EP4368735A1 - High-strength and high-toughness impact-resistant energy-absorbing al-mg-si alloy - Google Patents

High-strength and high-toughness impact-resistant energy-absorbing al-mg-si alloy Download PDF

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Publication number
EP4368735A1
EP4368735A1 EP21948982.0A EP21948982A EP4368735A1 EP 4368735 A1 EP4368735 A1 EP 4368735A1 EP 21948982 A EP21948982 A EP 21948982A EP 4368735 A1 EP4368735 A1 EP 4368735A1
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Prior art keywords
alloy
strength
absorbing
impact
mass
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EP21948982.0A
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German (de)
French (fr)
Inventor
Haichun JIANG
Qingrong RAN
Yuling Sun
Canwei LIU
Chunming GU
Zhengcheng SONG
Jiaming JING
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Ningbo Shintai Machines Co Ltd
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Ningbo Shintai Machines Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/05—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

Definitions

  • the present invention relates to the technical field of aluminum alloy materials, and in particular to a high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy.
  • Al-Mg-Si alloy is a heat-treatable strengthened aluminum alloy, which has the advantages of high specific strength, good formability, excellent corrosion resistance and high weldability, and is an important material for realizing the light weight of automobiles.
  • Al-Mg-Si alloy is widely used in (vehicle body) structural parts, such as a vehicle body cover part, an engine piston, an anti-collision beam, a bumper, and the like.
  • vehicle body vehicle body structural parts, such as a vehicle body cover part, an engine piston, an anti-collision beam, a bumper, and the like.
  • the service conditions of different components are different.
  • the present invention provides an Al-Mg-Si alloy having high bending toughness, impact toughness, crushing performance and energy absorption capacity while ensuring the strength, corrosion resistance and thermal stability of the alloy.
  • Mg and Si are the main additive elements of 6xxx alloy, and the second phase particles of ⁇ ", ⁇ ' and ⁇ are precipitated in the aging process to strengthen the Matrix.
  • the evolution of precipitated phases is as follows: supersaturated solid solution ⁇ GP Zone ⁇ ⁇ " ⁇ ⁇ '(B', U1, U2) ⁇ ⁇ .
  • the ⁇ " phase has the best strengthening effect, which is the most significant strengthened precipitated phase in peak aged alloy.
  • the ⁇ ' phase is the main precipitated phase in overaged alloy, and has an inferior strengthening effect compared with ⁇ " phase; and the ⁇ phase is an equilibrium phase which is non-coherent with aluminum Matrix and has a limited strengthening effect.
  • the mass ratio of Mg/Si free is controlled to be 0.72-1.40, avoiding the presence of excess Si in the aluminum matrix while ensuring a certain amount of Mg, and avoiding the effect of excess Mg on the properties of the alloy.
  • the content of Mg and Si together determine the strength level of the Al-Mg-Si alloy. It has been found that the increase in yield strength with 1% Si alone is about twice that with 1% Mg, so the strength level of the alloy is directly determined by (Mg + 2Si free ).
  • the Mg/Si free mass ratio in the Al-Mg-Si alloys of the present invention is all above 0.72, i.e. Mg is excess. In the Mg-excess alloy, when the Si content increases, more strengthened precipitated phases are formed by combining with the excess Mg, which significantly improves the yield strength of the alloy.
  • the nucleation rate of the strengthened precipitated phase can be increased only to some extent, thereby increasing the number of precipitated phases to a limited extent, which has a limited contribution to strength.
  • the content of Mg + 2Si free is less than 1.40%, the number of precipitated phases is insufficient and the strengthening effect decreases, and the strength of the alloy cannot meet the development target (yield strength ⁇ 240 MPa). The higher the value of Mg + 2Si free is, the worse the deformation performance of the alloy is.
  • Mg + 2Si free Si-0.3 ⁇ (Mn+Fe+Cr)
  • the mass ratio of Mg/Si free is controlled to be 0.72-1.40, and the percentage by mass of Mg + 2Si free still satisfies 1.40%-2.40%.
  • the percentage by mass of Mn + 2Cr is 0.40%-1.0%. Further preferably, the percentage by mass of Cr is 0.10%-0.20%.
  • Production and processing are a deformation process of external working material. With the continuous input of energy and the increase of deformation, a large amount of energy will be accumulated in the material. When the energy reaches a certain critical value ( ⁇ recrystallization activation energy), the material will be recrystallized. Recrystallization will first occur on the surface in direct contact with the work die and form a surface coarse-grained layer, and the formation of coarse-grained layer will seriously affect the uniformity and consistency of material properties.
  • Mn/Cr and Al can form submicron dispersed precipitated phases with Al, such as Al 6 Mn(Fe), Al(CrFe)Si and the like, which can effectively refine the grain structure to inhibit recrystallization during processing, stabilize the deformation structure in the product and reduce the thickness of coarse grain layer on the surface of the product, on the other hand, the plasticity of the alloy can also be improved.
