is heated at 150 ℃ for 1000 hours, the yield strength is only-255 MPa, and the yield strength is reduced to-75 MPa.
In conclusion, al-Mg-Si series aluminum alloy produced by the prior art cannot synchronously realize high performance and high-temperature long-time stability, namely the performance of the initial aluminum alloy is higher, but the performance of the material is obviously reduced and the thermal stability is poor after the material is heated for 1000 hours at 150 ℃, so that the material is heated to deform and lose efficacy, the service life is greatly reduced, the long-term use of the aluminum alloy in a heating environment is difficult to meet, and the requirements of customers and the requirements of the current market are difficult to meet; in addition, the prior art discloses that the performance of the aluminum alloy is obviously reduced after the aluminum alloy is heated at 150 ℃ for 1000 hours, which is also a technical problem which is difficult to solve at present.
Therefore, how to effectively inhibit the reduction of the yield strength of the Al-Mg-Si series aluminum alloy placed at high temperature for a long time and obtain the high-performance and high-temperature-resistant Al-Mg-Si series aluminum alloy is a technical problem to be solved urgently at present.
Disclosure of Invention
In order to solve the technical problem, the invention provides a high-performance and high-temperature-resistant Al-Mg-Si series aluminum alloy which comprises the following components in percentage by mass: mg:0.91-1.10%; si:1.21 to 1.4 percent; mn:0 to 0.2 percent; zr:0 to 0.2 percent; ag:0 to 0.05 percent; the total amount of inevitable impurities is less than or equal to 0.20 percent; the balance of Al; the preparation method of the aluminum alloy comprises the following steps:
(1) Under protective gas, sequentially adding pure Al, al-Si intermediate alloy, al-Zr intermediate alloy, al-Mn intermediate alloy, pure Ag and pure Mg into a smelting furnace for heating and melting, then cooling, carrying out heat preservation treatment, and then obtaining an aluminum alloy melt after stirring, refining, degassing and slag removal, wherein the heating and melting temperature is as follows: 700-780 ℃, and the heat preservation treatment comprises the following steps: keeping the temperature at 700-750 ℃ for 10-60min;
(2) And (2) guiding the aluminum alloy melt obtained in the step (1) into a water-cooling copper roller gap for sub-rapid solidification casting rolling, and then carrying out step homogenization heat treatment, multi-pass cold rolling, solid solution heat treatment, quenching and artificial aging treatment to obtain the high-performance and high-temperature-resistant Al-Mg-Si series aluminum alloy.
Further, the protective gas in the step (1) is argon or a mixed gas of carbon dioxide and sulfur hexafluoride; the volume ratio of the carbon dioxide to the sulfur hexafluoride is 85-90.
Further, the heating and melting temperature in the step (1) is as follows: 740 to 760 ℃.
Further, the heat preservation treatment in the step (1) comprises the following steps: keeping the temperature at 710-730 ℃ for 15-40min.
Further, the roll gap distance of the water-cooled copper roller in the step (2) is 2-4.5mm, the linear speed of the water-cooled copper roller is 5-15m/min, and the sub-rapid solidification is as follows: the cooling rate is 300-500K/s.
Further, the step homogenizing heat treatment in the step (2) is as follows: keeping the temperature at 450-460 ℃ for 2-5h, and keeping the temperature at 540-560 ℃ for 2-5h.
Further, the multi-pass cold rolling in the step (2) comprises the following steps: 4-8 times of cold rolling, and the total reduction is 65-80%.
Further, the solution heat treatment in the step (2) is: preserving the heat for 5-30min at 550-560 ℃.
Further, the artificial aging treatment in the step (2) comprises the following steps: keeping the temperature at 175-190 ℃ for 3-8h.
