CN116065066B - Light high-strength corrosion-resistant aluminum alloy material and preparation method thereof - Google Patents
Light high-strength corrosion-resistant aluminum alloy material and preparation method thereof Download PDFInfo
- Publication number
- CN116065066B CN116065066B CN202310201048.8A CN202310201048A CN116065066B CN 116065066 B CN116065066 B CN 116065066B CN 202310201048 A CN202310201048 A CN 202310201048A CN 116065066 B CN116065066 B CN 116065066B
- Authority
- CN
- China
- Prior art keywords
- aluminum alloy
- alloy material
- alloy
- corrosion
- strength
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—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
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—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
Abstract
The invention discloses a light high-strength corrosion-resistant aluminum alloy material and a preparation method thereof. The aluminum alloy contains: 6.0-10.0wt% of Mg, 1.0-3.5wt% of Zn, 0.1-1.3wt% of Si, and Mn, cu, zr, sc, ti element with total content not more than 0.8wt%, wherein the balance is Al and unavoidable impurities. The preparation method of the alloy deformation processing material comprises the following steps: (1) manufacturing an aluminum alloy ingot; (2) Homogenizing heat treatment and/or preheating the obtained cast ingot; (3) Thermally processing the cast ingot into a required processing material form or a pre-processing material by a thermal deformation processing method; (4) Optionally reheating the pre-processed material, and cold deforming the pre-processed material into a required processed material form; (5) subjecting the processed material to solution heat treatment; (6) Rapidly cooling the solution heat treated processed material to room temperature; (7) And (5) aging the processing material to obtain the alloy aging processing material. The aluminum alloy material has excellent low density, high strength, corrosion resistance and damage resistance.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy and preparation and processing thereof, and particularly relates to an Al-Mg-Zn-Si series aluminum alloy. More specifically, the invention relates to a light high-strength corrosion-resistant Al-Mg-Zn-Si series aluminum alloy material and a preparation method thereof.
Background
The aluminum alloy has the characteristics of light specific gravity, high specific strength, easy processing, low cost and the like, and has very wide application in the fields of aerospace, transportation and the like. In order to better support the weight-reducing design of aluminum alloy structural members, further development of novel aluminum alloys with low density, high strength, corrosion resistance and damage resistance characteristics is needed.
Existing commercial wrought aluminum alloys primarily include 2xxx series (Al-Cu-Mg), 3xxx series (Al-Mn), 4xxx series (Al-Si), 5xxx series (Al-Mg), 6xxx series (Al-Mg-Si), and 7xxx series (Al-Zn-Mg-Cu) aluminum alloys. Wherein, the 5xxx series aluminum alloy (Al-Mg series aluminum alloy) takes Mg as a main alloy element, has medium strength, excellent corrosion resistance and welding performance, and is a second large aluminum alloy type with the dosage being only inferior to that of the 6xxx series aluminum alloy. The common Al-Mg aluminum alloys at home and abroad mainly comprise 5052, 5056, 5083, 5182, 5A02, 5A06 and the like, wherein the Mg content is generally 2.5-5.5 wt%, the Mg content is highest and the density is lowest in all commercial wrought aluminum alloys, and the density is reduced by approximately 0.4% when the Mg content is increased by 1 wt%.
The atomic radius difference between Mg and Al is 13%, and in the range of normal Mg content (2.5-5.5 wt.%), lattice distortion is caused by Mg atoms being dissolved in an Al matrix in a solid solution mode, solid solution strengthening of the alloy is realized, and work hardening of the alloy is realized in the deformation process, so that the alloy is a main strengthening mechanism of Al-Mg aluminum alloy. When the Mg content is further increased beyond the normal range, a large amount of beta-Al which is distributed in a net shape along the grain boundary is precipitated in the alloy matrix 3 Mg 2 The phase is not coherent with the matrix, can not produce dispersion strengthening effect, and the self-corrosion potential of beta phase is-1.085V, more negative than the self-corrosion potential of the alpha-Al matrix, namely-0.812V, will be firstlyCorrosion occurs in the substrate, causing severe spalling corrosion and intergranular corrosion. Therefore, in the case of Al-Mg-based aluminum alloys, the improvement of the alloy strength by simply increasing the Mg content generally results in serious deterioration of the overall properties of the alloy. If the content of Mg in the Al-Mg aluminum alloy can be increased, and a precipitation strengthening phase is formed by adding proper alloy elements and excessive Mg elements, the formation of beta phase which is in net distribution along the grain boundary precipitation is effectively inhibited, so that the strength of the Al-Mg aluminum alloy is greatly increased and the serious deterioration of corrosion resistance is avoided while the low density characteristic is maintained.