  • Al such as Al 6 Mn(Fe), Al(CrFe)Si and the like
  • the plasticity of the alloy can also be improved.
  • too high Mn/Cr content will not only consume more main alloying element Si, reduce the strength of the alloy, but also significantly increase the quenching sensitivity of the alloy.
  • the Cr element is stronger than the Mn element in terms of overall performance, so the percentage by mass of Mn + 2Cr in the Al-Mg-Si alloy of the present invention needs to satisfy 0.40%-1.0%, and the percentage by mass of Cr is preferably 0.10%-0.20%.
  • the Al-Mg-Si alloy further includes V, V ⁇ 0.20% in percentage by mass. Further preferably, the percentage by mass of V is 0.05%-0.15%.
  • V can form peritectic dispersion phase with Al and other related elements in the melting and casting process, and distribute uniformly in the grains, which can effectively improve the dislocation movement channel in the deformation process and improve the impact toughness of the alloy; however, when too much V is added, the AlV phase tends to aggregate, which affects the uniformity of the alloy and deteriorates the toughness of the alloy.
  • the V-containing phase can effectively improve the high temperature properties and thermal stability of the alloy.
  • the Al-Mg-Si alloy further includes Cu, Cu ⁇ 0.25% in percentage by mass.
  • the Al-Mg-Si alloy further includes Ti, Ti ⁇ 0.10% in percentage by mass.
  • the other unavoidable impurity elements in the Al-Mg-Si alloy are each ⁇ 0.05%, and in total ⁇ 0.15%.
  • the Al-Mg-Si alloy has a multilayer structure of "the coarse-grained layer/fibrous tissue/ the coarse-grained layer/fibrous tissue/ the coarse-grained layer layer", and a thickness of a single-sided the coarse-grained layer ⁇ 0.3 ⁇ wall thickness.
  • the core fibrous tissue of the middle layer of the multilayer structure can effectively ensure the longitudinal bending performance and impact resistance of the product, while the coarse-grained layers on the inner and outer surfaces can improve the anisotropy and corrosion performance of the product to some extent.
  • the resulting aluminum alloy article of the present invention has a wall thickness of ⁇ 10 mm, and the properties may be low if the wall thickness is too thick to meet the yield strength requirement of 240 MPa.
  • the method for processing the high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy of the present invention includes an ageing treatment, the ageing treatment being a T6 treatment or a T7 treatment.
  • the high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy of the present invention may be processed using conventional aluminum alloys, including melting, casting, heat treatment, extrusion, and the like.
  • the raw materials are added as aluminum ingots, magnesium ingots, and intermediate alloy ingots such as Al-Si, Al-Mn, Al-Cr and Al-V.
  • the aluminum rod Prior to extrusion, the aluminum rod is preheated at 480-530 °C.
  • the high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy of the present invention has a yield strength of ⁇ 240 MPa and a good thermal stability. After the final alloy is annealed at 150°C/1000h, the yield strength of the final alloy is ⁇ 230 MPa and the bending toughness is excellent.
  • the bending angle of the alloy is ⁇ 75° in the transverse direction (perpendicular to the extrusion direction) and ⁇ 65° in the longitudinal direction (parallel to the extrusion direction).
  • the Al-Mg-Si alloys of the present invention are amenable to various other conventional aluminum alloy processing methods such as melting, casting, heat treatment, extrusion, etc.
  • the raw materials are added as aluminum ingots, magnesium ingots, and intermediate alloy ingots such as Al-Si, Al-Mn, Al-Cr and Al-V.
  • the refining agent is added during melting.
  • the aluminum rod is first preheated at 480-530°C.
  • composition of the Al-Mg-Si alloy as described in Examples 1 to 11 of table 2 was melted, semi-continuously cast into an ingot, the ingot was homogenized after cutting and tailing, extruded and cooled using a die with a corresponding section, and finally the extruded profile was subjected to ageing treatment using a T7 treatment.
  • Example 12 differs from Example 3 only in the ageing process, the ageing in Example 12 being a T6 treatment.
  • Comparative examples 1 to 4 differ from Example 1 only in the composition of the aluminum alloy, see Table 2 for details, and the preparation method is the same as that of Example 1.
  • Comparative examples 5 and 6 differ from Example 3 only in the ageing process, using natural ageing T4 and under-ageing T6X treatments, respectively.
  • the alloy samples with under-aging T6X showed only partial precipitation of solid solution alloy atoms, and had lower impact properties. Table 2.