Compared with the prior art, the invention has the following characteristics:
(1) Compared with the prior art, the Al-Mg-Si aluminum alloy has higher mechanical property through the interaction among alloy components and the synergistic effect of the process, can keep the higher mechanical property under the long-term heating condition, can be widely applied to the field of manufacturing of automobile parts, and reduces the production cost. The technical difficulty that the prior art is difficult to solve is: firstly, in order to obtain high-performance Al-Mg-Si series aluminum alloy in the prior art, a mode of adding a refiner to refine a second phase in the alloy preparation process is usually adopted to improve the material strength, so that the production cost of the alloy is obviously improved; secondly, the precipitation strengthening second phase of the Al-Mg-Si series aluminum alloy obtained in the prior art is mainly beta phase (Mg) 2 Si), the size of the phase is generally large and the distribution is broad (average diameter: 100nm-5 μm) which results in a material having a low initial yield strength, and further, in order to suppress a decrease in yield strength of the Al — Mg — Si-based alloy during a long-time treatment at high temperature, it is generally a strategy to suppress further coarsening of the β phase.
(2) The invention has the creativity that: the invention omits the addition of a refiner through the interaction between alloy components and the synergistic effect of the process, so that the Al-Mg-Si series aluminum alloy is mainly in a beta' phase (Mg) which is finer than that of the prior art 5 Si 6 ) The second phase is strengthened mainly for precipitation, but under the environment of long-term heating, the phase will be dissolved and coarsened, and further converted into beta' phase (Mg) 9 Si 5 ) And beta phase (Mg) 2 Si), which results in a substantial reduction in the strength of the alloy; while the invention breaks throughThe bottleneck of the technology effectively avoids the dissolution and coarsening of the beta ' phase and inhibits the transformation of the beta ' phase to the beta ' phase and the beta phase. And the following excellent effects are obtained through the interaction between elements and the synergistic effect of the process: firstly, a precipitation strengthening phase beta' (Mg) with smaller fineness, even dispersion and narrower size distribution is formed 5 Si 6 ): the average size is: the diameter is 1-1.2nm, the length is 10-12nm, so that the alloy has high mechanical property; and secondly, the transformation of beta 'opposite beta' phase and beta phase is effectively inhibited, and the initial mechanical property of the alloy is ensured to be higher, and the alloy can still keep better mechanical property under long-time high-temperature placement. In conclusion, the invention effectively reduces the production cost of the alloy under the condition of not adding a refiner, forms a fine, uniformly dispersed and narrow-size distribution precipitation strengthening phase beta' phase through the interaction between elements, effectively improves the initial mechanical property of the material and can still maintain higher mechanical property under long-time high-temperature placement.
(3) Compared with the prior art, the invention has the following advantages through the interaction between alloy components and the synergistic effect of the process: the microstructure of the Al-Mg-Si series aluminum alloy obtained by the invention has finer and more evenly distributed precipitation strengthening phase beta' (average size: diameter is 1-1.2nm, length is 10-12 nm). The aluminum alloy obtained by the invention not only can obtain higher mechanical property, wherein the yield strength is more than or equal to 333MPa, but also can still maintain better mechanical property under long-time high-temperature placement, can still maintain stable mechanical property after being heated for 1000 hours at 150 ℃, and the yield strength is more than or equal to 312MPa.
Detailed Description
The present invention will be described in further detail with reference to examples.
Example 1
An Al-1.35Si-0.91Mg alloy (comprising, by mass, 1.35% of Si, 0.91% of Mg, 0.20% or less of unavoidable impurities, and the balance Al) is prepared by the following steps:
(1) According to the alloy component ratio, under the protection of carbon dioxide and sulfur hexafluoride, heating and melting pure Al, al-Si intermediate alloy and pure Mg at 750 ℃, then cooling to 710 ℃, keeping the temperature and standing for 15min, then stirring, refining, degassing and removing slag to obtain an aluminum alloy melt, wherein the volume ratio of the carbon dioxide to the sulfur hexafluoride is 6:1;
(2) And (2) guiding the aluminum alloy melt obtained in the step (1) to a water-cooling copper roller gap for sub-rapid solidification casting rolling, wherein the roller gap distance of the water-cooling copper roller is 3mm, and the linear velocity of the water-cooling copper roller is 7.2m/min, so as to obtain an aluminum alloy thin strip, and performing step homogenization heat treatment on the aluminum alloy thin strip: preserving heat for 2h at 450 ℃, preserving heat for 2h at 550 ℃, cold-rolling for 5 times, keeping the total reduction of 70%, and then carrying out solution heat treatment: keeping the temperature at 550 ℃ for 5min, quenching and artificially aging to obtain the high-performance and high-temperature-resistant Al-1.35Si-0.91Mg aluminum alloy, wherein the sub-rapid solidification is as follows: the cooling rate is 450K/s, and the artificial aging treatment comprises the following steps: incubate at 175 ℃ for 8h.