In order to enable the Al-Mg aluminum alloy to realize aging precipitation strengthening, the prior study shows that the T-Mg can be respectively formed by adding two alloying elements of Ag and Zn 32 (Al,Ag) 49 And T-Mg 32 (Al,Zn) 49 Precipitating the strengthening phase. From the sixty of the last century, studies have been carried out to find and confirm that the addition of trace Ag elements to Al-Mg alloy precipitates T-Mg 32( Al,Ag) 49 Precipitation strengthening phase, orientation relation of T phase and alpha-Al matrix is (010) T ∥(112) α Sum (001) T ∥(110) α Lattice parameter a=1.41 nm. Although the addition of Ag can effectively improve the precipitation strengthening reaction of the Al-Mg alloy, and the reasonable combination of pretreatment and aging treatment can lead the Al-Mg-Ag alloy to obtain good strength and plasticity matching, the Ag element is expensive and is difficult to be applied to industrial production in a large amount. At the beginning of the century, studies have been conducted to find that, after adding Zn element to a conventional Al-Mg-based aluminum alloy, T-Mg can be formed at the alloy grain boundary by a strengthening heat treatment 32 (Al,Zn) 49 The precipitated phase inhibits the formation of beta phase, thereby effectively improving the strength of Al-Mg aluminum alloy, avoiding the serious deterioration of the corrosion resistance of the Al-Mg aluminum alloy and showing important application value. For example: patent document CN104694800a discloses a high-strength, light-weight Al-Mg-Zn alloy, whose basic component ranges are: 6.0-10.0wt% of Mg, 3.0-5.0wt% of Zn, less than 2.0 wt% of Cu, less than 1.2wt% of Mn, less than 0.3 wt% of Fe, less than 0.3 wt% of Si, and adding at least one element in Cr, ti, zr, sc, hf, la, ce, pr, nd, wherein the addition amount of the single element is less than 0.5wt%, and the alloy has tensile strength in the state of T6The strength exceeds 530Mpa. Patent document CN104862551a discloses a method for preparing Al-Mg-Cu-Zn aluminum alloy and aluminum alloy sheet, which comprises the following basic components: 4.0-6.0wt% of Mg, 0.30-1.0wt% of Cu, 1.0-3.5wt% of Zn, less than or equal to 0.4wt% of Mn, less than or equal to 0.4wt% of Fe, less than or equal to 0.4wt% of Si, less than or equal to 0.2wt% of Cr, less than or equal to 0.1wt% of Ti, and the balance of Al and unavoidable impurities. Patent document CN110541096a discloses a high-strength weldable Al-Mg-Zn-Cu alloy and a method for preparing the same, the basic component ranges of which are: 4.3-7.0wt% of Mg, 2.5-5.0wt% of Zn, 0.4-1.2wt% of Cu, less than or equal to 0.3 wt% of Mn, less than or equal to 0.1wt% of Cr, less than or equal to 0.2wt% of Ti, less than or equal to 0.3 wt% of Zr, and the balance of Al and unavoidable impurities, wherein the mass ratio of Zn/Mg is less than or equal to 1.0, and the alloy strength is basically equivalent to that of the traditional 7xxx series aluminum alloy. Patent document CN103866167a discloses an aluminum alloy and an alloy sheet thereof, and a preparation method of the alloy sheet, wherein the basic component ranges are as follows: 5.5 to 6.0wt% of Mg, 0.6 to 1.2wt% of Zn, 0.1 to 0.2wt% of Cu, 0.6 to 1.0wt% of Mn, 0.05 to 0.25wt% of Zr, less than or equal to 0.1wt% of Cr, less than or equal to 0.15wt% of Ti, less than or equal to 0.25wt% of Fe, less than or equal to 0.2wt% of Si, and the balance of Al, by adding Zn, the alloy greatly reduces Al by adding Zn 3 Mg 2 The ability to continue to precipitate at grain boundaries exhibits higher strength and corrosion resistance than conventional AA5059-H321 and AA5059-H131 panels. Patent document CN104152759A discloses a high-strength corrosion-resistant Al-Mg alloy and a preparation process thereof, wherein the basic component ranges are as follows: 5.0-6.5 wt% of Mg, 1.2-2.5 wt% of Zn, 0.4-1.2 wt% of Mn, 0.05-0.25 wt% of Zr, less than or equal to 0.4 and wt wt% of Cu, less than or equal to 0.1wt% of Cr, less than or equal to 0.15 and wt wt% of Ti, less than or equal to 0.4wt% of Fe, less than or equal to 0.4 and wt wt% of Si, and the balance of Al and unavoidable impurities. Patent document CN114438356A discloses a high-strength corrosion-resistant high-toughness Al-Mg-Zn-Ag (-Cu) aluminum alloyThe basic components range is: 4.0-6.5 wt% of Mg, 3.0-5.5 wt% of Zn, 0.05-0.8 wt% of Ag, less than or equal to 1.0wt wt% of Cu, less than or equal to 0.15wt wt% of Mn, less than or equal to 0.15wt wt% of Ti, less than or equal to 0.20wt wt% of Zr, and the balance of Al and unavoidable impurities, wherein the alloy has improved strength and 3-grade intergranular corrosion.
Although development work of Al-Mg-Zn series alloys has achieved a certain result in recent years, there is still a great room for improvement in terms of excellent matching of key properties such as low density-high strength-corrosion resistance-damage resistance of alloys, for example: most research work is still focused on adding Zn element and the like to Al-Mg series aluminum alloy based on normal (or slightly higher) Mg content range, so that the Al-Mg series aluminum alloy loses the inherent low density advantage due to the addition of high-density Zn element and other elements while the alloy (strength) performance is improved, and the specific strength performance is not obvious compared with the traditional 2xxx series and 7xxx series aluminum alloys; in the research work of Al-Mg series aluminum alloy with high Mg content, the alloy still precipitates higher amount of beta-Al due to unreasonable addition types, addition amounts and the like of alloy elements 3 Mg 2 The phase and the grain boundary are distributed in a net shape, and the corrosion resistance of the alloy is deteriorated.
Therefore, further research and development of novel Al-Mg aluminum alloy materials with excellent matching of key performances such as low density, high strength, corrosion resistance, damage resistance and the like are necessary.
Disclosure of Invention
The invention is found through a great deal of research and industrial practice that the prior Al-Mg-Zn series aluminum alloy mainly takes Mg and Zn as main strengthening components and Mg 32 (Al,Zn) 49 The phase is a main strengthening phase, the precipitation sequence and the type of the main strengthening phase are relatively single, and ideal light-weight, high-strength, corrosion resistance and damage resistance comprehensive performance matching is difficult to obtain. If the prior Al-Mg-Zn series aluminum alloy is obviously improved in Mg content and added with a proper amount of Si in the form of main alloy elements, the alloy is further lightened, and simultaneously, an aging precipitation sequence is newly added, so that the aging strengthening response capability of the alloy can be obviously enhanced, and the beta-Al after the Mg content is greatly improved is further inhibited 3 Mg 2 Phase generationThe deterioration of the corrosion performance of the alloy is effectively avoided; further assisting in adopting Zr, mn, sc, cu and other elements to carry out microalloying is beneficial to refining of material structure, enhancement of precipitated phase and improvement of material performance. The component range and the proportion of each element of the alloy are subjected to fine optimization design, so that the alloy is an important guarantee for obtaining excellent performance matching. Through reasonable design, the alloy can cooperatively precipitate Mg in the aging process under the condition of ensuring light weight 32 (Al,Zn) 49 And Mg (magnesium) 2 Precipitation strengthening phase of Si structure and reducing excessive beta-Al under high Mg condition 3 Mg 2 The phase is separated out, so that the Al-Mg-Zn-Si series alloy of the invention can obtain high strength and toughness and simultaneously maintain good corrosion resistance.