  • Example 1 Examples 1-12 and Comparative examples 1 to 4 Alloy Components in Percentage by Mass (wt%) Alloy Mg Si Mn Cr V Cu Fe Ti Mg/Si free Mg+2Si free
  • Example 1 0.58 0.92 0.37 0.12 / 0.08 0.17 0.03 0.83 1.98
  • Example 2 0.75 0.80 0.35 0.14 / 0.12 0.18 0.04 1.30 1.90
  • Example 3 0.56 0.67 0.37 0.17 0.08 0.13 0.14 0.02 1.26 1.45
  • Example 4 0.83 0.87 0.27 0.15 / 0.15 0.18 0.02 1.24 2.17
  • Example 5 0.82 0.89 0.56 0.16 / 0.13 0.14 0.02 1.36 2.03
  • Example 6 0.81 0.88 0.29 0.08 / 0.11 0.17 0.03 1.16 2.21
  • Example 7 0.57 0.68 0.37 0.15 / 0.12 0.15 0.03 1.25 1.48
  • Example 8 0.55 0.67 0.36 0.16 0.10 / 0.14 0.02 1.22 1.45
  • Example 9 0.80 0.89
  • the product made of the Al-Mg-Si alloy of Example 1 was compared with the alloy product of Comparative example 1 in terms of crushing and cracking.
  • the comparative effect is shown in FIG. 1 .
  • the alloy product of Example 1 did not produce any through-cracks after crushing, while the alloy product of Comparative example 1 produced severe cracks after crushing, and some of the blocks were crushed and separated from the matrix. As can be seen, the crushing performance of the alloy of Example 1 is much better than that of the alloy of Comparative example 1.
  • the aluminum alloy articles of Examples 1-12 and Comparative examples 1-6 were tested for mechanical properties, flexural toughness, and crushing performance.
  • the bending toughness test standard is VDA238-100, the test sample size is 60mm ⁇ 60 mm, the test direction is parallel (longitudinal direction)/perpendicular (transverse direction) to the extrusion direction, when the maximum load of indenter decreases by 60 N, the test ends, and the specific test diagram is shown in FIG. 3 .
  • the crushing performance evaluation of aluminum alloys was done by quasi-static compression testing (in the direction of profile extrusion).
  • the crushing sample had an original length of 300 mm and was compressed to 100 mm at a speed of 100 mm/min.
  • the crushing performance of the alloy was evaluated by measuring the crack length on the sample after the test, with no through-crack being class A, the through-crack ⁇ 10mm being class B and the through-crack > 10mm being class C.
  • the crushing ratings A and B indicate excellent crushing performance.
  • Table 3 Mechanical properties, flexural toughness, crushing performance of the alloys of Examples 1-12 and Comparative examples 1-6.
  • the alloys of the present invention as compared with Comparative examples 1-2 and 4, has a great improvement in longitudinal bending toughness and crushing performance, in which the longitudinal bending angle is increased from 50° to more than 65°, and the crushing performance grade is increased from grade C to grade B and more. Meanwhile, the impact-resistant energy-absorbing Al-Mg-Si alloy of the present invention was also significantly improved in conventional mechanical properties (tensile strength, yield strength, elongation) compared to Comparative examples 3, 5 and 6, with an average tensile strength of ⁇ 265 MPa, an average yield strength of ⁇ 240 MPa, and an average elongation after fracture of ⁇ 11%.
  • the alloy of Comparative example 5 has excellent elongation, bending toughness and crushing properties, but the overall strength is too low, with a yield strength of only 115 MPa, less than 50% of the alloy of Example 1, indicating that the T4 process treatment does not achieve the desired strength effect.
  • the elongation and bending properties of the alloy of Comparative example 6 were good, but the crushing properties were very poor, and the alloy was difficult to form when crushed.
  • the aluminum alloy provided by the present invention not only has excellent conventional mechanical properties, with a yield strength of ⁇ 240 MPa and an elongation after fracture of ⁇ 10%; at the same time, the alloy has good bending toughness, the bending angle of the alloy in transverse direction (perpendicular to extrusion direction) is ⁇ 75 °, and the bending angle of the alloy in longitudinal direction (parallel to extrusion direction) is ⁇ 65 °; and the outstanding crushing and impact-resistant energy-absorbing properties, and the overall crushing properties of the alloy are all ⁇ B grade.

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Abstract

The present invention belongs to the technical field of aluminum alloy materials, and in particular relates to a high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy. The Al-Mg-Si alloy of the present invention comprises Mg 0.40-1.00%, Si 0.50-0.90%, Mn ≤ 0.60%, Cr ≤ 0.30%, Fe ≤ 0.25%, Al 96.8-99.1% in percentage by mass, wherein Si<sub>free</sub>=Si-0.3×(Mn+Fe+Cr), a mass ratio of Mg/Si<sub>free</sub> is 0.72-1.40, and a percentage by mass of Mg+2Si<sub>free</sub> is 1.40%-2.40%. The aluminum alloy not only has excellent conventional mechanical properties, but also has good bending toughness and outstanding crushing and impact-resistant energy-absorbing properties.

Description

    Technical Field
  • The present invention relates to the technical field of aluminum alloy materials, and in particular to a high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy.