Table 1 shows the mechanical properties of the aluminum alloy obtained in step (2) of example 1 when heated at 150 ℃ for various periods of time
| Heating time/h | Yield strength/MPa |
| 0 | 333 |
| 1000 | 312 |
Example 2
An Al-1.21Si-0.92Mg-0.05Zr-0.20Mn alloy (comprising, in mass percent, 1.21% of Si, 0.92% of Mg, 0.05% of Zr, 0.20% of Mn, and not more than 0.20% of unavoidable impurities, with the balance being Al), the preparation method comprising the steps of:
(1) According to the alloy component ratio, under the protection of argon gas, heating and melting pure Al, al-Si intermediate alloy, al-Zr intermediate alloy, al-Mn intermediate alloy and pure Mg at 745 ℃, then cooling to 710 ℃, preserving heat and standing for 20min, and then stirring, refining, degassing and removing slag to obtain an aluminum alloy melt;
(2) And (2) guiding the aluminum alloy melt obtained in the step (1) to a water-cooling copper roller gap for sub-rapid solidification casting rolling, wherein the roller gap distance of the water-cooling copper roller is 3.5mm, and the linear speed of the water-cooling copper roller is 7.2m/min, so as to obtain an aluminum alloy thin strip, and performing step homogenization heat treatment on the aluminum alloy thin strip: preserving heat for 2h at 450 ℃, preserving heat for 2h at 550 ℃, cold-rolling for 5 times, keeping the total reduction of 72%, and then carrying out solution heat treatment: keeping the temperature at 550 ℃ for 10min, quenching and artificially aging to obtain the high-performance and high-temperature-resistant Al-1.21Si-0.92Mg-0.05Zr-0.20Mn aluminum alloy, wherein the sub-rapid solidification is as follows: the cooling rate is 410K/s, and the artificial aging treatment comprises the following steps: the temperature is kept at 180 ℃ for 5h.
Table 2 shows the mechanical properties of the aluminum alloy obtained in step (2) of example 2 when heated at 150 ℃ for various periods of time
| Heating time/h | Yield strength/MPa |
| 0 | 340 |
| 1000 | 319 |
Example 3
An Al-1.35Si-0.99Mg-0.08Zr alloy (comprising, by mass, 1.35% of Si, 0.99% of Mg, 0.08% of Zr, 0.20% or less of unavoidable impurities, and the balance Al) is prepared by the steps of:
(1) According to the alloy component ratio, under the protection of carbon dioxide and sulfur hexafluoride, heating and melting pure Al, al-Si intermediate alloy, al-Zr intermediate alloy and pure Mg at 750 ℃, then cooling to 715 ℃, preserving heat and standing for 20min, then stirring, refining, degassing and removing slag to obtain an aluminum alloy melt, wherein the volume ratio of the carbon dioxide to the sulfur hexafluoride is 6:1;
(2) Guiding the aluminum alloy melt obtained in the step (1) to a roll gap of a water-cooling copper roll for sub-rapid solidification casting and rolling, wherein the roll gap distance of the water-cooling copper roll is 4mm, and the linear velocity of the water-cooling copper roll is 7m/min, so as to obtain an aluminum alloy thin strip, and carrying out step homogenization heat treatment on the aluminum alloy thin strip: preserving heat for 2h at 450 ℃, preserving heat for 3h at 550 ℃, cold rolling for 6 times, keeping the total reduction of 75 percent, and then carrying out solution heat treatment: keeping the temperature at 550 ℃ for 10min, quenching and artificially aging to obtain the high-performance and high-temperature-resistant Al-1.35Si-0.99Mg-0.08Zr aluminum alloy, wherein the sub-rapid solidification is as follows: the cooling rate is 370K/s, and the artificial aging treatment comprises the following steps: the temperature is kept at 180 ℃ for 7h.