The invention aims to overcome the defect of the matching of the comprehensive properties of the existing Al-Mg-Zn series aluminum alloy materials, and further improves the matching of the comprehensive properties by the optimized design of components and the preparation and processing technology on the basis of the existing alloys, thereby providing an ideal material for the Al-Mg-Zn-Si series aluminum alloy with light weight, high toughness and corrosion resistance for high-end manufacturing industry.
The first technical problem to be solved by the invention is to provide a light-weight, high-strength, corrosion-resistant and damage-resistant aluminum alloy material, and the second technical problem to be solved by the invention is to provide a preparation method of the aluminum alloy material; the third technical problem to be solved by the invention is to provide that the aluminum alloy material is welded with itself or other alloys to form a new product; the fourth technical problem to be solved by the invention is to propose that the aluminum alloy material is processed into a final component by various surface treatment, stamping forming and machining modes; a fifth technical problem to be solved by the present invention is to propose the use of said final component.
The invention relates to a light high-strength corrosion-resistant aluminum alloy material, which comprises the following components in percentage by weight: 6.0-10.0wt% of Mg, 1.0-3.5wt% of Zn, 0.1-1.3wt% of Si, and Mn, cu, zr, sc, ti element with total content not more than 0.8wt%, wherein the balance is Al and unavoidable impurities.
The first preferred scheme of the invention is as follows: the aluminum alloy contains: 6.3-9.9wt% of Mg, 1.1-2.9wt% of Zn, 0.15-1.0wt% of Si, and Mn, cu, zr, sc, ti element with the total content not exceeding 0.6wt%, wherein the balance is Al and unavoidable impurities.
As a second preferred aspect of the present invention, the aluminum alloy contains: 6.6-9.0wt% of Mg, 1.3-2.9wt% of Zn and 0.15-0.8wt% of Si.
As a third preferred aspect of the present invention, the aluminum alloy contains: 7.1-8.8 wt% of Mg, 1.5-2.8 wt% of Zn and 0.25-0.7 wt% of Si.
As a fourth preferred aspect of the present invention, the aluminum alloy contains: 7.3-8.5wt% of Mg, 1.5-2.7wt% of Zn and 0.4-0.6wt% of Si.
As a fifth preferred aspect of the present invention, in the aluminum alloy, the contents of Mg, zn, si satisfy the relation: (9 xMg)/(1 xSi) + (8 xZn) is not more than 2.5 and not more than 6.
As a sixth preferred aspect of the present invention, the aluminum alloy contains: mn 0.10-0.50wt%.
As a seventh preferred aspect of the present invention, the aluminum alloy contains: cu 0.10-0.50wt%.
As an eighth preferred aspect of the present invention, the aluminum alloy contains: 0.01-0.15 wt% of Ti.
As a ninth preferred aspect of the present invention, the aluminum alloy contains: zr 0.05-0.25wt%.
As a tenth preferred aspect of the present invention, the aluminum alloy contains: 0.05-0.30wt% of Sc; preferably, the following are satisfied: meanwhile, the alloy contains 0.05-0.20wt% of Zr; further preferred are the contents of Sc and Zr and the following: 0.15 The weight percent of (Sc+Zr) is less than or equal to 0.35 and wt percent.
As a tenth preferred aspect of the present invention, the above-mentioned aluminum alloy contains unavoidable impurities including elements that are unintentionally introduced as impurities during the production of the alloy ingot, as required to satisfy: fe is less than or equal to 0.40wt%, other impurity elements are each less than or equal to 0.20wt%, and the sum is less than or equal to 0.50wt%. Preferably, the following are satisfied: fe is less than or equal to 0.20wt%, other impurity elements are each less than or equal to 0.10wt%, and the sum is less than or equal to 0.25wt%. Further preferably, the following are satisfied: fe is less than or equal to 0.10wt%.
The invention also relates to a preparation method for producing the aluminum alloy material. The process of the aluminum alloy deformed processing material can be described as an alloy preparation-smelting-semi-continuous casting preparation ingot casting-homogenization heat treatment of ingot casting-heat deformation processing- (intermediate annealing) - (cold deformation processing) -solution treatment- (pre-deformation or straightening) -aging treatment-supply product "; the basic preparation process of the aluminum alloy castings can be described as "alloy formulation-smelting-cast forming of castings-solution treatment-aging treatment-commodity products".
The preparation method for producing the aluminum alloy deformation processing material comprises the following steps:
(1) Manufacturing a semi-continuous cast ingot according to the invention;
(2) Homogenizing heat treatment and/or preheating the obtained cast ingot;
(3) Hot deforming the ingot into a desired form of a processed material or into a pre-processed material by one or more hot deforming methods selected from extrusion, rolling and forging;
(4) Optionally reheating the pre-processed material, and cold deforming the pre-processed material into a required processed material form;
(5) Carrying out solution heat treatment on the processing material;
(6) Rapidly cooling the solution heat treated processed material to room temperature; and
(7) And (3) carrying out natural aging or artificial aging treatment on the cooled processing material to obtain the alloy aging processing material.
In the step (1), the ingot casting is manufactured by adopting smelting, degassing, impurity removal and semi-continuous casting modes; in the smelting process, mg and Zn are used as cores to accurately control element content, and the proportion among alloy elements is quickly supplemented and adjusted through on-line component detection and analysis, so that the whole ingot casting manufacturing process is completed. In a preferred aspect, 0.0002 to 0.005wt% Be is added as Al-Be intermediate during smelting to alter the oxide film properties to reduce oxidation burn-out and inclusions. In another preferred aspect, wherein in step (1), further comprising applying an electromagnetic field, an ultrasonic field, or mechanical agitation at or near the crystallizer site.
In step (2), the homogenization heat treatment is performed by a means selected from the group consisting of: (1) Carrying out single-stage homogenization heat treatment for a total time of 12-60 hours at a temperature of 360-490 ℃; and (2) performing two-stage or multi-stage homogenization heat treatment for a total time of 12-60 h at 360-500 ℃.
In the steps (3) and (4), the preheating temperature and the reheating temperature before each thermal deformation processing are 370-460 ℃ and the processing time is 1-8 h; in a preferred aspect, the cold deformation pass further comprises an intermediate annealing treatment of 350-450 ℃/0.5-6 hours.