    • Background Art
  • With the rapid development of human economy and society, energy problems and environmental problems emerge one after another, the sustainable development of green low-carbon environmental protection has become the target of development of the society at present. Motor vehicle fuel consumption accounts for a considerable proportion of the total crude oil consumption. The rapid development of the automotive industry not only poses a great challenge to China's oil supply, but also brings unprecedented pressure on the environment due to the emission of automobile exhaust. Energy saving and emission reduction is the key to the transformation and upgrading of automobile industry, and lightweight is an important means to achieve energy saving and emission reduction.
  • Al-Mg-Si alloy is a heat-treatable strengthened aluminum alloy, which has the advantages of high specific strength, good formability, excellent corrosion resistance and high weldability, and is an important material for realizing the light weight of automobiles. At present, Al-Mg-Si alloy is widely used in (vehicle body) structural parts, such as a vehicle body cover part, an engine piston, an anti-collision beam, a bumper, and the like. However, the service conditions of different components are different. In addition to improving the conventional mechanical properties of the materials, it is also necessary to improve the relevant performance under different service conditions of the components, such as a battery tray of a new energy vehicle and a key safety structural component such as an automobile anti-collision beam, which may be broken by external violent impact under service conditions, and even cause serious personnel and property losses. Therefore, the impact-resistant energy-absorbing properties of aluminum alloys used under such conditions are particularly important.
  • At present, the focus in industrial production is still strength of aluminum alloys, and the impact-resistant energy-absorbing properties of aluminum alloys are rarely studied. Although a Chinese patent No. CN 109504870 B provides a lightweight aluminum alloy for automobile anti-collision beam, a direct melt reaction technology together with an ultrasonic magnetic coupling field technology is used to regulate the synthesis reaction process and solidification process to obtain the composite material with uniform distribution of in-situ nanoparticles. Then the composite material is prepared by hot extrusion forming and heat treatment, the preparation process is complex, difficult, and costly, and it is not suitable for wide application. It is found from study 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. In addition, the microstructure of the material is also important to the impact-resistant energy-absorbing property.
    • Summary of the Invention
  • In view of the above-mentioned problems of the prior art, the present invention provides an Al-Mg-Si alloy having high bending toughness, impact toughness, crushing performance and energy absorption capacity while ensuring the strength, corrosion resistance and thermal stability of the alloy.
  • The above object of the present invention is achieved by the following technical solution: a high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy including Mg 0.40-1.00%, Si 0.50-0.90%, Mn ≤ 0.60%, Cr ≤ 0.30%, Fe ≤ 0.25%, Al 96.8-99.1% in percentage by mass, wherein Sifree=Si-0.3×(Mn+Fe+Cr), a mass ratio of Mg/Sifree is 0.72-1.40, and a percentage by mass of Mg+2Sifree is 1.40%-2.40%.
  • Mg and Si are the main additive elements of 6xxx alloy, and the second phase particles of β", β' and β are precipitated in the aging process to strengthen the Matrix. According to the latest study of Al-Mg-Si alloy in the aging process, the evolution of precipitated phases is as follows: supersaturated solid solution → GP Zone → β" → β'(B', U1, U2) → β. Among them, the β" phase has the best strengthening effect, which is the most significant strengthened precipitated phase in peak aged alloy. The β' phase is the main precipitated phase in overaged alloy, and has an inferior strengthening effect compared with β" phase; and the β phase is an equilibrium phase which is non-coherent with aluminum Matrix and has a limited strengthening effect.
  • Information about the precipitated phases in 6xxx alloy
    Precipitated phases Coherent with Matrix Chemical composition
    GP region Coherent lattice Mg2+XAl7-X-YSi2+Y
    β" Coherent lattice Mg5Si6
    β' Semi-coherent lattice Mg5Si3
    β Non-coherent lattice Mg2Si
  • In the composition design of 6xxx alloy, β(Mg2Si) phase is often considered to be the main strengthened precipitated phase in the alloy, so it is a misunderstanding to use Mg/Si atomic ratio = 2:1 as the principle of Mg, Si ratio design.
  • Because the best strengthening effect in Al-Mg-Si alloys is β" phase, their Mg/Si atomic ratio is 5/6. From the above, the reasonable composition design should refer to the atomic ratio of β" phase, i.e. Mg/Si atomic ratio = 5:6, which is 0.714: 1 if converted into a mass ratio (relative atomic mass of Mg is 24, and relative atomic mass of Si is 28).