Table 3 shows the mechanical properties of the aluminum alloy obtained in step (2) of example 3 when heated at 150 ℃ for various periods of time
| Heating time/h | Yield strength/MPa |
| 0 | 344 |
| 1000 | 322 |
Example 4
An Al-1.38Si-1.08Mg-0.15Zr-0.10Mn alloy (comprising, in mass percent, 1.38% of Si, 1.08% of Mg, 0.15% of Zr, 0.10% of Mn, and less than or equal to 0.20% of unavoidable impurities, with the balance being Al) is prepared by the following steps:
(1) According to the alloy component ratio, under the protection of carbon dioxide and sulfur hexafluoride, heating and melting pure Al, al-Si intermediate alloy, al-Zr intermediate alloy, al-Mn intermediate alloy and pure Mg at 750 ℃, then cooling to 715 ℃, preserving heat and standing for 20min, then stirring, refining, degassing and removing slag to obtain an aluminum alloy melt, wherein the volume ratio of the carbon dioxide to the sulfur hexafluoride is 6:1;
(2) And (2) guiding the aluminum alloy melt obtained in the step (1) to a water-cooling copper roller gap for sub-rapid solidification casting rolling, wherein the roller gap distance of the water-cooling copper roller is 3.5mm, and the linear speed of the water-cooling copper roller is 7.2m/min, so as to obtain an aluminum alloy thin strip, and performing step homogenization heat treatment on the aluminum alloy thin strip: preserving heat for 5h at 450 ℃, preserving heat for 5h at 555 ℃, cold rolling for 5 times, and carrying out solution heat treatment on the steel sheet with the total reduction of 75 percent: keeping the temperature at 555 ℃ for 30min, quenching and artificially aging to obtain the high-performance and high-temperature-resistant Al-1.38Si-1.08Mg-0.15Zr-0.10Mn aluminum alloy, wherein the sub-rapid solidification is as follows: the cooling rate is 410K/s, and the artificial aging treatment comprises the following steps: the temperature is kept at 190 ℃ for 4h.
Table 4 shows the mechanical properties of the aluminum alloy obtained in step (2) of example 4 when heated at 150 ℃ for different periods of time
| Heating time/h | Yield strength/MPa |
| 0 | 353 |
| 1000 | 330 |
Example 5
An Al-1.23Si-0.97Mg-0.20Zr-0.05Ag alloy (which comprises, by mass, 1.23% of Si, 0.97% of Mg, 0.20% of Zr, 0.05% of Ag, 0.20% or less of unavoidable impurities, and the balance Al), the preparation method comprising the steps of:
(1) According to the alloy component ratio, under the protection of argon gas, heating and melting pure Al, al-Si intermediate alloy, al-Zr intermediate alloy, pure Mg and pure Ag at 750 ℃, then cooling to 720 ℃, preserving heat and standing for 25min, and then stirring, refining, degassing and removing slag to obtain an aluminum alloy solution;
(2) And (2) guiding the aluminum alloy melt obtained in the step (1) to a water-cooled copper roller gap for sub-rapid solidification casting rolling, wherein the roller gap distance of the water-cooled copper roller is 4.5mm, the linear velocity of the water-cooled copper roller is 7m/min, an aluminum alloy thin strip is obtained, and the aluminum alloy thin strip is subjected to step homogenization heat treatment: preserving heat for 5h at 450 ℃, preserving heat for 5h at 560 ℃, cold rolling for 6 times, reducing the total reduction by 78 percent, and then carrying out solution heat treatment: keeping the temperature at 560 ℃ for 10min, quenching and artificially aging to obtain the high-performance and high-temperature-resistant Al-1.23Si-0.97Mg-0.20Zr-0.05Ag aluminum alloy, wherein the sub-rapid solidification is as follows: the cooling rate is 350K/s, and the artificial aging treatment comprises the following steps: the temperature was maintained at 190 ℃ for 3h.