In step (5), the solution heat treatment is further performed by adjusting the size of the crystals and the ratio of the recrystallized structure in the material according to the performance requirements, and by a mode selected from the group consisting of: (1) Carrying out single-stage, double-stage or multi-stage solution heat treatment for 0.5-8 h at 440-500 ℃; and (2) continuously heating and solution heat treating for 0.5-5 hours at 440-500 ℃. In a preferred aspect, a continuous elevated temperature solution heat treatment is employed, at a rate of less than or equal to 60 ℃/min.
In step (6), the work material is rapidly cooled to room temperature using a means selected from the group consisting of cooling medium spray quenching, immersion quenching, strong wind cooling, and combinations thereof.
In step (7), the artificial aging heat treatment is performed by a means selected from the group consisting of: (1) After quenching and cooling are completed, natural aging is carried out at room temperature, and the time is more than or equal to 48 and h; (2) Carrying out artificial aging treatment at 70-240 ℃ within 2h after quenching and cooling, wherein the total time is 6-60 h; and (3) after quenching and cooling are completed, adopting a mode of combining natural aging and artificial aging, wherein the artificial aging temperature is 70-240 ℃ and the time is 6-60 hours.
Between steps (6) and (7), the method may further comprise the steps of: straightening and/or pre-deforming the cooled processing material, straightening the cooled processing material by using roll straightening, stretching bending straightening and a combination thereof to improve the flatness of the processing material, and pre-deforming the cooled processing material by using stretching, compression and a combination thereof to reduce the residual stress formed by quenching and cooling, thereby being convenient for subsequent processing and application.
The processing material is a wire rod, a bar, a pipe, a thin plate, a thick plate or a forging product through the preparation method.
Wherein, the density of the light high-strength corrosion-resistant aluminum alloy material is less than or equal to 2.68g/cm 3 The tensile strength is more than or equal to 400MPa, and the peeling corrosion performance is not lower than EA grade. Preferably, the density of the aluminum alloy material is less than or equal to 2.66g/cm 3 The tensile strength is more than or equal to 410MPa, and the peeling corrosion performance is not lower than EA grade. Further preferably, the density of the aluminum alloy material is not more than 2.64g/cm 3 The tensile strength is more than or equal to 420MPa, and the peeling corrosion performance is not lower than PC grade.
The invention also relates to a preparation method for producing the aluminum alloy casting, which comprises the following steps:
(1) Preparing an aluminum alloy casting by adopting smelting, degassing, removing impurities, casting by using a sand mold or a metal mold, or casting by using a die casting mode; in the smelting process, mg and Zn are used as cores to accurately control element content, and the proportion among alloy elements is quickly supplemented and adjusted through on-line component detection and analysis, so that the whole casting preparation process is completed;
(2) Carrying out solution heat treatment on the obtained aluminum alloy casting: comprises the steps of carrying out single-stage, double-stage or multi-stage solution heat treatment on an aluminum alloy casting with the total time of 0.5-8 h at 440-500 ℃, or carrying out continuous heating solution heat treatment on the aluminum alloy casting with the total time of 0.5-5 h at 440-500 ℃;
(3) Carrying out natural aging or artificial aging heat treatment on the aluminum alloy casting; natural aging is carried out at room temperature, and the time is more than or equal to 48 and h; the artificial aging treatment is carried out at the temperature of 70-240 ℃ for 6-60 hours; or the natural aging and the artificial aging are combined, the artificial aging temperature is 70-240 ℃ and the time is 6-60 hours.
The aluminum alloy material is welded with the aluminum alloy material or other alloys to form a new product; the welding mode comprises friction stir welding, fusion welding, brazing, electron beam welding and laser welding. It can also be processed into a final component by various surface treatments, press forming, machining; the final component is a load-bearing structural member.
The invention has the beneficial effects that:
(1) The Al-Mg-Zn-Si aluminum alloy is subjected to component optimization design and is assisted by a matched preparation method, so that the high Mg content and Mg are realized 32 (Al,Zn) 49 And Mg (magnesium) 2 The Si structure phase double aging precipitation sequence is cooperatively strengthened, so that alloy strengthening response capability is remarkably improved, and the material has high strength and toughness and good corrosion resistance while light weight is ensured. The material has excellent comprehensive performance, is ideal material for various bearing structural members, and can meet the harsh requirements of various high-end manufacturing on light high-performance aluminum alloy materials.
(2) The invention realizes the Mg by adding the alloy element Si 2 The introduction of a new aging sequence of the Si structural phase provides a foundation for further improving the Mg content in the Al-Mg aluminum alloy, further develops the aging strengthening potential of the alloy, is beneficial to promoting the development of light weight in the fields of aerospace, transportation, automobiles, ships and the like, and has important social benefit and economic benefit.
(3) The material has the advantages of excellent performance, moderate price, simple and practical preparation method, strong operability, easy industrialized popularization and considerable market prospect.
Drawings
FIG. 1 is a TEM morphology photograph of an aged intragranular precipitated phase of the 22# alloy in example 2 of the present invention.
Fig. 2 is a TEM morphology photograph of the aging state grain boundary precipitation phase of the 22# alloy in example 2 of the present invention.
FIG. 3 is a comparison of specific strength versus fracture toughness for an alloy of the present invention versus a typical alloy of the prior art.
FIG. 4 is a comparison of specific strength versus corrosion resistance for an alloy of the present invention versus a typical prior art alloy.
Detailed Description
The technical scheme of the invention is further described in detail below by combining examples.
Example 1
Alloy extrusion plate strips were prepared on a laboratory scale to demonstrate the principles of the present invention. The composition of the experimental alloys is shown in table 1.
Round ingots with phi of 210mm are prepared by alloy smelting, degassing, removing impurities and simulating semi-continuous casting conditions which are well known in the industry, and the homogenization heat treatment system of the cast ingot is selected to be (400+/-5 ℃/12 h) + (475+/-5 ℃/24 h) and air-cooled. The extrusion blank with the specification phi of 180mm is obtained after peeling, milling and sawing. Preheating the blank at 440+ -10deg.C for 4 hr, and extruding to obtain 25×100mm specification plate belt, wherein the extrusion temperature is controlled at 400 deg.C. And (3) putting the extrusion plate strip into an air furnace at 450 ℃, carrying out continuous heating solution heat treatment at 450-480 ℃ for 90min, immediately carrying out 1.5-2% stretching straightening treatment after water quenching, and then respectively carrying out two-stage aging treatment of 90+/-5 ℃/24h+140+/-5 ℃/22-26 h according to the characteristics of the alloy.