  • In the Al-Mg-Si alloy, if the alloy ratio is lower than this ratio, there will be excess Si in the aluminum matrix. The excess Si is easy to segregate on the grain boundary and reduce the grain boundary bonding force. At the same time, it will also easily cause stress concentration as the source of crack initiation in the deformation process, which will damage the plastic and deformation energy absorption effect of the alloy, and a certain excess of Mg will help to improve the thermal stability of the alloy. However, if there is too much Mg excess, this part of the excess Mg will not effectively combine with Si to form strengthened precipitated phases, and the strengthening effect will be weakened. At the same time, too much Mg can also reduce the extrudability of the alloy (with the increase of Mg/Sifree value, the strain-hardening index of the alloy increases, and the workability of the alloy decreases) and bring high quenching sensitivity, which is not conducive to mass production. In the present invention, by comprehensively considering the consumption of Si element by Mn, Fe, Cr and other elements, the free silicon Sifree=Si-0.3 * (Mn + Fe + Cr) which can be used for forming a β" strengthened phase can be used for forming a β" strengthened phase. In the present invention, the mass ratio of Mg/Sifree is controlled to be 0.72-1.40, avoiding the presence of excess Si in the aluminum matrix while ensuring a certain amount of Mg, and avoiding the effect of excess Mg on the properties of the alloy.
  • Furthermore, the content of Mg and Si together determine the strength level of the Al-Mg-Si alloy. It has been found that the increase in yield strength with 1% Si alone is about twice that with 1% Mg, so the strength level of the alloy is directly determined by (Mg + 2Sifree). The Mg/Sifree mass ratio in the Al-Mg-Si alloys of the present invention is all above 0.72, i.e. Mg is excess. In the Mg-excess alloy, when the Si content increases, more strengthened precipitated phases are formed by combining with the excess Mg, which significantly improves the yield strength of the alloy. When the addition of Mg is continued, since there is no effective Si to combine with it to form strengthened phase, the nucleation rate of the strengthened precipitated phase can be increased only to some extent, thereby increasing the number of precipitated phases to a limited extent, which has a limited contribution to strength. However, when the content of Mg + 2Sifree is less than 1.40%, the number of precipitated phases is insufficient and the strengthening effect decreases, and the strength of the alloy cannot meet the development target (yield strength ≥ 240 MPa). The higher the value of Mg + 2Sifree is, the worse the deformation performance of the alloy is. When the total content of Mg + 2Sifree is more than 2.40%, the alloy is easy to crack in the crushing and drop hammer deformation energy absorption test, and the impact-resistant energy-absorbing performance is significantly reduced. Therefore, a reasonable total content of Mg + 2Sifree in the present invention is in the range of 1.40%-2.40%. In summary, in the Al-Mg-Si alloy of the present invention, Sifree = Si-0.3×(Mn+Fe+Cr), the mass ratio of Mg/Sifree is controlled to be 0.72-1.40, and the percentage by mass of Mg + 2Sifree still satisfies 1.40%-2.40%.
  • In the Al-Mg-Si alloy, the percentage by mass of Mn + 2Cr is 0.40%-1.0%. Further preferably, the percentage by mass of Cr is 0.10%-0.20%. Production and processing are a deformation process of external working material. With the continuous input of energy and the increase of deformation, a large amount of energy will be accumulated in the material. When the energy reaches a certain critical value (≥ recrystallization activation energy), the material will be recrystallized. Recrystallization will first occur on the surface in direct contact with the work die and form a surface coarse-grained layer, and the formation of coarse-grained layer will seriously affect the uniformity and consistency of material properties. Mn/Cr and Al can form submicron dispersed precipitated phases with Al, such as Al6Mn(Fe), Al(CrFe)Si and the like, which can effectively refine the grain structure to inhibit recrystallization during processing, stabilize the deformation structure in the product and reduce the thickness of coarse grain layer on the surface of the product, on the other hand, the plasticity of the alloy can also be improved. However, too high Mn/Cr content will not only consume more main alloying element Si, reduce the strength of the alloy, but also significantly increase the quenching sensitivity of the alloy. The Cr element is stronger than the Mn element in terms of overall performance, so the percentage by mass of Mn + 2Cr in the Al-Mg-Si alloy of the present invention needs to satisfy 0.40%-1.0%, and the percentage by mass of Cr is preferably 0.10%-0.20%.
  • The Al-Mg-Si alloy further includes V, V ≤ 0.20% in percentage by mass. Further preferably, the percentage by mass of V is 0.05%-0.15%. V can form peritectic dispersion phase with Al and other related elements in the melting and casting process, and distribute uniformly in the grains, which can effectively improve the dislocation movement channel in the deformation process and improve the impact toughness of the alloy; however, when too much V is added, the AlV phase tends to aggregate, 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 properties and thermal stability of the alloy. Thus for the Al-Mg-Si alloy of the present invention V ≤ 0.20%, preferably 0.05%-0.15%.
  • The Al-Mg-Si alloy further includes Cu, Cu ≤ 0.25% in percentage by mass.
  • The Al-Mg-Si alloy further includes Ti, Ti ≤ 0.10% in percentage by mass.
  • The other unavoidable impurity elements in the Al-Mg-Si alloy are each ≤ 0.05%, and in total ≤ 0.15%.
  • In the above-mentioned high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy, the Al-Mg-Si alloy has a multilayer structure of "the coarse-grained layer/fibrous tissue/ the coarse-grained layer/fibrous tissue/ the coarse-grained layer layer", and a thickness of a single-sided the coarse-grained layer ≤ 0.3 × wall thickness. The core fibrous tissue of the middle layer of the multilayer structure can effectively ensure the longitudinal bending performance and impact resistance of the product, while the coarse-grained layers on the inner and outer surfaces can improve the anisotropy and corrosion performance of the product to some extent.
  • Preferably, the resulting aluminum alloy article of the present invention has a wall thickness of ≤ 10 mm, and the properties may be low if the wall thickness is too thick to meet the yield strength requirement of 240 MPa.
  • The method for processing the high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy of the present invention includes an ageing treatment, the ageing treatment being a T6 treatment or a T7 treatment.
  • The high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy of the present invention may be processed using conventional aluminum alloys, including melting, casting, heat treatment, extrusion, and the like.
  • In the smelting process, the raw materials are added as aluminum ingots, magnesium ingots, and intermediate alloy ingots such as Al-Si, Al-Mn, Al-Cr and Al-V.
  • Prior to extrusion, the aluminum rod is preheated at 480-530 °C.
  • The high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy of the present invention has a yield strength of ≥ 240 MPa and a good thermal stability. After the final alloy is annealed at 150°C/1000h, the yield strength of the final alloy is ≥ 230 MPa and the bending toughness is excellent. The bending angle of the alloy is ≥ 75° in the transverse direction (perpendicular to the extrusion direction) and ≥ 65° in the longitudinal direction (parallel to the extrusion direction).
  • The present invention has the following advantageous effects compared to the prior art:
    1. (1) In the present invention, by optimizing the contents of the main alloying elements Mg/Si, Mn, Cr and even V in the Al-Mg-Si alloy, the bending toughness and crushing performance of the Al-Mg-Si alloy can be effectively improved under the premise of ensuring the strength, corrosion resistance and thermal stability of the alloy, and the impact-resistant energy-absorbing performance of the alloy can be significantly improved, and the alloy profile does not produce more than 30 mm of through-cracks under the impact action of a 250 Kg weight at a speed of 40 Km/h.
    2. (2) The Mg/Si ratio and the total amount of the main alloying element of the present invention are reasonably designed to increase the strain-hardening index of the alloy, improve the deformation behavior of the alloy, reduce the local stress concentration, and improve the deformation uniformity and energy absorption capacity while ensuring the strength of the alloy.
    3. (3) The Mn and Cr atoms of the present invention have a strong attraction effect with Al and Si atoms, and easily form dispersed second phase particles, which can effectively pin the migration of grain boundaries and inhibit the recrystallization of the alloy during processing; V is easy to react with Al and Si atoms to form intermetallic compounds, which are uniformly distributed in the grains, effectively improving the dislocation movement channel and deformation uniformity, and improving the plasticity and impact toughness of the alloy.
    Brief Description of the Drawings
    • FIG. 1 is a graph showing the comparative effect of crushing and cracking of a product made of the impact-resistant energy-absorbing Al-Mg-Si alloy of Example 1 and a product made of the alloy of Comparative example 1;
    • FIG. 2 is a high-speed impact test and results for the impact-resistant energy-absorbing Al-Mg-Si alloy product of Example 3;
    • FIG. 3 is a testing schematic diagram showing flexural toughness of impact-resistant energy-absorbing Al-Mg-Si alloy products.
    Detailed Description of the Invention
  • The technical solution of the present invention is further described below by means of specific examples. Unless otherwise specified, the raw materials used in the examples of the present invention are all common raw materials in the art, and the methods used in the examples are all conventional methods in the art. It should be understood that the particular Examples described herein are merely illustrative of the present invention and are not intended to limit the present invention in any way.
  • The Al-Mg-Si alloys of the present invention are amenable to various other conventional aluminum alloy processing methods such as melting, casting, heat treatment, extrusion, etc.
  • In the smelting process, the raw materials are added as aluminum ingots, magnesium ingots, and intermediate alloy ingots such as Al-Si, Al-Mn, Al-Cr and Al-V. The refining agent is added during melting.
  • It is extruded, the aluminum rod is first preheated at 480-530°C.
    • Examples 1 to 11
  • The composition of the Al-Mg-Si alloy as described in Examples 1 to 11 of table 2 was melted, semi-continuously cast into an ingot, the ingot was homogenized after cutting and tailing, extruded and cooled using a die with a corresponding section, and finally the extruded profile was subjected to ageing treatment using a T7 treatment.
    • Example 12
  • Example 12 differs from Example 3 only in the ageing process, the ageing in Example 12 being a T6 treatment.
    • Comparative examples 1 to 4
  • Comparative examples 1 to 4 differ from Example 1 only in the composition of the aluminum alloy, see Table 2 for details, and the preparation method is the same as that of Example 1.