Table 5 shows the mechanical properties of the aluminum alloy obtained in step (2) of example 5 when heated at 150 ℃ for various periods of time
| Heating time/h | Yield strength/MPa |
| 0 | 347 |
| 1000 | 325 |
Example 6
An Al-1.23Si-0.93Mg-0.08Zr-0.15Mn-0.04Ag alloy (comprising, in mass percent, 1.23% of Si, 0.93% of Mg, 0.08% of Zr, 0.15% of Mn, 0.04% of Ag, 0.20% or less of unavoidable impurities, and the balance Al), the preparation method comprising the steps of:
(1) According to the alloy component ratio, under the protection of argon gas, heating and melting pure Al, al-Si intermediate alloy, al-Zr intermediate alloy, al-Mn intermediate alloy, pure Ag and pure Mg at 760 ℃, then cooling to 720 ℃, preserving heat and standing for 30min, and then stirring, refining, degassing and removing slag to obtain an aluminum alloy solution;
(2) And (2) guiding the aluminum alloy melt obtained in the step (1) into a water-cooling copper roller gap for sub-rapid solidification casting rolling, wherein the roller gap distance of the water-cooling copper roller is 3.5mm, and the linear velocity of the water-cooling copper roller is 7.2m/min, so as to obtain an aluminum alloy thin strip, and performing step homogenization heat treatment on the aluminum alloy thin strip: preserving heat for 3h at 450 ℃, preserving heat for 5h at 550 ℃, cold rolling for 5 times, keeping the total reduction of 75 percent, and then carrying out solution heat treatment: keeping the temperature at 560 ℃ for 15min, quenching and artificially aging to obtain the high-performance and high-temperature-resistant Al-1.23Si-0.93Mg-0.08Zr-0.15Mn-0.04Ag aluminum alloy, wherein the sub-rapid solidification is as follows: the cooling rate is 410K/s, and the artificial aging treatment comprises the following steps: keeping the temperature at 180 ℃ for 7h; the average grain diameter of the obtained aluminum alloy is 5-9 mu m, and the grains are uniformly distributed; average size of the main precipitation strengthening phases: the diameter is 1-1.2nm, and the length is 10-12nm. Compared with the prior art, the aluminum alloy obtained by the invention has fine grain size and uniform distribution; the main precipitation strengthening phase is not only uniform and dispersed, but also fine.
Table 6 shows the mechanical properties of the aluminum alloy obtained in step (2) of example 6 when heated at 150 ℃ for different periods of time
| Heating time/h | Yield strength/MPa |
| 0 | 364 |
| 1000 | 344 |
Example 7
An Al-1.22Si-0.96Mg-0.08Zr-0.18Mn-0.03Ag alloy (which comprises, by mass, 1.22% of Si, 0.96% of Mg, 0.08% of Zr, 0.18% of Mn, 0.03% of Ag, 0.20% or less of unavoidable impurities, and the balance Al), and the preparation method comprises the following steps:
(1) According to the alloy component ratio, under the protection of argon gas, heating and melting pure Al, al-Si intermediate alloy, al-Zr intermediate alloy, al-Mn intermediate alloy, pure Ag and pure Mg at 750 ℃, then cooling to 715 ℃, preserving heat and standing for 30min, and then stirring, refining, degassing and removing slag to obtain an aluminum alloy solution;
(2) And (2) guiding the aluminum alloy melt obtained in the step (1) into a water-cooling copper roller gap for sub-rapid solidification casting rolling, wherein the roller gap distance of the water-cooling copper roller is 3.2mm, and the linear velocity of the water-cooling copper roller is 7.6m/min, so as to obtain an aluminum alloy thin strip, and performing step homogenization heat treatment on the aluminum alloy thin strip: preserving heat at 460 ℃ for 3h, preserving heat at 550 ℃ for 5h, cold rolling for 5 times, keeping total reduction of 72%, and then carrying out solution heat treatment: keeping the temperature at 560 ℃ for 10min, quenching and artificially aging to obtain the high-performance and high-temperature-resistant Al-1.22Si-0.96Mg-0.08Zr-0.18Mn-0.03Ag aluminum alloy, wherein the sub-rapid solidification is as follows: the cooling rate is 430K/s, and the artificial aging treatment comprises the following steps: the temperature was maintained at 190 ℃ for 3h.