Samples were cut according to the relevant methods, and the alloys were subjected to density (GB/T1423), tensile properties (GB/T16865), fracture toughness (GB/T4161), fatigue properties (GB/T3075), spalling corrosion (GB/T22639) and intergranular corrosion tests according to the relevant test criteria to evaluate as usual performance indexes of the alloys, and the results are shown in Table 2.
Table 1 experimental alloy compositions
Table 2 results of performance test of experimental alloys
As can be seen from table 2, alloys # 1, # 2, # 3, # 4, # 5, # 6, # 7, # 8, # 9, # 10, # 11, # 12, # 13 and # 14 all have a good match of density-strength-plasticity-fracture toughness-fatigue-corrosion resistance: density of not more than 2.66g/cm 3 The tensile strength is kept above 430MPa, the elongation after fracture is higher than 11.0%, and the fracture toughness is higher than 31.0MPa ‧ m 1/2 At a level, under the condition of constant stress of 241MPa, the strain ratio is 0.1The fatigue test is passed after 12 ten thousand cycles, the corrosion grade of the alloy spalling is N grade, and the corrosion grade between crystals is not lower than 3 grade. The properties of the 15# alloy, the 16# alloy, the 17# alloy, the 18# alloy, the 19# alloy and the 20# alloy do not meet the good matching of density, strength, plasticity, fracture toughness, fatigue property and corrosion resistance, wherein the 15# alloy has low Mg content, relatively low strength and deteriorated corrosion resistance; the 16# alloy has lower Mg and Zn contents and relatively lowest strength; the 17# alloy has high Mg and low Zn content, and the corrosion resistance is seriously deteriorated; in contrast, 18# alloy has low Mg and high Zn content, and has low elongation after breaking, low plasticity, deteriorated corrosion resistance and high density; the 19# alloy has high Mg and Zn content and high strength, but the plasticity and corrosion resistance are seriously deteriorated; the Si content of the alloy No. 20 is higher, the plasticity and fatigue performance of the alloy No. 20 are reduced, and the corrosion resistance is slightly reduced.
Example 2
An aluminum alloy rolled sheet was prepared in a laboratory, and the composition of the experimental alloy composition is shown in table 3.
A slab ingot with the thickness of 100mm is prepared by alloy smelting, degassing, removing impurities and simulating semi-continuous casting conditions which are well known in the industry, and the ingot is subjected to three-stage (400+/-5 ℃/12 h) + (475+/-5 ℃/24 h) + (500+/-5 ℃/12 h) homogenization heat treatment and air cooling respectively. The rolling blank with the thickness of 80mm is obtained after peeling, milling and sawing. Preheating the blank for 2 hours at 450+/-10 ℃, rolling for 3-4 times along the width direction of the slab ingot at the initial rolling temperature of 440 ℃, performing intermediate annealing treatment at 400+/-5 ℃/2 hours, and then reversing rolling and rolling to a thickness of about 20mm along the length direction of the slab ingot. The plate is put into an air furnace at 450 ℃, solution heat treatment is carried out at 450 ℃/30min+480 ℃/60min, 2% pre-stretching deformation treatment is carried out immediately after water quenching, and then two-stage aging treatment is carried out at 90+/-5 ℃/24 h+140+/-5 ℃/24h according to the characteristics of the alloy.
Samples were cut according to the relevant methods, and the alloys were subjected to density (GB/T1423), tensile properties (GB/T16865), fracture toughness (GB/T4161), fatigue properties (GB/T3075), spalling corrosion (GB/T22639) and intergranular corrosion tests according to the relevant test criteria to evaluate as usual performance indexes of the alloys, and the results are shown in Table 4.
TABLE 3 experimental alloy compositions
Note that: * this means that the element is an impurity element and is not added as an alloying element.
Table 4 results of Performance test of experimental alloys
As can be seen from Table 4, both the 21# and 22# alloys of the present invention exhibited good toughness and corrosion resistance matches, which are significantly better than the 23# alloy without Si addition. FIGS. 1 and 2 show TEM morphology photographs of the intergranular and intergranular precipitated phases of the 22# alloy, respectively, and it is evident that T-Mg is precipitated in the alloy at the same time 32 (Al,Zn) 49 Phase and beta' -Mg 2 The Si phase and the grain boundary precipitation phase are in break distribution, which is beneficial to the alloy to obtain high strength and toughness and good corrosion resistance.
Example 3
Aluminum alloy small-sized forgings were prepared on a pilot scale platform, and the alloy composition is shown in table 5.
Round ingots with phi of 530mm are prepared by alloy smelting, degassing and impurity removal well known in the industry through semi-continuous casting, and the homogenization heat treatment system of the cast ingot is selected to be (400+/-5 ℃/12 h) + (475+/-5 ℃/30 h) + (500+/-5 ℃/10 h) and air-cooled. And (5) peeling, milling and sawing to obtain extrusion blanks with the specification of phi 490 mm. Preheating the blank for 6 hours at 440+/-10 ℃, extruding and deforming to obtain an extrusion rod blank with the specification phi of 240mm, forging the extrusion rod blank in multiple ways to obtain a small-specification forging with the specification 60 multiplied by 500 multiplied by 900mm, and controlling the extrusion and forging deformation temperatures at 400-420 ℃. And (3) placing the forging into an air furnace at 450 ℃, carrying out solution heat treatment at 450 ℃/30min+480 ℃/90min, immediately carrying out pre-compression deformation treatment of 1.5-2.5% after water quenching, and then carrying out double-stage aging treatment of 90+/-5 ℃/24 h+140+/-5 ℃/28 h.
Samples were cut according to the relevant methods, and the alloys were subjected to density (GB/T1423), tensile properties (GB/T16865), fracture toughness (GB/T4161), fatigue properties (GB/T3075), spalling corrosion (GB/T22639) and intergranular corrosion tests according to the relevant test criteria to evaluate as usual performance indexes of the alloys, and the results are shown in Table 6.
TABLE 5 experimental alloy compositions
Table 6 results of Performance test of experimental alloys
As can be seen from table 6, the 24# alloy of the present invention exhibits a good toughness and corrosion resistance match.
Example 4
Aluminum alloy castings were prepared in the laboratory and the alloy composition is shown in table 7.
