CN113667866B - High-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy - Google Patents
High-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy Download PDFInfo
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- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
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- 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
- C22F1/043—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 silicon as the next major constituent
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- 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
- C22F1/047—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 magnesium as the next major constituent
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
- C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
Abstract
The invention belongs to the technical field of aluminum alloy materials, and particularly relates to a high-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy. The Al-Mg-Si alloy comprises, by mass, 0.40-1.00% of Mg0.50-0.90% of Si, less than or equal to 0.60% of Mn, less than or equal to 0.30% of Cr, less than or equal to 0.25% of Fe, and 96.8-99.1% of Al, wherein Si isfree＝Si‑0.3×(Mn+Fe+Cr)，Mg/SifreeThe mass ratio is 0.72-1.40, and Mg +2SifreeThe mass percentage is 1.40-2.40%. The aluminum alloy provided by the invention not only has excellent conventional mechanical properties, but also has good bending toughness, and also has outstanding crushing and impact resistance and energy absorption properties.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy materials, and particularly relates to a high-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy.
Background
With the continuous high-speed development of the human economic society, the energy problem and the environmental problem emerge continuously, and the environment-friendly, low-carbon and environment-friendly sustainable development is a development direction of the current society. The oil consumption of motor vehicles accounts for a certain proportion of the total consumption of crude oil, and the rapidly developed automobile industry not only provides great challenge for petroleum supply in China, but also brings unprecedented pressure to the environment due to the emission of automobile tail gas. Energy conservation and emission reduction are the key for transformation and upgrading of the automobile industry, and light weight is an important means for realizing energy conservation and emission reduction.
The Al-Mg-Si alloy belongs to heat-treatable reinforced aluminum alloy, has the advantages of high specific strength, good formability, excellent corrosion resistance, high weldability and the like, is an important material for realizing light weight of automobiles, and is widely applied to structural members (automobile bodies) at present, such as: the automobile body panel, the engine piston, the anticollision roof beam and bumper etc.. However, the service conditions of different parts are different from each other, and besides improving the conventional mechanical properties of the material, the related properties of the parts under the corresponding service conditions need to be improved according to different service conditions of the parts, for example, key safety structural members such as a new energy automobile battery tray and an automobile anti-collision beam may be broken by external violent collision under the service conditions, and even serious personnel and property losses are caused. Therefore, the impact resistance and energy absorption performance of the aluminum alloy used under the working conditions are particularly important.
At present, the main focus in industrial production is still on the strength of the aluminum alloy, and the impact resistance and energy absorption performance of the aluminum alloy are rarely researched. Although the chinese patent CN109504870B provides a lightweight aluminum alloy for automobile anti-collision beams, the synthesis reaction process and the solidification process are controlled by combining the direct melt reaction technology with the ultrasonic magnetic coupling field technology to obtain a composite material with in-situ nanoparticles uniformly distributed, and then the composite material is subjected to hot extrusion forming and heat treatment, so that the preparation process is complex, difficult, high in cost and not suitable for wide application. And researches find that the impact resistance of the material is not only related to the strength of the material, but also closely related to the plasticity and toughness of the material, and in addition, the microstructure of the material is also important to the impact resistance and energy absorption performance of the material.
Disclosure of Invention
Aiming at the problems in the prior art, the invention provides the Al-Mg-Si alloy which has high bending toughness, impact toughness, crushing performance and energy absorption capacity on the premise of ensuring the strength, corrosion resistance and thermal stability of the alloy.
The above object of the present invention is achieved by the following technical solutions: the high-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy comprises, by mass, 0.40-1.00% of Mg0.50-0.90%, less than or equal to 0.60% of Mn, less than or equal to 0.30% of Cr, less than or equal to 0.25% of Fe and 96.8-99.1% of Al, wherein Sifree = Si-0.3 x (Mn + Fe + Cr), the mass ratio of Mg/Sifree is 0.72-1.40, and the mass percentage of Mg +2Sifree is 1.40% -2.40%.
Mg and Si are main additive elements of the 6xxx alloy, and are interacted to separate out second phase particles of GP zones, beta' and beta and the like in the aging process to strengthen the matrix. According to the newly researched evolution law of a precipitated phase of the Al-Mg-Si alloy in the aging process, the method comprises the following steps: supersaturated solid solution → GP zone → β '(B', U1, U2) → β. Wherein the beta' phase has the best strengthening effect and is the most main strengthening precipitation phase in the peak aging alloy; the beta 'phase is a main precipitated phase in the alloy during overaging, and the strengthening effect is not as good as that of the beta' phase; the beta phase is a balance phase and is in a non-coherent relationship with the aluminum matrix, and the strengthening effect is limited.