Table 7 shows the mechanical properties of the aluminum alloy obtained in step (2) of example 7 when heated at 150 ℃ for various periods of time
| Heating time/h | Yield strength/MPa |
| 0 | 350 |
| 1000 | 327 |
Comparative example 1
Journal name "Journal of alloys and Compounds", year: 2022, term number: 909, article number: 164819, paper author: qiaoli Li et al, entitled "preferential overview decorating and mechanical properties in 6082 aluminum alloy along long-term thermal exposure". Page 2 "2.Materials and method" paragraph 1: the selected material is commercial 6082 (Al-Mg-Si series) aluminum alloy and comprises the following components in percentage by mass: si:1.19%, mg:0.75%, mn:0.68%, fe:0.18%, cr:0.048%, zn:0.032%, cu:0.027%, ti:0.025% and the balance of Al. Commercial 6082aluminium alloy is solution heat treated at 540 ℃ for 1h, water quenched and then aged at 175 ℃ for 8h to obtain aluminium alloy profiles. Page 3 fig. 3: the yield strength of the aluminum alloy section is 330MPa, and is 255MPa after being heated for 1000 hours at 150 ℃, and the yield strength is reduced to 75MPa.
According to the data, the following data are shown: the alloy addition amount of the comparative example 1 is larger than that of all the examples of the present invention, but the initial mechanical properties of the alloy of the comparative example 1 are lower than those of all the examples of the present invention, and the stability in high-temperature long-time standing is lower than those of all the examples of the present invention, so that the present invention achieves a significant technical effect compared with the prior art.
Comparative example 2
Journal name "Materials characteristics", year: 2021, term number: 181, article number: 111464, paper author: wenyuan Gong et Al, entitled "giantake hardbanding stress of multi-scale prediction threaded Al-Mg-Si-Cu-Zn alloy via pre-imaging procedures". Page 2 "2.Materials and methods" paragraph 1: the selected material is Al-Mg-Si series aluminum alloy and comprises the following components in percentage by mass: si:1.60%, mg:1.20%, cu:0.20%, zn:3.00%, fe:0.40%, mn:0.50%, ti:0.02%, ni:0.03 percent and the balance of Al. The aluminum alloy is subjected to smelting, hot rolling at 540 ℃, cold rolling, annealing at 400 ℃ for 1h, solution heat treatment at 550 ℃ for 8min, water quenching, pre-aging at 80-185 ℃ for 0-12 h, natural aging at 25 ℃ for 14 days, pre-deformation for 2%, and then aging at 185 ℃ for 20min to obtain the aluminum alloy section. Page 5 "3.4. Gain microstructure analysis": the average grain size of the aluminum alloy section is 13 mu m. Page table 8, 2: average size of main precipitation strengthening phase (β "phase) of the aluminum alloy profile described above: the diameter is 3.7nm and the length is 24.3nm.
Compared with the alloy obtained in the embodiment 6 of the present invention, the alloy used in the comparative example 2 has the addition amount and the contents of Si and Mg higher than those of the alloy obtained in the embodiment 6 of the present invention, and according to the report in the prior art, for the Al — Mg-Si based (6 based) alloy, the higher the contents of Si and Mg are, the more beneficial the reduction of the crystal grains and the sizes of the precipitation strengthening phases, and according to the calculation in the prior art, the alloy obtained in the embodiment 6 of the present invention has the crystal grains and the sizes of the precipitation strengthening phases larger than those of the comparative example 2, but the result shows that: the sizes of alloy grains and precipitation strengthening phases obtained in the embodiment 6 of the invention are smaller than those of the alloy grains and precipitation strengthening phases in the comparative example 2, so compared with the prior art, the invention achieves unexpected technical effects; in addition, comparative example 2, which employs high temperature hot rolling and multi-step aging including long-term aging of natural aging at 25 ℃ for 14 days, saves alloy production costs and realizes a short process alloy, so that the present invention saves production costs compared to the prior art.