Preparing raw materials (high-purity aluminum, pure magnesium, pure zinc, al-Si intermediate alloy, al-Zr intermediate alloy and Al-Ti-B intermediate alloy refiner), baking a tool and a die, melting the high-purity aluminum at 730 ℃, adding the pure zinc, the Al-Si intermediate alloy and the Al-Zr intermediate alloy according to the conventional sequence, and stirring to completely melt the high-purity aluminum; cooling to 720 ℃, adding the Al-Ti-B intermediate alloy, stirring to be thick, and standing for 4-6 min; continuously cooling to 710 ℃, pressing pure magnesium wrapped by aluminum foil into aluminum alloy liquid by using a bell jar, and stirring to fully melt the aluminum alloy liquid; heating to 720 ℃, carrying out degassing, deslagging and refining, and carrying out stokehold inspection; standing for 30min at the casting temperature of 690 ℃, and casting the aluminum alloy melt into a baked metal mold, wherein the temperature of the mold is about 180-200 ℃; and (3) putting the prepared aluminum alloy casting into an air furnace at 470 ℃, carrying out solution heat treatment at 470+/-5 ℃/12 h+485+/-5 ℃/12h, carrying out natural aging for 48h after water cooling, and then carrying out double-stage aging treatment at 95+/-5 ℃/12 h+150+/-5 ℃/24 h.
Samples were cut according to the related methods, and the alloys were subjected to density (GB/T1423), tensile properties (GB/T16865), spalling corrosion (GB/T22639) and intergranular corrosion tests according to the related test criteria to evaluate as general performance indexes of the alloys, and the results are shown in Table 8.
TABLE 7 Experimental alloy compositions
Table 8 results of Performance test of experimental alloys
As can be seen from table 8, the 25# alloy of the present invention exhibits a high strength grade and a good strong plasticity and corrosion resistance match compared to the 26# alloy (Al-Mg-Si cast aluminum alloy) casting.
Example 5
The alloys were prepared on an industrial scale, and the composition of the alloys is shown in Table 9.
Round ingots with phi 480mm specifications are prepared by alloy smelting, degassing and impurity removal well known in the industry through semi-continuous casting, the homogenization heat treatment system of the 27# alloy cast ingots, the 28# alloy cast ingots and the 29# alloy cast ingots is selected to be (405+/-5 ℃/10 h) + (475+/-18 ℃/18 h) + (505+/-5 ℃/12 h), and the other alloys are subjected to air cooling by adopting the conventional annealing system of 470-500 ℃/36 h. And (5) peeling, milling and sawing to obtain the extrusion blank with the specification phi 450 mm. Preheating the blank at 430+/-10 ℃ for 4 hours, and performing extrusion deformation to obtain a large-sized extrusion plate belt with the thickness of 35 multiplied by 400mm, wherein the extrusion temperature is controlled to be about 380+/-10 ℃. According to the characteristics of the alloy, proper technological parameters are selected within the range of 475-540 ℃, solution heat treatment is carried out on the alloy plate strip, 1.5-2% of stretching straightening treatment is immediately carried out after water quenching, then typical ageing treatment in an ageing state is carried out on the 27# alloy, the 28# alloy and the 29# alloy, double-stage ageing treatment of 90+/-3 ℃/24 h+140+/-3 ℃/24h is carried out on the 30# alloy, 121+/-5 ℃/6h+163+/-5 ℃/20h is carried out on the 31# alloy, 190+/-5 ℃/12h is carried out on the 32# alloy, and better comprehensive performance matching is obtained on the alloy material.
Samples were cut according to the relevant methods, and the alloys were subjected to density (GB/T1423), tensile properties (GB/T16865), fracture toughness (GB/T4161), fatigue properties (GB/T3075), spalling corrosion (GB/T22639) and intergranular corrosion tests according to the relevant test criteria to evaluate as usual performance indexes of the alloys, and the results are shown in Table 10.
Table 9 experimental alloy compositions
Note that: the composition points of # 30, # 31 and # 32 were taken as the median values of the 7050, 2024 and 6005A aluminum alloys, respectively, in the international association of aluminum registration composition ranges.
Table 10 results of Performance test of experimental alloys
As can be seen from Table 10, the 27# alloy, the 28# alloy and the 29# alloy of the present invention all have low density, good matching of toughness and corrosion resistance, have obvious comprehensive performance advantages, have low density, have high strength level and maintain high fracture toughness, fatigue resistance and corrosion resistance compared with the 7050 alloy (30 # alloy), the 2024 alloy (31 # alloy) and the 6005A alloy (32 # alloy) prepared under the same conditions.
Fig. 3 and 4 show the specific strength versus fracture toughness and corrosion resistance of alloys 27#, 28#, 29#, 7050 alloy (30 # alloy), 2024 alloy (31 # alloy) and 6005A alloy (32 # alloy), respectively, of the present invention. It can be seen that the alloy articles of the present invention exhibit a good mechanical-corrosion performance match.
Claims (35)
1. A lightweight high strength corrosion resistant aluminum alloy material, wherein the aluminum alloy comprises: 6.0-9.9wt% of Mg, 1.1-3.01wt% of Zn, 0.1-1.15wt% of Si and at least one Mn, cu, zr, sc, ti element with the total content not exceeding 0.8wt%, wherein the balance is Al and unavoidable impurities;
the density of the aluminum alloy material is less than or equal to 2.68g/cm 3 The tensile strength is more than or equal to 400MPa, and the peeling corrosion performance is not lower than EA grade.
2. The light weight, high strength and corrosion resistant aluminum alloy material of claim 1, wherein said aluminum alloy comprises: 6.3-9.9wt% of Mg, 1.1-2.9wt% of Zn, 0.15-1.0wt% of Si, and Mn, cu, zr, sc, ti element with the total content not exceeding 0.6wt%, wherein the balance is Al and unavoidable impurities.
3. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 2, wherein said aluminum alloy comprises: 6.6-9.0wt% of Mg, 1.3-2.9wt% of Zn and 0.15-0.8wt% of Si.
4. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 2, wherein said aluminum alloy comprises: 7.1-8.8 wt% of Mg, 1.5-2.8 wt% of Zn and 0.25-0.7 wt% of Si.
5. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 2, wherein said aluminum alloy comprises: 7.3-8.5wt% of Mg, 1.5-2.7wt% of Zn and 0.4-0.6wt% of Si.