Table 1.6 information on precipitated phases in xxx alloys.
In the composition design of 6xxx alloys, a beta (Mg 2 Si) phase is often regarded as a main strengthening precipitated phase in the alloys, so that the Mg/Si atomic ratio =2:1 is taken as a principle of Mg and Si proportioning design, which is a misleading area.
Since the best effect of high strength and high strengthening in Al-Mg-Si alloys is the β '' phase, their Mg/Si atomic ratio is 5/6. As can be seen from the above, rational composition design should be 0.714:1 (Mg relative atomic mass 24 and Si relative atomic mass 28) in terms of mass ratio with reference to the atomic ratio of β ″ phase, i.e., Mg/Si atomic ratio =5: 6.
In the Al-Mg-Si alloy, if the alloy proportion is lower than the ratio, excessive Si exists in an aluminum matrix, the excessive Si is easy to segregate and precipitate on grain boundaries, the grain boundary bonding force is reduced, meanwhile, stress concentration is easy to cause to become a source of crack initiation in the deformation process, the plasticity and the deformation energy absorption effect of the alloy are damaged, certain excessive Mg is beneficial to improving the thermal stability of the alloy, but if the excessive Mg is too much, the excessive Mg does not effectively combine with the Si to form a strengthening precipitation phase, the strengthening effect is weakened on the contrary, meanwhile, the excessive Mg also reduces the extrudability of the alloy (the alloy strain hardening index is increased along with the increase of the Mg/Sifree value, the alloy processing and forming property is reduced), and high quenching sensitivity is brought to be not beneficial to large-scale production. The invention comprehensively considers the consumption of Mn, Fe, Cr and other elements on Si, can be used for forming free silicon Sifree = Si-0.3 (Mn + Fe + Cr) of a beta '' strengthening phase, controls the Mg/Sifree mass ratio to be 0.72-1.40, avoids the excessive Si existing in an aluminum matrix, simultaneously ensures certain Mg, and avoids the excessive Mg from influencing the alloy performance.
Furthermore, the contents of Mg and Si together determine the strength level of the Al-Mg-Si alloy. It was found that increasing 1% Si alone produced about a 2-fold increase in yield strength over 1% Mg, so the strength level of the alloy was directly determined by (Mg +2 Sifree). The mass ratio of Mg/Sifree in the Al-Mg-Si alloy is more than 0.72, namely the Mg is excessive. In the alloy with excess Mg, when the content of Si is increased, more strengthening precipitated phases are formed by combining with the excess Mg, so that the yield strength of the alloy is obviously improved; when the addition of Mg is continued, since there is no effective Si to combine with it to form a strengthening phase, the nucleation rate of the strengthening precipitates can be increased only to some extent, so that the number of precipitates is increased limitedly, which contributes to the strength to a limited extent. However, when Mg +2Sifree is less than 1.40%, the amount of precipitated phases is insufficient, the strengthening effect is reduced, and the alloy strength cannot meet the development target (the yield strength is more than or equal to 240 MPa); the higher the value of Mg +2Sifree, the worse the deformation performance of the alloy, and when the total content of Mg +2Sifree is more than 2.40%, the alloy is easy to crack during deformation energy absorption tests such as crushing, drop hammer and the like, and the impact resistance and energy absorption performance are obviously reduced. Therefore, the reasonable total content range of Mg +2Sifree in the invention is 1.40-2.40%. In conclusion, in the Al-Mg-Si alloy, the mass ratio of Mg/Sifree = Si-0.3 x (Mn + Fe + Cr) is controlled to be 0.72-1.40, and the mass percentage of Mg +2Sifree is 1.40-2.40%.