To sum up: compared with the prior art, the invention ensures that the finally obtained alloy has more fine and evenly distributed precipitation strengthening phases than the prior art through the interaction among alloy components and the synergistic effect of the process; in addition, compared with the prior art, the alloy can have higher mechanical property under the condition of room temperature or high temperature treatment, and even after being heated for 1000 hours at 150 ℃, the alloy with more excellent performance than the prior art can be obtained.
Claims (4)
1. A high-performance and high-temperature-resistant Al-Mg-Si series aluminum alloy is characterized in that: the alloy comprises the following components in percentage by mass: mg:0.91-1.10%; si:1.21 to 1.4 percent; mn: 0-less Mn than or equal to 0.2%; zr: 0-straw Zr is less than or equal to 0.2 percent; ag: 0-straw Ag is less than or equal to 0.05 percent; the total amount of inevitable impurities is less than or equal to 0.20 percent; the balance of Al; the preparation method of the aluminum alloy comprises the following steps:
(1) Under protective gas, sequentially adding pure Al, al-Si intermediate alloy, al-Zr intermediate alloy, al-Mn intermediate alloy, pure Ag and pure Mg into a smelting furnace for heating and melting, then cooling, carrying out heat preservation treatment, and then obtaining an aluminum alloy melt after stirring, refining, degassing and slag removal, wherein the heating and melting temperature is as follows: 700-780 ℃, and the heat preservation treatment comprises the following steps: keeping the temperature at 700-750 ℃ for 10-60min;
(2) Guiding the aluminum alloy melt obtained in the step (1) into a water-cooling copper roller gap for sub-rapid solidification casting rolling, and then carrying out step homogenization heat treatment, multi-pass cold rolling, solution heat treatment, quenching and artificial aging treatment to obtain high-performance and high-temperature-resistant Al-Mg-Si series aluminum alloy;
the roll gap distance of the water-cooled copper roller in the step (2) is 2-4.5mm, the linear speed of the water-cooled copper roller is 5-15m/min, and the sub-rapid solidification is as follows: the cooling rate is 300-500K/s;
the step homogenizing heat treatment in the step (2) comprises the following steps: preserving heat for 2-5h at 450-460 ℃, and preserving heat for 2-5h at 540-560 ℃; the multi-pass cold rolling comprises the following steps: 4-8 times of cold rolling, wherein the total reduction is 65-80%; the solution heat treatment comprises the following steps: preserving heat at 550-560 ℃ for 5-30min; the artificial aging treatment comprises the following steps: preserving the heat for 3-8h at 175-190 ℃;
the average size of the main precipitation strengthening phases of the Al-Mg-Si series aluminum alloy obtained in the step (2): the diameter is 1-1.2nm, and the length is 10-12nm.
2. The high-performance and high-temperature-resistant Al-Mg-Si aluminum alloy according to claim 1, wherein: the protective gas in the step (1) is argon or a mixed gas of carbon dioxide and sulfur hexafluoride; the volume ratio of the carbon dioxide to the sulfur hexafluoride is 85-90.
3. The high performance, high temperature resistant Al-Mg-Si based aluminum alloy of claim 1, wherein: the heating and melting temperature in the step (1) is as follows: 740 to 760 ℃.
4. The high performance, high temperature resistant Al-Mg-Si based aluminum alloy of claim 1, wherein: the heat preservation treatment in the step (1) comprises the following steps: keeping the temperature at 710-730 deg.C for 15-40min.
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| CN114574735A (en) * | 2022-03-04 | 2022-06-03 | 北京工业大学 | Cu-containing high-strength corrosion-resistant Al-Mg-Si alloy and preparation method thereof |
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| JP2000160310A (en) * | 1998-11-25 | 2000-06-13 | Shinko Arukoa Yuso Kizai Kk | Production of aluminum alloy sheet suppressed in cold aging property |
| CN112522553A (en) * | 2020-12-01 | 2021-03-19 | 吉林大学 | High-performance Al-Mg-Si alloy and preparation method thereof |
| CN114540682A (en) * | 2022-02-28 | 2022-05-27 | 吉林大学 | Multi-element microalloying high-efficiency extruded magnesium alloy and preparation method thereof |
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