6. The light-weight high-strength corrosion-resistant aluminum alloy material according to claim 2, wherein the contents of Mg, zn, si in the aluminum alloy satisfy the relation: (9 xMg)/(1 xSi) + (8 xZn) is not more than 2.5 and not more than 6.
7. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 2, wherein said aluminum alloy comprises: mn 0.10-0.50wt%.
8. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 2, wherein said aluminum alloy comprises: cu 0.10-0.50wt%.
9. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 2, wherein said aluminum alloy comprises: 0.01-0.15 wt% of Ti.
10. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 2, wherein said aluminum alloy comprises: zr 0.05-0.25wt%.
11. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 2, wherein said aluminum alloy comprises: 0.05-0.30wt% of Sc.
12. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 11, wherein said aluminum alloy comprises: 0.05-0.20wt% of Sc.
13. The light-weight high-strength corrosion-resistant aluminum alloy material according to claim 12, wherein in said aluminum alloy, the sum of Sc and Zr contents satisfies: 0.15 The weight percent of (Sc+Zr) is less than or equal to 0.35 and wt percent.
14. The light-weight high-strength corrosion-resistant aluminum alloy material according to claim 2, wherein the unavoidable impurities include elements that are unintentionally carried in as impurities during the production of the alloy ingot, wherein Fe is 0.40 wt.% or less, each of other impurity elements is 0.20 wt.% or less, and the sum is 0.50 wt.% or less in the aluminum alloy.
15. The lightweight high strength corrosion resistant aluminum alloy material as set forth in claim 14, wherein said unavoidable impurities include elements that are unintentionally carried in as impurities during the manufacture of the alloy ingot, said aluminum alloy having Fe of 0.20 wt.% or less, each of the other impurity elements of 0.10 wt.% or less, and the sum of the other impurity elements of 0.25 wt.% or less.
16. The light-weight high-strength corrosion-resistant aluminum alloy material according to claim 15, wherein Fe is 0.10wt% or less in the aluminum alloy.
17. A method of producing a wrought aluminum alloy material, comprising the steps of:
(1) Producing an ingot of the aluminum alloy material according to any one of claims 1 to 16;
(2) Homogenizing heat treatment and/or preheating the obtained cast ingot;
(3) Hot deforming the ingot into a desired form of a processed material or into a pre-processed material by one or more hot deforming methods selected from extrusion, rolling and forging;
(4) Optionally reheating the pre-processed material, and cold deforming the pre-processed material into a required processed material form;
(5) Carrying out solution heat treatment on the processing material;
(6) Rapidly cooling the solution heat treated processed material to room temperature; and
(7) And (3) carrying out natural aging or artificial aging treatment on the cooled processing material to obtain the alloy aging processing material.
18. The method of claim 17, wherein in step (1), the ingot is produced by smelting, degassing, inclusion removal and semi-continuous casting; in the smelting process, mg and Zn are used as cores to accurately control element content, and the proportion among alloy elements is quickly supplemented and adjusted through on-line component detection and analysis, so that the whole ingot casting manufacturing process is completed.
19. The method according to claim 18, wherein in the step (1), 0.0002 to 0.005wt% Be is added in the form of al—be intermediate during smelting to change the oxide film properties, reduce oxidation burn-out and inclusions.
20. The method of claim 18, further comprising, in step (1), applying an electromagnetic field, an ultrasonic field, or mechanical agitation at or near the crystallizer site.
21. The method of claim 17, wherein in step (2), the homogenizing heat treatment is performed by a means selected from the group consisting of:
(1) Carrying out single-stage homogenization heat treatment for a total time of 12-60 hours at a temperature of 360-490 ℃; and
(2) And (3) performing two-stage or multi-stage homogenization heat treatment for 12-60 hours in the total temperature range of 360-500 ℃.
22. The method of claim 17, wherein in the steps (3) and (4), the preheating temperature and the reheating temperature before each heat deformation process are 370-460 ℃ and the treatment time is 1-8 hours.
23. The method of claim 17, wherein in step (4), the cold deformation pass further comprises an intermediate annealing treatment of 350 to 450 ℃/0.5 to 6 hours.
24. The method of claim 17, wherein in step (5), the solution heat treatment is performed by further adjusting the ratio of the sub-crystalline size and the recrystallized structure of the material according to the performance requirements, and by a means selected from the group consisting of:
(1) Carrying out single-stage, double-stage or multi-stage solution heat treatment for 0.5-8 h at 440-500 ℃; and
(2) And (3) carrying out continuous heating solution heat treatment for 0.5-5 hours at the temperature of 440-500 ℃.
25. The method of claim 24, wherein the solution heat treatment is performed at a continuous elevated temperature of 60 ℃/min or less.
26. The method of claim 17, wherein in step (6), the work piece is rapidly cooled to room temperature using a means selected from the group consisting of cooling medium spray quenching, submerged quenching, strong wind cooling, and combinations thereof.
27. The method according to claim 17, wherein in step (7) the artificial aging heat treatment is performed by means selected from the group consisting of:
(1) After quenching and cooling are completed, natural aging is carried out at room temperature, and the time is more than or equal to 48 and h;
(2) Carrying out artificial aging treatment at 70-240 ℃ within 2h after quenching and cooling, wherein the total time is 6-60 h; and
(3) After quenching and cooling are completed, natural aging and artificial aging are combined, and the artificial aging temperature is 70-240 ℃ and the time is 6-60 hours.
28. The method of claim 17, further comprising, between steps (6) and (7), the steps of: straightening and/or pre-deforming the cooled processing material, straightening the cooled processing material by using roll straightening, stretching bending straightening and a combination thereof to improve the flatness of the processing material, and pre-deforming the cooled processing material by using stretching, compression and a combination thereof to reduce the residual stress formed by quenching and cooling, thereby being convenient for subsequent processing and application.
29. The method of claim 17, wherein the work material is a wire, rod, tube, sheet, thick plate, or forging product.
30. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 29, wherein the aluminum alloy material has a density of 2.66g/cm or less 3 The tensile strength is more than or equal to 410MPa, and the peeling corrosion performance is not lower than EA grade.
31. The light weight, high strength and corrosion resistant aluminum alloy material according to claim 30, wherein the aluminum alloy material has a density of 2.64g/cm or less 3 The tensile strength is more than or equal to 420MPa, and the peeling corrosion performance is not lower than PC grade.