In the Al-Mg-Si alloy, the mass percent of Mn +2Cr is 0.40-1.0%. More preferably, the mass percentage of Cr is 0.10-0.20%. The production and processing are processes that an external working material deforms, a large amount of energy is accumulated in the material along with continuous input of energy and increase of deformation, when the energy reaches a certain critical value (more than or equal to recrystallization activation energy), the material recrystallizes, the recrystallization always occurs on the surface which is in direct contact with a tool and a die, a surface coarse crystal layer is formed, and the uniformity and consistency of the material performance are seriously influenced by the formation of the coarse crystal layer. The Mn/Cr can form submicron-grade dispersed precipitated phases with Al, such as Al6Mn (Fe) and Al (CrFe) Si, and the precipitated phases can effectively refine the grain structure to inhibit recrystallization in the processing process, stabilize the deformation structure in the product and reduce the thickness of a coarse crystal layer on the surface of the product; on the other hand, the plasticity of the alloy can be improved. However, too high Mn/Cr content not only consumes more main alloy element Si and reduces alloy strength, but also obviously increases the quenching sensitivity of the alloy. In the aspect of comprehensive performance, Cr is stronger than Mn, so the mass percent of Mn +2Cr in the Al-Mg-Si alloy of the invention needs to meet 0.40-1.0%, and the mass percent of Cr is preferably 0.10-0.20%.
The Al-Mg-Si alloy also comprises V, and the V is less than or equal to 0.20 percent by mass percent. More preferably, V is 0.05 to 0.15% by mass. V can form peritectic disperse phase with Al and other related elements in the casting process and is uniformly distributed in the crystal, so that the channel of dislocation motion in the deformation process is effectively improved, and the impact toughness of the alloy is improved; however, when the amount of V added is too large, the AlV phase tends to be segregated, which affects the uniformity of the alloy and deteriorates the toughness of the alloy. In addition, the V-containing phase can effectively improve the high-temperature performance of the alloy and improve the thermal stability of the alloy. The Al-Mg-Si alloys according to the invention therefore have a V of 0.20% or less, preferably 0.05 to 0.15%.
The Al-Mg-Si alloy also comprises Cu, and the Cu is less than or equal to 0.25 percent by mass percent.
The Al-Mg-Si alloy also comprises Ti, and the Ti is less than or equal to 0.10 percent by mass percent.
The single content of other inevitable impurity elements in the Al-Mg-Si alloy is less than or equal to 0.05 percent, and the total content is less than or equal to 0.15 percent.
In the high-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy, the Al-Mg-Si alloy has a multilayer structure of coarse crystal layers/fiber structures/coarse crystal layers, and the thickness of the single-side coarse crystal layers is less than or equal to 0.3 multiplied by the wall thickness. The longitudinal bending performance and the shock resistance of the product can be effectively ensured by the core fiber tissue of the middle layer of the multilayer structure, and the anisotropy and the corrosion performance of the product performance can be improved to a certain extent by the coarse crystal layers on the inner surface and the outer surface.
Preferably, the wall thickness of the aluminum alloy product obtained by the invention is less than or equal to 10mm, and the performance is possibly lower when the wall thickness is too thick, so that the requirement of the yield strength of 240MPa is difficult to meet.
The processing method of the high-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy comprises aging treatment, wherein the aging treatment is T6 treatment or T7 treatment.
The high-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy can adopt the processing method of the conventional aluminum alloy, including smelting, casting, heat treatment, extrusion molding and the like.
During smelting, the raw materials are added in the form of aluminum ingots, magnesium ingots, and intermediate alloy ingots such as Al-Si, Al-Mn, Al-Cr, Al-V, etc.
Preheating the aluminum bar before extrusion molding, wherein the preheating temperature is 480-530 ℃.
The high-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy has the yield strength of more than or equal to 240MPa and better thermal stability, the yield strength of the final alloy is more than or equal to 230MPa after heat preservation at 150 ℃/1000h, the bending toughness is excellent, the transverse (vertical to the extrusion direction) bending angle of the alloy is more than or equal to 75 degrees, and the longitudinal (parallel to the extrusion direction) bending angle of the alloy is more than or equal to 65 degrees.
Compared with the prior art, the invention has the following beneficial effects:
(1) according to the invention, through optimally designing the contents of main alloy elements such as Mg/Si, Mn and Cr in the Al-Mg-Si alloy, even V and the like, on the premise of ensuring the strength, corrosion resistance and thermal stability of the alloy, the bending toughness and crushing performance of the Al-Mg-Si alloy are effectively improved, the impact resistance and energy absorption performance of the alloy are obviously improved, and the alloy section bar does not generate through cracks larger than 30mm under the impact action of a 250Kg weight at the speed of 40 Km/h.
(2) The invention has reasonable design of the main alloy element Mg/Si ratio and the total amount thereof, can improve the strain hardening index of the alloy, improve the deformation behavior of the alloy, reduce local stress concentration and improve the deformation uniformity and energy absorption capacity while ensuring the strength of the alloy.
(3) The Mn and Cr atoms, Al and Si atoms have strong attraction effect, and dispersed second phase particles are easily formed, and the particles can effectively pin the migration of grain boundaries and inhibit the recrystallization of the alloy in the processing process; v is easy to react with Al and Si atoms to form intermetallic compounds which are uniformly distributed in the crystal, thereby effectively improving the channel of dislocation motion and the uniformity of deformation in the deformation process and improving the plasticity and impact toughness of the alloy.
Drawings
FIG. 1 is a graph showing the effect of crushing cracking comparison between the product made of the impact-resistant energy-absorbing Al-Mg-Si alloy of example 1 and the product made of the alloy of comparative example 1;
FIG. 2 is a high-speed impact test and results of the impact-absorbing Al-Mg-Si alloy product of example 3;
FIG. 3 is a schematic diagram of a bending toughness test of an impact-resistant energy-absorbing Al-Mg-Si alloy product.
Detailed Description
The technical solution of the present invention is further described and illustrated by the following specific examples. The raw materials used in the examples of the present invention are those commonly used in the art, and the methods used in the examples are those conventional in the art, unless otherwise specified. It should be understood that the specific embodiments described herein are only for the purpose of facilitating understanding of the present invention, and are not intended to limit the present invention specifically.
The Al-Mg-Si alloy is suitable for various other conventional aluminum alloy processing methods such as smelting, casting, heat treatment, extrusion molding and the like.
During smelting, aluminum ingots, magnesium ingots and intermediate alloy ingots of Al-Si, Al-Mn, Al-Cr, Al-V and the like are added as raw materials. And adding a refiner in the smelting process.
The extrusion molding is to preheat the aluminum bar at the temperature of 480-530 ℃.
Examples 1 to 11
The Al-Mg-Si alloy compositions described in examples 1 to 11 of Table 2 were melted, semicontinuously cast into ingots, trimmed to remove the ends, homogenized, extruded and cooled using corresponding section dies, and finally subjected to aging treatment using T7.
Example 12
Example 12 differs from example 3 only in the aging process, which in example 12 was treated with T6.
Comparative examples 1 to 4
Comparative examples 1 to 4 differ from example 1 only in the composition of the aluminum alloy, and specifically refer to table 2, the preparation method is the same as example 1.
Comparative examples 5 to 6
Comparative examples 5 to 6 differ from example 3 only in the ageing process, with natural ageing T4 and underageing T6X treatments respectively. The alloy sample treated by the underaged T6X has the solid solution alloy atoms only partially precipitated, and has lower performance and poorer impact performance.
TABLE 2 examples 1-12 and comparative examples 1-4 alloy compositions in percent by weight (wt%).
The crush cracking of the product made of the Al-Mg-Si alloy of example 1 was compared with the crush cracking of the alloy of comparative example 1, and the comparative results are shown in FIG. 1, where the alloy of example 1 did not produce any through cracks after crushing, while the alloy of comparative example 1 produced severe cracking after crushing, and some of the blocks had been crushed away from the matrix. In conclusion, the crushing performance of the alloy in the example 1 is far better than that of the alloy in the comparative example 1.
The Al-Mg-Si alloy in the example 3 is made into a product, a high-speed impact test is carried out, the test result is shown in figure 2, and the alloy product in the example 3 does not generate a through crack of more than or equal to 20mm after high-speed collision (40 Km/h), which shows that the alloy in the example 3 has excellent impact resistance.
The aluminum alloy products of examples 1-12 and comparative examples 1-6 were tested for mechanical properties, bending toughness, and crushing performance. Wherein the bending toughness test standard is VDA238-100, the test sample size is 60mm × 60mm, the test direction is parallel (longitudinal)/perpendicular (transverse) to the extrusion direction, and the test is finished when the maximum load of the pressure head is reduced by 60N, and the specific test diagram is shown in FIG. 3. The magnitude of the alloy bending angle alpha is closely related to the thickness t of the test sample, and the comparison is carried out by converting the bending angle alpha into an angle alpha' of a standard sample thickness t0 (2 mm) according to the following formula:
the evaluation of the crushing performance of the aluminum alloy was performed by a quasi-static compression test (in the direction of profile extrusion). The crushed sample had an original length of 300mm and was compressed to 100mm at a speed of 100 mm/min. The crushing performance of the alloy is evaluated by measuring the length of the cracks on the sample after the test, wherein the No-through cracks are A grade, the No-10 mm through cracks are B grade, and the No-10 mm through cracks are C grade. The products with the crushing grades A and B show excellent crushing performance.
TABLE 3 mechanical properties, bending toughness, crushing performance of the alloys of examples 1-12 and comparative examples 1-6.
Compared with the comparative examples 1-2 and 4, the longitudinal bending toughness and the crushing performance of the alloy disclosed by the invention are greatly improved, wherein the longitudinal bending angle is improved to more than 65 degrees from 50 degrees, and the crushing performance grade is improved to B grade or above from C grade. Meanwhile, compared with comparative examples 3 and 5-6, the impact-resistant energy-absorbing Al-Mg-Si alloy disclosed by the invention has the advantages that the conventional mechanical properties (tensile strength, yield strength and elongation) are also obviously improved, the average tensile strength is more than or equal to 265MPa, the average yield strength is more than or equal to 240MPa, and the average elongation after fracture is more than or equal to 11%. The alloy of comparative example 5 is excellent in elongation, bending toughness and crushing performance, but has too low an overall strength, wherein the yield strength is only 115MPa, which is less than 50% of that of the alloy of example 1, indicating that the T4 process cannot achieve the expected strength effect. The alloy of comparative example 6 has satisfactory elongation and bending properties, but has extremely poor crushing properties, and is difficult to form when the alloy is crushed.
In conclusion, the aluminum alloy provided by the invention has excellent conventional mechanical properties, the yield strength is more than or equal to 240MPa, and the elongation after fracture is more than or equal to 10%; meanwhile, the alloy has good bending toughness, the bending angle of the alloy in the transverse direction (vertical to the extrusion direction) is more than or equal to 75 degrees, and the bending angle of the alloy in the longitudinal direction (parallel to the extrusion direction) is more than or equal to 65 degrees; and outstanding crushing and impact-resistant energy-absorbing performance, and the integral crushing performance of the alloy is more than or equal to grade B.
The above embodiments are not exhaustive of the range of parameters of the claimed technical solutions of the present invention and the new technical solutions formed by equivalent replacement of single or multiple technical features in the technical solutions of the embodiments are also within the scope of the claimed technical solutions of the present invention, and if no specific description is given for all the parameters involved in the technical solutions of the present invention, there is no unique combination of the parameters with each other that is not replaceable.
The specific embodiments described herein are merely illustrative of the spirit of the invention and do not limit the scope of the invention. The technical solutions similar or similar to the present invention can be obtained by those skilled in the art through equivalent replacement or equivalent transformation, and all fall within the protection scope of the present invention.
Claims (7)
1. The high-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy is characterized by consisting of, by mass, 0.40-1.00% of Mg, 0.50-0.90% of Si, not more than 0.60% of Mn, not more than 0.30% of Cr, not more than 0.25% of Fe and 96.8-99.1% of Al, wherein Si isfree=Si-0.3×(Mn+Fe+Cr)，Mg/SifreeThe mass ratio is 0.72-1.40, and Mg +2SifreeThe mass percentage is 1.40% -2.40%; the mass percent of Mn +2Cr is 0.40-1.0%; said Al-Mg-Si alloy having "coarse crystal layer/fibrous structure/coarse crystal layerThe thickness of the single-side coarse crystal layer is less than or equal to 0.3 multiplied by the wall thickness; the processing method of the Al-Mg-Si alloy comprises aging treatment, wherein the aging treatment is T6 treatment or T7 treatment.
2. The Al-Mg-Si alloy with high strength and toughness and energy absorption function as claimed in claim 1, wherein the mass percent of Cr in the Al-Mg-Si alloy is 0.10-0.20%.
3. The Al-Mg-Si alloy with high strength and toughness and energy absorption function as claimed in claim 1, wherein the Al-Mg-Si alloy further comprises V, and the V is less than or equal to 0.20 percent by mass.
4. The Al-Mg-Si alloy with high strength and toughness and energy absorption function as claimed in claim 3, wherein V is 0.05-0.15% by mass.
5. The Al-Mg-Si alloy with high strength, high toughness, impact resistance and energy absorption as claimed in claim 1 or 4, wherein the Al-Mg-Si alloy further comprises Cu, and the Cu is less than or equal to 0.25 percent by mass percent.
6. The Al-Mg-Si alloy with high strength, high toughness, impact resistance and energy absorption as claimed in claim 5, wherein the Al-Mg-Si alloy further comprises Ti, and the Ti is less than or equal to 0.10 percent by mass.
7. The Al-Mg-Si alloy with high strength, high toughness, impact resistance and energy absorption as claimed in claim 1, 4 or 6, wherein the other inevitable impurity elements in the Al-Mg-Si alloy are less than or equal to 0.05% individually and less than or equal to 0.15% in total.
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| CN202110757516.0A CN113667866B (en) | 2021-07-05 | 2021-07-05 | High-strength high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy |
| EP21948982.0A EP4368735A1 (en) | 2021-07-05 | 2021-08-23 | High-strength and high-toughness impact-resistant energy-absorbing al-mg-si alloy |
| PCT/CN2021/113975 WO2023279493A1 (en) | 2021-07-05 | 2021-08-23 | High-strength and high-toughness impact-resistant energy-absorbing al-mg-si alloy |
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| JP2000054049A (en) * | 1998-08-07 | 2000-02-22 | Mitsubishi Alum Co Ltd | Aluminum-magnesium-silicon alloy extruded shape material for side member excellent in collapse characteristic and its production |
| CN103290278B (en) * | 2013-06-07 | 2015-09-16 | 湖南大学 | The high energy absorption capacity aluminium alloy of a kind of body of a motor car |
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| CN116083764A (en) * | 2015-12-23 | 2023-05-09 | 诺尔斯海德公司 | Method for producing heat treatable aluminium alloys with improved mechanical properties |
| CN108220706B (en) * | 2018-01-02 | 2020-03-13 | 山东友升铝业有限公司 | Deformation aluminum alloy for improving crushing performance of extruded profile |
| CN108193093A (en) * | 2018-01-02 | 2018-06-22 | 山东友升铝业有限公司 | A kind of vehicle energy absorption box aluminum alloy materials |
| CN109504870B (en) | 2018-11-21 | 2020-11-20 | 江苏大学 | In-situ nano reinforced aluminum alloy for lightweight automobile anti-collision beam and preparation method thereof |
| CN110079716B (en) * | 2019-05-23 | 2021-12-03 | 鼎镁新材料科技股份有限公司 | High-manganese-chromium-6 XXX series aluminum alloy material for automobile body and preparation method thereof |
| CN110129634B (en) * | 2019-05-23 | 2021-10-22 | 鼎镁新材料科技股份有限公司 | Impact-resistant high-energy-absorption high-manganese 6XXX series aluminum alloy and preparation method thereof |
| CN111041289A (en) * | 2019-12-18 | 2020-04-21 | 山东友升铝业有限公司 | 6005A aluminum alloy for automobile and energy absorption box processing method |
| CN110846539B (en) * | 2019-12-19 | 2021-02-09 | 辽宁忠旺集团有限公司 | High-energy-absorption Al-Mg-Si-Cu alloy and preparation method thereof |
| CN111560546B (en) * | 2020-04-29 | 2021-08-03 | 佛山市三水凤铝铝业有限公司 | Aluminum alloy with high crushing performance and preparation method of section bar of aluminum alloy |
| CN112442618B (en) * | 2020-11-24 | 2022-05-20 | 辽宁忠旺集团有限公司 | Novel Al-Mg-Si aluminum alloy energy-absorbing material for collision and preparation method thereof |
| CN112760528A (en) * | 2020-12-24 | 2021-05-07 | 亚太轻合金(南通)科技有限公司 | Aluminum alloy for improving crushing performance of 6008 energy-absorbing box and preparation method thereof |
-
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- 2021-08-23 WO PCT/CN2021/113975 patent/WO2023279493A1/en active Application Filing
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108165841A (en) * | 2018-01-29 | 2018-06-15 | 辽宁忠旺集团有限公司 | A kind of 6008 aluminium alloy energy-absorption box processing technology of automobile |
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