    • Comparative examples 5 and 6
  • Comparative examples 5 and 6 differ from Example 3 only in the ageing process, using natural ageing T4 and under-ageing T6X treatments, respectively. The alloy samples with under-aging T6X showed only partial precipitation of solid solution alloy atoms, and had lower impact properties. Table 2. Examples 1-12 and Comparative examples 1 to 4 Alloy Components in Percentage by Mass (wt%)
    Alloy Mg Si Mn Cr V Cu Fe Ti Mg/Sifree Mg+2Sifree
    Example 1 0.58 0.92 0.37 0.12 / 0.08 0.17 0.03 0.83 1.98
    Example 2 0.75 0.80 0.35 0.14 / 0.12 0.18 0.04 1.30 1.90
    Example 3 0.56 0.67 0.37 0.17 0.08 0.13 0.14 0.02 1.26 1.45
    Example 4 0.83 0.87 0.27 0.15 / 0.15 0.18 0.02 1.24 2.17
    Example 5 0.82 0.89 0.56 0.16 / 0.13 0.14 0.02 1.36 2.03
    Example 6 0.81 0.88 0.29 0.08 / 0.11 0.17 0.03 1.16 2.21
    Example 7 0.57 0.68 0.37 0.15 / 0.12 0.15 0.03 1.25 1.48
    Example 8 0.55 0.67 0.36 0.16 0.10 / 0.14 0.02 1.22 1.45
    Example 9 0.80 0.89 0.53 0.26 / 0.13 0.14 0.02 1.38 1.96
    Example 10 0.57 0.68 0.08 0.04 / 0.12 0.15 0.03 0.97 1.75
    Example 11 0.57 0.69 0.36 0.17 0.07 0.28 0.15 0.03 1.23 1.50
    Example 12 0.56 0.67 0.37 0.17 0.08 0.13 0.14 0.02 1.26 1.45
    Comparative example 1 0.85 0.50 0.07 / 0.10 0.09 0.12 0.04 1.95 1.72
    Comparative example 2 0.48 0.78 0.06 / 0.13 0.12 0.16 0.07 0.68 1.89
    Comparative example 3 0.51 0.48 0.03 / / 0.01 0.17 0.03 1.23 1.34
    Comparative example 4 0.85 1.04 0.46 0.12 / 0.05 0.14 0.02 1.06 2.45
  • The product made of the Al-Mg-Si alloy of Example 1 was compared with the alloy product of Comparative example 1 in terms of crushing and cracking. The comparative effect is shown in FIG. 1. The alloy product of Example 1 did not produce any through-cracks after crushing, while the alloy product of Comparative example 1 produced severe cracks after crushing, and some of the blocks were crushed and separated from the matrix. As can be seen, the crushing performance of the alloy of Example 1 is much better than that of the alloy of Comparative example 1.
  • A high-speed impact test was performed on the product made of the Al-Mg-Si alloy of Example 3, and the test results are shown in FIG. 2. After high-speed impact (40 Km/h), the product of the alloy of Example 3 did not produce through-crack that is ≥ 20 mm, indicating that the alloy of Example 3 has excellent impact resistance.
  • The aluminum alloy articles of Examples 1-12 and Comparative examples 1-6 were tested for mechanical properties, flexural toughness, and crushing performance. The bending toughness test standard is VDA238-100, the test sample size is 60mm × 60 mm, the test direction is parallel (longitudinal direction)/perpendicular (transverse direction) to the extrusion direction, when the maximum load of indenter decreases by 60 N, the test ends, and the specific test diagram is shown in FIG. 3. The bending angle α of the alloy is closely related to the thickness t of the test sample, and the comparison is carried out by converting it into an angle α' of the thickness t0(2 mm) of the standard sample according to the following formula:
    α ′ = α t t 0
    Figure imgb0001
  • the crushing performance evaluation of aluminum alloys was done by quasi-static compression testing (in the direction of profile extrusion). The crushing sample had an original length of 300 mm and was compressed to 100 mm at a speed of 100 mm/min. The crushing performance of the alloy was evaluated by measuring the crack length on the sample after the test, with no through-crack being class A, the through-crack ≤ 10mm being class B and the through-crack > 10mm being class C. The crushing ratings A and B indicate excellent crushing performance. Table 3. Mechanical properties, flexural toughness, crushing performance of the alloys of Examples 1-12 and Comparative examples 1-6.
    Examples Performance
    Tensile strength Yield Strength Elongation Calculating bending angle Crushing performance
    MPa MPa % Lateral/° Longitudinal/° Grade
    Example 1 292 269 11 106 85 A
    Example 2 306 275 12 94 76 B
    Example 3 286 255 12 114 94 A
    Example 4 319 296 11 91 81 B
    Example 5 278 247 14 102 92 A
    Example 6 321 302 11 89 76 B
    Example 7 288 259 12 108 90 B
    Example 8 278 251 12 116 95 A
    Example 9 265 241 14 103 92 A
    Example 10 290 275 11 78 67 B
    Example 11 302 289 11 82 71 B
    Example 12 297 273 11 98 86 B
    Comparative example 1 275 260 11 113 53 C
    Comparative example 2 270 251 10 115 52 C
    Comparative example 3 266 235 12 112 98 A
    Comparative example 4 342 326 11 84 46 C
    Comparative example 5 219 115 23 124 119 A
    Comparative example 6 271 193 20 109 89 C
  • The alloys of the present invention, as compared with Comparative examples 1-2 and 4, has a great improvement in longitudinal bending toughness and crushing performance, in which the longitudinal bending angle is increased from 50° to more than 65°, and the crushing performance grade is increased from grade C to grade B and more. Meanwhile, the impact-resistant energy-absorbing Al-Mg-Si alloy of the present invention was also significantly improved in conventional mechanical properties (tensile strength, yield strength, elongation) compared to Comparative examples 3, 5 and 6, with an average tensile strength of ≥ 265 MPa, an average yield strength of ≥ 240 MPa, and an average elongation after fracture of ≥ 11%. The alloy of Comparative example 5 has excellent elongation, bending toughness and crushing properties, but the overall strength is too low, with a yield strength of only 115 MPa, less than 50% of the alloy of Example 1, indicating that the T4 process treatment does not achieve the desired strength effect. The elongation and bending properties of the alloy of Comparative example 6 were good, but the crushing properties were very poor, and the alloy was difficult to form when crushed.
  • In summary, the aluminum alloy provided by the present invention not only has excellent conventional mechanical properties, with a yield strength of ≥ 240 MPa and an elongation after fracture of ≥ 10%; at the same time, the alloy has good bending toughness, the bending angle of the alloy in transverse direction (perpendicular to extrusion direction) is ≥ 75 °, and the bending angle of the alloy in longitudinal direction (parallel to extrusion direction) is ≥ 65 °; and the outstanding crushing and impact-resistant energy-absorbing properties, and the overall crushing properties of the alloy are all ≥ B grade.
  • The above examples are not exhaustive of the point values within the parameters of the claimed technical solutions of the present invention, as well as the new technical solutions formed by the equivalent replacement of single or multiple technical features in the technical solutions of the examples, are also within the scope of the claimed invention, and all the parameters involved in the technical solutions of the present invention, if not specifically stated, do not have an irreplaceable unique combination with each other.
  • The specific examples described herein are merely illustrative of the spirit of the present invention and are not intended to limit the scope of the present invention. A person skilled in the art to which the present invention pertains may obtain similar or analogous technical solutions to the present invention by using equivalent substitution or equivalent transformation, all falling within the scope of the present invention.

Claims (10)

  1. A high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy, characterized in that the Al-Mg-Si alloy comprises Mg 0.40-1.00%, Si 0.50-0.90%, Mn ≤ 0.60%, Cr ≤ 0.30%, Fe ≤ 0.25%, Al 96.8-99.1% in percentage by mass, wherein Sifree=Si-0.3×(Mn+Fe+Cr), a mass ratio of Mg/Sifree is 0.72-1.40, and a percentage by mass of Mg+2Sifree is 1.40%-2.40%.
  2. The high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy according to claim 1, characterized in that a percentage by mass of Mn + 2Cr is 0.40%-1.0% of the Al-Mg-Si alloy.
  3. The high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy according to claim 1 or 2, characterized in that a percentage by mass of Cr is 0.10-0.20% of the Al-Mg-Si alloy.
  4. The high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy according to claim 1 or 2, characterized in that the Al-Mg-Si alloy further comprises V, V ≤ 0.20% in percentage by mass.
  5. The high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy according to claim 4, characterized in that a percentage by mass of V is 0.05-0.15%.
  6. The high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy according to claim 1 or 5, characterized in that the Al-Mg-Si alloy further comprises Cu, Cu ≤ 0.25% in percentage by mass.
  7. The high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy according to claim 6, characterized in that the Al-Mg-Si alloy further comprises Ti, Ti ≤ 0.10% in percentage by mass.
  8. The high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy according to claim 1 or 2 or 5 or 7, characterized in that the other unavoidable impurity elements in the Al-Mg-Si alloy are each ≤ 0.05%, and in total ≤ 0.15%.
  9. The high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy according to claim 1, characterized in that the Al-Mg-Si alloy has a multilayer structure of "macrocrystalline layer/fibrous tissue/macrocrystalline layer", and a thickness of a single-sided macrocrystalline layer ≤ 0.3 × wall thickness.
  10. A method for processing the high-strength and high-toughness impact-resistant energy-absorbing Al-Mg-Si alloy according to claim 1, characterized in that the method for processing the Al-Mg-Si alloy comprises an ageing treatment, the ageing treatment being a T6 treatment or a T7 treatment.
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