32. A method of producing a cast aluminum alloy material, comprising the steps of:
(1) Preparing an aluminum alloy casting of the aluminum alloy material according to any one of claims 1-16 by smelting, degassing, removing impurities, casting with a sand mold, or casting with a metal mold, or die casting; in the smelting process, mg and Zn are used as cores to accurately control element content, and the proportion among alloy elements is quickly supplemented and adjusted through on-line component detection and analysis, so that the whole casting preparation process is completed;
(2) Carrying out solution heat treatment on the obtained aluminum alloy casting: comprises the steps of carrying out single-stage, double-stage or multi-stage solution heat treatment on an aluminum alloy casting with the total time of 0.5-8 h at 440-500 ℃, or carrying out continuous heating solution heat treatment on the aluminum alloy casting with the total time of 0.5-5 h at 440-500 ℃;
(3) Carrying out natural aging or artificial aging heat treatment on the aluminum alloy casting; natural aging is carried out at room temperature, and the time is more than or equal to 48 and h; the artificial aging treatment is carried out at the temperature of 70-240 ℃ for 6-60 hours; or the natural aging and the artificial aging are combined, the artificial aging temperature is 70-240 ℃ and the time is 6-60 hours.
33. A product characterized in that the product is formed by welding the light high-strength corrosion-resistant aluminum alloy material according to any one of claims 1-16 and 30-31 or the light high-strength corrosion-resistant aluminum alloy material manufactured by the method according to any one of claims 17-29 and 32 with the light high-strength corrosion-resistant aluminum alloy material or other alloys; the welding mode comprises friction stir welding, fusion welding, brazing, electron beam welding and laser welding.
34. A final member characterized in that the light-weight high-strength corrosion-resistant aluminum alloy material according to any one of claims 1 to 16, 30 to 31 or the light-weight high-strength corrosion-resistant aluminum alloy material manufactured by the method according to any one of claims 17 to 29, 32 is processed into a final member by various surface treatments, press forming, machining.
35. The final element according to claim 34, wherein said final element is a load bearing structure.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310201048.8A CN116065066B (en) | 2023-03-06 | 2023-03-06 | Light high-strength corrosion-resistant aluminum alloy material and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310201048.8A CN116065066B (en) | 2023-03-06 | 2023-03-06 | Light high-strength corrosion-resistant aluminum alloy material and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN116065066A CN116065066A (en) | 2023-05-05 |
| CN116065066B true CN116065066B (en) | 2023-07-07 |
Family
ID=86175032
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202310201048.8A Active CN116065066B (en) | 2023-03-06 | 2023-03-06 | Light high-strength corrosion-resistant aluminum alloy material and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN116065066B (en) |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6959476B2 (en) * | 2003-10-27 | 2005-11-01 | Commonwealth Industries, Inc. | Aluminum automotive drive shaft |
| JP6418714B2 (en) * | 2014-03-19 | 2018-11-07 | 株式会社Uacj | Aluminum alloy clad material and method for producing the same, heat exchanger using the aluminum alloy clad material, and method for producing the same |
| CN104313413B (en) * | 2014-10-24 | 2016-08-24 | 北京科技大学 | A kind of Al-Mg-Zn system alloy and the preparation method of sheet alloy thereof |
| CN108359920B (en) * | 2018-01-25 | 2019-09-10 | 北京科技大学 | A kind of short route prepares the deformation heat treatment method of the anti-corrosion Al-Mg-Zn aluminium alloy of high-strength height |
| CN110714149A (en) * | 2019-11-14 | 2020-01-21 | 台州欧本汽摩配件有限公司 | Electric vehicle hub and machining method thereof |
-
2023
- 2023-03-06 CN CN202310201048.8A patent/CN116065066B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN116065066A (en) | 2023-05-05 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP6458003B2 (en) | Aluminum alloy material suitable for manufacturing automobile body panel and method for producing the same | |
| EP3394304B1 (en) | Method for producing a heat treatable aluminium alloy with improved mechanical properties | |
| EP2386667B1 (en) | Aluminum alloy product adapted to produce structure piece and producing method thereof | |
| JP4101749B2 (en) | Weldable high strength Al-Mg-Si alloy | |
| CN103266246B (en) | Be suitable to the Al-Cu-Li alloy product of aerospace applications | |
| CN102796925B (en) | High-strength die-casting aluminum alloy for pressure casting | |
| CN100482829C (en) | Manufacturing method of aluminum alloy plate for train compartment | |
| CN113293273B (en) | Processing method of 2xxx series aluminum alloy bar and wire for fastener | |
| EP3390678A1 (en) | High strength 6xxx aluminum alloys and methods of making the same | |
| WO2009062866A1 (en) | Al-mg-zn wrought alloy product and method of its manufacture | |
| EP1000179A1 (en) | HIGH STRENGTH Al-Mg-Zn-Si ALLOY FOR WELDED STRUCTURES AND BRAZING APPLICATION | |
| KR20090127185A (en) | Alloy composition and preparation thereof | |
| CN110331319A (en) | It is a kind of containing scandium and the high-strength of erbium, high-ductility Alcoa and preparation method thereof | |
| CN110947762A (en) | Preparation method of 308 aluminum alloy three-layer composite plate for vacuum brazing | |
| CN113718139A (en) | Al-Mg-Si-Cu-Mn aluminum alloy and processing method of extrusion material thereof | |
| CN114438356A (en) | Preparation method of high-strength, corrosion-resistant and high-toughness Al-Mg-Zn-Ag (-Cu) aluminum alloy | |
| CA2997819C (en) | High-strength aluminum-based alloy and method for producing articles therefrom | |
| CA2741587C (en) | Aluminium alloy products for manufacturing structural components and method of producing the same | |
| CN110408805B (en) | Aluminum alloy bar and preparation method thereof | |
| CN116065066B (en) | Light high-strength corrosion-resistant aluminum alloy material and preparation method thereof | |
| WO2021003528A1 (en) | Aluminium alloys | |
| CN115401293A (en) | Application of aluminum-magnesium-silicon extrusion plate capable of MIG welding of dissimilar aluminum alloy | |
| CN117535570A (en) | Aluminum-magnesium alloy plate with high formability and high welding performance and preparation method thereof | |
| CN115522107A (en) | 7-series high-strength high-bending-resistance anti-collision cross beam for automobile and manufacturing method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |