CN111270115A - Method for manufacturing high-strength 7000 series aluminum alloy section for automobile body - Google Patents
Method for manufacturing high-strength 7000 series aluminum alloy section for automobile body Download PDFInfo
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- CN111270115A CN111270115A CN202010265792.0A CN202010265792A CN111270115A CN 111270115 A CN111270115 A CN 111270115A CN 202010265792 A CN202010265792 A CN 202010265792A CN 111270115 A CN111270115 A CN 111270115A
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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- C22C1/02—Making non-ferrous alloys by melting
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- 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
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- 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
- C22F1/053—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 zinc as the next major constituent
Abstract
The invention provides a manufacturing method of a high-strength 7000 series aluminum alloy section for an automobile body, which comprises the following alloy elements in percentage by mass: 0.119 to 0.138 percent of Si, 0.148 to 0.17 percent of Fe, 0.05 to 0.19 percent of Cu, 0.04 to 0.10 percent of Mn, 0.72 to 0.99 percent of Mg, 0.05 to 0.10 percent of Cr, 5.55 to 6.0 percent of Zn, 0.15 to 0.22 percent of Zr, 0.02 to 0.04 percent of Ti, less than or equal to 0.05 percent of other single elements, less than or equal to 0.15 percent of other elements, and the balance of aluminum; wherein the Zn/Mg ratio is controlled to be 6-8; the processing technology comprises the steps of smelting, purifying treatment, casting into a rod, homogenizing annealing, extruding, cooling, stretching, natural aging and artificial aging treatment. The section obtained by the manufacturing method provided by the invention has ultrahigh mechanical property and good corrosion resistance, fatigue resistance and crushing resistance, and is very suitable for mass production of parts such as aluminum alloy energy absorption boxes, front and rear longitudinal beams, doorsills, door anti-collision beams and the like used in automobile bumper systems.
Description
Technical Field
The invention relates to the field of aluminum alloy materials, in particular to a manufacturing method of a high-strength 7000 series aluminum alloy section for an automobile body.
Background
7000 series (Al-Zn-Mg-Cu) aluminum alloy profiles are widely used in aerospace, high-speed rail and high-end automobile manufacturing, and the production and manufacturing of such aluminum alloy profiles generally include: smelting, casting, homogenizing, extruding, natural aging, bending, welding and forming and artificial aging heat treatment.
7000-series aluminum alloys tend to form relatively coarse grain structures and coarse eutectic structures during casting, and the causes of the formation of coarse grain structures are generally classified into two types: (1) the casting temperature is too high or the heat preservation time of the aluminum liquid is too long, so that few nucleation particles are generated during solidification and the grain refining effect is not uniform, and the grains grow; (2) insufficient cooling strength results in low freezing supercooling degree, and causes coarsening of the grain structure. The coarse eutectic structure is difficult to completely eliminate by using a traditional homogenization system, and has adverse effects on the crushing performance, impact toughness, corrosion performance, welding performance and fatigue performance of the extruded profile.
In addition, after the 7000 series aluminum alloy is extruded into a profile, the grain structure is mainly fibrous crystal, the recrystallization percentage is small, and the cooling rate of the profile is increased, so that the mechanical property of the profile can be improved, and the property uniformity of different wall thicknesses can be improved. The effects of reducing recrystallization fraction and improving mechanical properties of the fiber crystals can be achieved by properly controlling the extrusion temperature, speed, cooling mode and die temperature. By further controlling the natural aging and artificial aging processes, the size and the number of the precipitated phases in the crystal interior and the crystal boundary can be effectively regulated and controlled, so that the material has better comprehensive performance.
The inventors studied the prior art and exemplified the nominal chemical composition of 7003 (national standard) aluminum alloy for vehicle bodies as shown in table 1 below.
TABLE 1 Mass% of alloy elements of 7003 (national standard) aluminum alloy for vehicle bodies
The prior casting smelting and extrusion process technology has the following problems:
(1) the Zn/Mg ratio is unreasonable in design, and the component design is high; the design of trace elements is unreasonable, the contents of Cr, Ti and Mn are too high, and the contents of Si and Fe are also larger; the Cu content also needs to be further adjusted.
(2) The quality of molten aluminum or aluminum ingots used for smelting and the quality of master alloys are common.
(3) The casting process parameters are unreasonable, the addition mode and time of the intermediate alloy need to be improved, for example, the addition of Cu element in the initial smelting stage is easy to cause non-uniform melting, the burning loss of Al-Mg intermediate alloy is serious, and MgO oxide film is easy to generate, so that the intermediate alloy is not suitable for being added in the initial smelting stage. The heat preservation standing time is not strict enough, and the heat preservation time is far more than 20-30min, so that hydrogen absorption and heavy element precipitation are easily caused. Too high a casting temperature may result in insufficient cooling strength, resulting in the cast aluminum bar having too short a cooling time in the center to form coarse eutectic structures and large-grained inclusion phases, reducing the processing, welding, fatigue and crushing properties of the material.
(4) The homogenization process is unreasonable: at present, a high-temperature short-time single-stage or double-stage homogenization heat treatment process is generally adopted, a homogenizing furnace cannot realize gradient temperature rise, and Al capable of inhibiting recrystallization is caused3Zr particles cannot be dispersed and separated out uniformly.
(5) Unreasonable parameters of the extrusion process: the extrusion temperature is too low, the surface quality of an extruded product is poor, the extrusion speed is too low, the service life of a die is rapidly reduced, and the bridge position of the die is cracked; al precipitated by dispersion due to overhigh extrusion temperature3Zr loses the function of inhibiting recrystallization, the temperature of the material outlet exceeds the solidus line of the Zr, the surface coarse crystal layer is enlarged, and the materialThe material is over-burnt, the comprehensive performance is sharply reduced, and the collision safety and the fatigue corrosion resistance of the automobile alloy in the whole life cycle cannot be realized;
(6) the extrusion die is unreasonable in material selection heat treatment and design: h13 hot work die steel or CrMnMo which is forged and remelted is not selected as the material of the extrusion die, and the spheroidizing annealing temperature of the forging is too high to cause the material structure to be loose; oil quenching or a quenching medium with a lower cooling rate is not selected for heat treatment quenching; the heat treatment tempering times are unreasonable in design, and the tempering temperature and time of each stage are unreasonable in control; the number of welding lines in the design of the extrusion die is large, so that the number of bridge positions is increased; the bridge position design is according to the traditional design idea, and is thick and the diversion trench is not smooth enough; the coarse grains at the welding line position of the extruded section are serious, the mechanical property is higher, the toughness is poorer, the reduction of the bending and welding properties is obvious, and the comprehensive performance of the final part is not favorably achieved.
(7) The heat treatment process is unreasonable: the final aging heat treatment can be carried out by various processes such as T6/T79/T76/T73, and most manufacturers cannot understand the aging process, so that the material cannot meet the performance requirement of the automobile alloy; the differences in impact toughness, weldability and bend formability can also be considerable with identical properties.
The 7 aspects directly determine whether the extruded aluminum alloy section has higher strength, good bending welding performance and higher high-speed collision energy absorption effect.
Disclosure of Invention
The invention aims to solve the defects of the prior art and provides a method for manufacturing a high-strength 7000 series aluminum alloy profile for an automobile body, and the following two technical schemes are adopted.
The first technical scheme is as follows:
a manufacturing method of a high-strength 7000 series aluminum alloy profile for an automobile body is characterized by comprising the following steps of:
1) the raw materials comprise the following alloy elements in percentage by mass: 0.119 to 0.138 percent of Si, 0.148 to 0.17 percent of Fe, 0.05 to 0.19 percent of Cu, 0.04 to 0.10 percent of Mn, 0.72 to 0.99 percent of Mg, 0.05 to 0.10 percent of Cr, 5.55 to 6.0 percent of Zns, 0.15 to 0.22 percent of Zr, 0.02 to 0.04 percent of Ti, less than or equal to 0.05 percent of other single elements, less than or equal to 0.15 percent of other elements, and the balance of aluminum; wherein the Zn/Mg ratio is controlled to be 6-8;
2) the specific processing technology is as follows:
① smelting, namely putting the purified molten aluminum into a dump smelting furnace, adding other alloy element components for smelting at 761-780 ℃ to completely melt the raw materials and obtain a melt with uniformly distributed components;
② purifying the melt, casting into rod, namely purifying the melt, casting the purified melt into cast rod, wherein the casting temperature is 720-729 ℃, the die temperature is 690-710 ℃, the casting speed is 140mm/min, and the casting water pressure is 0.08-0.14 MPa;
③ homogenizing annealing, wherein the cast rod is subjected to three-stage homogenizing annealing process;
the main purpose of the homogenization annealing adopted in the invention is to reduce the segregation of chemical components and the nonuniformity of structures caused in the casting process of the aluminum alloy ingot, heat the aluminum alloy ingot to high temperature and preserve heat for a long time so as to achieve the purpose of homogenizing the chemical components and the structures. The purpose of the three-stage homogenization is to make Al3Zr particles are separated out and keep coherent relation with the matrix, and the growth of the grain structure can be effectively prevented. The cooling adopts a larger cooling rate, and aims to obtain the dispersed precipitated phase structure distribution for solving primary phases with equal impurities in the solid solution part.
④, extruding, namely putting the cast rod after the homogenizing annealing into an extrusion cylinder of 2800T for extrusion treatment to obtain a semi-finished product of the aluminum alloy section, wherein the extrusion heating temperature is 470-510 ℃, the outlet speed of the extruded section is 7-14m/min, the extrusion outlet temperature is 540-570 ℃, and the heating temperature of an extrusion die is 490-510 ℃;
the extrusion process parameters adopted by the invention are beneficial to forming a sub-grain structure with fiber grains as the main part and a microstructure with a very small amount of recrystallized structures, so that the dislocation structure of the material is increased through a certain tensile deformation, and the formation of GP zones and the precipitation of reinforced particles are accelerated.
⑤ cooling, wherein the extruded section is cooled by super strong wind, and the cooling system is uniformly distributed up and down and left and right;
⑥, stretching, namely stretching the extruded semi-finished product of the aluminum alloy section, wherein the stretching deformation is controlled to be 1-3%;
the stretching process adopted by the invention can ensure certain stress strain of the section bar, so that the section bar is subjected to certain work hardening, more dislocation structures are formed in the material for strengthening, and a nucleation position is provided for the precipitation of a later-stage precipitated phase.
⑦ natural aging and artificial aging, namely standing the extruded and stretched section for 7-60 days for natural aging, and then performing artificial aging, wherein the artificial aging process adopts a two-stage aging process, the first-stage aging temperature is 90-110 ℃, the second-stage aging temperature is 150-165 ℃, and the artificial aging ensures that the material has high tensile strength and yield strength, good elongation and above all good high-speed collision energy absorption effect.
The mechanical property strength reaches tensile strength Rm of more than 370MPa, Rp0.2 of more than 350MPa, A50 of more than 15 percent, the maximum static collapse force reaches 480kN, the average force reaches 350kN, and the absorbed energy reaches 70 kJ.
Further, the three-stage homogenization annealing process in the step ③ is 300 ℃/4h +400 ℃/5h +500 ℃/5h, and the temperature rise speed of each stage is 50 ℃/h.
Further, the cooling rate of step ⑤ is 30-50 ℃/s.
And furthermore, the natural aging time of the step ⑦ is 14-28 days, the natural aging time of the profile is more severe in 3-14 days, and tends to be smooth in 14-28 days, so the natural aging time is preferably 14-28 days.
Preferably, the raw materials comprise the following alloy elements in percentage by mass: 0.125-0.135% of Si, 0.155-0.16% of Fe0.09-0.18% of Cu, 0.06-0.09% of Mn, 0.91-0.99% of Mg, 0.07-0.09% of Cr, 5.55-5.95% of Zn, 0.15-0.22% of Zr, 0.02-0.04% of Ti, less than or equal to 0.05% of other single elements, less than or equal to 0.15% of other elements, and the balance of aluminum; wherein the Zn/Mg ratio is controlled to 6-7.
The second technical scheme is as follows:
the manufacturing method of the high-strength 7000-series aluminum alloy section for the automobile body is basically the same as the technical scheme I, and is different in that the raw materials comprise the following alloy elements in percentage by mass: 0.11 to 0.13 percent of Si, 0.11 to 0.13 percent of Fe, 0.05 to 0.08 percent of Cu, 0.06 to 0.09 percent of Mn, 0.75 to 1.0 percent of Mg, 0.023 to 0.95 percent of Cr, 5.75 to 5.95 percent of Zns, 0.16 to 0.23 percent of Zr, 0.02 to 0.04 percent of Ti, less than or equal to 0.05 percent of other single elements, less than or equal to 0.15 percent of other elements, and the balance of aluminum; wherein the Zn/Mg ratio is controlled to 6-8.
Preferably, the raw materials comprise the following alloy elements in percentage by mass: 0.115 to 0.125 percent of Si, 0.115 to 0.125 percent of Fe0.115, 0.06 to 0.07 percent of Cu, 0.07 to 0.08 percent of Mn, 0.82 to 0.88 percent of Mg, 0.075 to 0.85 percent of Cr0, 5.85 to 5.95 percent of Zn, 0.18 to 0.20 percent of Zr, 0.02 to 0.04 percent of Ti, less than or equal to 0.05 percent of other single elements, less than or equal to 0.15 percent of other elements, and the balance of aluminum; wherein the Zn/Mg ratio is controlled to be 7-8.
After the technical scheme is adopted, the manufacturing method of the high-strength 7000 series aluminum alloy section for the automobile body has the following advantages:
(1) the invention carries out full optimization design on the chemical components of 7000 series aluminum alloy, greatly reduces the contents of trace alloy elements Cr, Ti and Mn, properly reduces the contents of the trace alloy elements Si and Fe, controls the Zn/Mg ratio within the range of 6-8, and adds the trace elements in the form of intermediate alloy at reasonable time, so that the cast alloy forms smaller element segregation, and forms more Al with smaller size after the homogenization process at the later stage3Zr microscopic particles enable the aluminum alloy cast rod to form fiber crystal grains as a main part and recrystallized crystal grains as an auxiliary part in the extrusion process.
(2) The invention has higher melting temperature, leads the atomic bonds among the alloy elements to be broken to form long-range disordered atoms, quickly cools to reasonable melting temperature, enters a holding furnace for heat preservation, adopts Japan import equipment for online degassing, and adopts American import wagstaff casting equipment for casting to obtain a microstructure with fine surface quality and grain size and dispersed distribution of precipitated phases.
(3) The homogenization annealing adopts multi-stage homogenization treatment, the temperature rise rate is 50 ℃/h, the alloy segregation can be eliminated, and the particles for inhibiting recrystallization are dispersed and distributed.
(4) Reasonable die materials, die designs and process parameters are adopted in the extrusion process, the uniformity of grain structures of different wall thicknesses of the section bar and the consistency of quenching rates are guaranteed, a uniform supersaturated solid solution is formed, and GP zones and metastable phases can be uniformly formed after artificial aging, so that the section bar has excellent corrosion resistance, welding performance, fatigue performance, impact performance and crushing performance.
(5) The design of the extrusion process ensures that the head, the middle and the tail of the section are mainly made of fiber crystals, so that the unilateral coarse crystal layer of the section is less than 3% of the wall thickness, and the solid solubility of the alloy is ensured by adopting a forced cooling mode.
(6) The profile, when subjected to static crush testing, exhibits excellent folding performance with no cracking at the folded lips, slight cracking only at the geometric corners, and a crush maximum force reduction of less than 25%. The profile has excellent crushing performance and keeps good consistency.
For a better understanding and practice, the invention is described in detail below with reference to the accompanying drawings.
Drawings
FIG. 1 is a photograph of a typical crush of an aluminum alloy profile of the present invention.
Detailed Description
All materials, reagents and equipment selected for use in the present invention are well known in the art, but do not limit the practice of the invention, and other reagents and equipment well known in the art may be suitable for use in the practice of the following embodiments of the invention.
Example 1
A method for manufacturing a high-strength 7000-series aluminum alloy profile for an automobile body,
1) the raw materials comprise the following alloy elements in percentage by mass: 0.119% of Si, 0.148% of Fe, 0.05% of Cu, 0.04% of Mn, 0.72% of Mg, 0.05% of Cr, 5.55% of Zn, 0.15% of Zr, 0.02% of Ti, 0.05% of other single elements, 0.15% of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled at 6;
2) the specific processing technology is as follows:
① smelting, namely putting the purified molten aluminum into a dump smelting furnace, adding other alloy element components for smelting at 761 ℃ to completely melt the raw materials and obtain a melt with uniformly distributed components;
② purifying the melt, casting into rod, namely purifying the melt, and casting the purified melt into a cast rod at the casting temperature of 720 ℃, the die temperature of 690 ℃, the casting speed of 120mm/min and the casting water pressure of 0.08 MPa;
③ homogenizing annealing, wherein the cast rod is subjected to a three-stage homogenizing annealing process, the three-stage homogenizing annealing process comprises 300 ℃/4h +400 ℃/5h +500 ℃/5h, and the temperature rise speed of each stage is 50 ℃/h.
④, extruding, namely putting the cast rod after the homogenizing annealing into an extrusion cylinder of 2800T for extrusion treatment to obtain a semi-finished product of the aluminum alloy section, wherein the extrusion heating temperature is 470 ℃, the outlet speed of the extruded section is 7m/min, the extrusion outlet temperature is 540 ℃, and the heating temperature of an extrusion die is 490 ℃;
⑤ cooling, wherein the extruded section is cooled by super strong wind, the cooling rate is 30 ℃/s, and the cooling system is uniformly distributed up and down and left and right;
⑥, stretching, namely stretching the extruded semi-finished product of the aluminum alloy section, wherein the stretching deformation is controlled to be 1%;
⑦ natural aging and artificial aging treatment, namely standing the extruded and stretched section for 14 days for natural aging, and then performing artificial aging treatment, wherein the artificial aging treatment adopts a two-stage aging process, the first-stage aging temperature is 90 ℃, and the second-stage aging temperature is 150 ℃.
Examples2
The manufacturing method of the high-strength 7000-series aluminum alloy profile for the automobile body comprises the following steps of: 0.138% of Si, 0.17% of Fe, 0.19% of Cu0.19%, 0.10% of Mn0.99% of Mg, 0.10% of Cr, 6.0% of Zn, 0.22% of Zr, 0.04% of Ti, 0.04% of other single elements, 0.10% of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled at 8.
Example 3
The manufacturing method of the high-strength 7000-series aluminum alloy profile for the automobile body comprises the following steps of: 0.125% of Si, 0.155% of Fe, 0.09% of Cu0.09%, 0.06% of Mn0.91%, 0.07% of Mg, 5.55% of Zn, 0.15% of Zr, 0.02% of Ti, 0.05% of other single elements, 0.12% of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled at 6.
Example 4
The manufacturing method of the high-strength 7000-series aluminum alloy profile for the automobile body comprises the following steps of: 0.135% of Si, 0.16% of Fe, 0.18% of Cu0.09% of Mn, 0.99% of Mg, 0.09% of Cr, 5.95% of Zn, 0.22% of Zr, 0.04% of Ti, 0.04% of other single elements, 0.09% of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled at 7.
Example 5
The manufacturing method of the high-strength 7000-series aluminum alloy profile for the automobile body comprises the following steps of: 0.12 percent of Si, 0.15 percent of Fe, 0.18 percent of Cu0.08 percent of Mn0.08 percent of Mg, 0.08 percent of Cr, 5.9 percent of Zn, 0.18 percent of Zr, 0.03 percent of Ti, 0.04 percent of the content of other single elements, 0.09 percent of the total content of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled at 7.
Example 6
A method for manufacturing a high-strength 7000-series aluminum alloy profile for an automobile body,
1) the raw materials comprise the following alloy elements in percentage by mass: 0.11% of Si, 0.11% of Fe, 0.05% of Cu, 0.06% of Mn, 0.75% of Mg, 0.023% of Cr, 5.75% of Zn, 0.16% of Zr, 0.02% of Ti, 0.05% of other single elements, 0.15% of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled at 6.
2) The specific processing technology is as follows:
① smelting, namely putting the purified molten aluminum into a dump smelting furnace, adding other alloy element components for smelting at 780 ℃, so that the raw materials are completely melted and a melt with uniformly distributed components is obtained;
② purifying the melt, casting into rod, namely purifying the melt, and casting the purified melt into a cast rod, wherein the casting temperature is 729 ℃, the die temperature is 710 ℃, the casting speed is 140mm/min, and the casting water pressure is 0.14 MPa;
③ homogenizing annealing, wherein the cast rod is subjected to a three-stage homogenizing annealing process, the three-stage homogenizing annealing process comprises 300 ℃/4h +400 ℃/5h +500 ℃/5h, and the temperature rise speed of each stage is 50 ℃/h.
④, extruding, namely putting the cast rod after the homogenizing annealing into an extrusion cylinder of 2800T for extrusion treatment to obtain a semi-finished product of the aluminum alloy section, wherein the extrusion heating temperature is 510 ℃, the outlet speed of the extruded section is 14m/min, the extrusion outlet temperature is 570 ℃, and the heating temperature of an extrusion die is 510 ℃;
⑤ cooling, wherein the extruded section is cooled by super strong wind, the cooling rate is 50 ℃/s, and the cooling system is uniformly distributed up and down and left and right;
⑥, stretching, namely stretching the extruded semi-finished product of the aluminum alloy section, wherein the stretching deformation is controlled to be 3%;
⑦ natural aging and artificial aging treatment, namely standing the extruded and stretched section for 28 days for natural aging, and then performing artificial aging treatment, wherein the artificial aging treatment adopts a two-stage aging process, the first-stage aging temperature is 110 ℃, and the second-stage aging temperature is 165 ℃.
Example 7
The manufacturing method of the high-strength 7000-series aluminum alloy profile for the automobile body comprises the following steps of: 0.13% of Si, 0.13% of Fe, 0.08% of Cu0.08%, 0.09% of Mn0.0%, 1.0% of Mg, 0.95% of Cr, 5.95% of Zn, 0.23% of Zr, 0.04% of Ti, 0.04% of other single elements, 0.10% of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled at 8.
Example 8
The manufacturing method of the high-strength 7000-series aluminum alloy profile for the automobile body comprises the following steps of: 0.115% of Si, 0.115% of Fe, 0.06% of Cu0.06%, 0.07% of Mn0.82%, 0.075% of Mg, 5.85% of Zn, 0.18% of Zr, 0.02% of Ti, 0.05% of other single elements, 0.10% of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled at 7.
Example 9
The manufacturing method of the high-strength 7000-series aluminum alloy profile for the automobile body comprises the following steps of: 0.125 percent of Si, 0.125 percent of Fe, 0.07 percent of Cu0.08 percent of Mn0.08 percent of Mg, 0.88 percent of Cr, 5.95 percent of Zn, 0.20 percent of Zr, 0.04 percent of Ti, 0.04 percent of other single elements, less than or equal to 0.12 percent of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled at 8.
Example 10
The manufacturing method of the high-strength 7000-series aluminum alloy profile for the automobile body comprises the following steps of: 0.12 percent of Si, 0.11 percent of Fe, 0.07 percent of Cu0.07 percent of Mn, 0.08 percent of Mg, 0.05 percent of Cr, 5.9 percent of Zn, 0.18 percent of Zr, 0.035 percent of Ti, 0.03 percent of other single elements, 0.08 percent of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled at 8.
The following table shows the tensile properties and crushing behavior at room temperature for the aluminum alloy sections of examples 1-10And (4) performance. As can be seen from the table, the room temperature tensile mechanical property can reach the tensile strength Rm>370MPa，Rp0.2>350MPa，A50>15 percent; the static crushing performance can reach the maximum crushing force>480kN, average crushing force>350kN, absorbed energy>70 kJ. Therefore, the section bar has ultrahigh mechanical property and good corrosion resistance, fatigue resistance and crushing resistance, and is very suitable for producing components such as aluminum alloy energy absorption boxes, front and rear longitudinal beams, doorsills, door anti-collision beams and the like used in automobile bumper systems in batches.
TABLE 2 tensile Properties at room temperature and crushing Properties of the examples
The inventors conducted static crushing experiments on all the profiles obtained in examples 1 to 10, and showed excellent static impact effect. The experimental results of the profiles obtained in examples 1 to 3 are shown in fig. 1, and the impact effect is very good, so that the profiles are suitable for manufacturing aluminum alloy energy absorption boxes, longitudinal beams, doorsills and automobile side door anti-collision beams for automobile bumper systems.
Therefore, the aluminum alloy section obtained by the manufacturing method has good static collision effect through the design and development of alloy chemical components, the smelting casting and homogenization treatment of the cast rod, reasonable extrusion process parameters and a reasonable heat treatment process system. In conclusion, the aluminum alloy section obtained by the manufacturing method is particularly suitable for manufacturing aluminum alloy energy absorption boxes, longitudinal beams, doorsills and automobile side door anti-collision beams for automobile bumper systems.
The present invention is not limited to the above-described embodiments, and various modifications and variations of the present invention are intended to be included within the scope of the claims and the equivalent technology of the present invention if they do not depart from the spirit and scope of the present invention.
Claims (10)
1. A manufacturing method of a high-strength 7000 series aluminum alloy profile for an automobile body is characterized by comprising the following steps of:
1) the raw materials comprise the following alloy elements in percentage by mass: 0.119 to 0.138 percent of Si, 0.148 to 0.17 percent of Fe, 0.05 to 0.19 percent of Cu, 0.04 to 0.10 percent of Mn, 0.72 to 0.99 percent of Mg, 0.05 to 0.10 percent of Cr, 5.55 to 6.0 percent of Zns, 0.15 to 0.22 percent of Zr, 0.02 to 0.04 percent of Ti, less than or equal to 0.05 percent of other single elements, less than or equal to 0.15 percent of other elements, and the balance of aluminum; wherein the Zn/Mg ratio is controlled to be 6-8;
2) the specific processing technology is as follows:
① smelting, namely putting the purified molten aluminum into a dump smelting furnace, adding other alloy element components for smelting at 761-780 ℃ to completely melt the raw materials and obtain a melt with uniformly distributed components;
② purifying the melt, casting into rod, namely purifying the melt, casting the purified melt into cast rod, wherein the casting temperature is 720-729 ℃, the die temperature is 690-710 ℃, the casting speed is 140mm/min, and the casting water pressure is 0.08-0.14 MPa;
③ homogenizing annealing, wherein the cast rod is subjected to three-stage homogenizing annealing process;
④, extruding, namely putting the cast rod after the homogenizing annealing into an extrusion cylinder of 2800T for extrusion treatment to obtain a semi-finished product of the aluminum alloy section, wherein the extrusion heating temperature is 470-510 ℃, the outlet speed of the extruded section is 7-14m/min, the extrusion outlet temperature is 540-570 ℃, and the heating temperature of an extrusion die is 490-510 ℃;
⑤ cooling, wherein the extruded section is cooled by super strong wind, and the cooling system is uniformly distributed up and down and left and right;
⑥, stretching, namely stretching the extruded semi-finished product of the aluminum alloy section, wherein the stretching deformation is controlled to be 1-3%;
⑦ natural aging and artificial aging treatment, namely standing the extruded and stretched section for 7-60 days for natural aging, and then performing artificial aging treatment, wherein the artificial aging treatment adopts a two-stage aging process, the first-stage aging temperature is 90-110 ℃, and the second-stage aging temperature is 150-165 ℃.
2. The method for manufacturing the high-strength 7000-series aluminum alloy section for the automobile body as claimed in claim 1, wherein the three-stage homogenization annealing process in step ③ is 300 ℃/4h +400 ℃/5h +500 ℃/5h, and the temperature rise rate of each stage is 50 ℃/h.
3. The method of making a high strength 7000 series aluminum alloy section for automotive bodies as claimed in claim 1, wherein said cooling rate of step ⑤ is 30-50 ℃/s.
4. The method of making a high strength 7000 series aluminum alloy section for automotive bodies as claimed in claim 1, wherein said natural aging time of step ⑦ is 14-28 days.
5. The manufacturing method of the high-strength 7000-series aluminum alloy profile for the automobile body according to any one of claims 1 to 4, wherein the raw materials comprise the following alloy elements in percentage by mass: 0.125 to 0.135 percent of Si, 0.155 to 0.16 percent of Fe, 0.09 to 0.18 percent of Cu, 0.06 to 0.09 percent of Mn, 0.91 to 0.99 percent of Mg, 0.07 to 0.09 percent of Cr, 5.55 to 5.95 percent of Zns, 0.15 to 0.22 percent of Zr, 0.02 to 0.04 percent of Ti, less than or equal to 0.05 percent of other single elements, less than or equal to 0.15 percent of other elements, and the balance of aluminum; wherein the Zn/Mg ratio is controlled to 6-7.
6. A manufacturing method of a high-strength 7000 series aluminum alloy profile for an automobile body is characterized by comprising the following steps of:
1) the raw materials comprise the following alloy elements in percentage by mass: 0.11 to 0.13 percent of Si, 0.11 to 0.13 percent of Fe, 0.05 to 0.08 percent of Cu0.05, 0.06 to 0.09 percent of Mn, 0.75 to 1.0 percent of Mg, 0.023 to 0.95 percent of Cr, 5.75 to 5.95 percent of Zn, 0.16 to 0.23 percent of Zr, 0.02 to 0.04 percent of Ti, less than or equal to 0.05 percent of other single elements, less than or equal to 0.15 percent of other elements and the balance of aluminum; wherein the Zn/Mg ratio is controlled to be 6-8;
2) the specific processing technology is as follows:
① smelting, namely putting the purified molten aluminum into a dump smelting furnace, adding other alloy element components for smelting at 761-780 ℃ to completely melt the raw materials and obtain a melt with uniformly distributed components;
② purifying the melt, casting into rod, namely purifying the melt, casting the purified melt into cast rod, wherein the casting temperature is 720-729 ℃, the die temperature is 690-710 ℃, the casting speed is 140mm/min, and the casting water pressure is 0.08-0.14 MPa;
③ homogenizing annealing, wherein the cast rod is subjected to three-stage homogenizing annealing process;
④, extruding, namely putting the cast rod after the homogenizing annealing into an extrusion cylinder of 2800T for extrusion treatment to obtain a semi-finished product of the aluminum alloy section, wherein the extrusion heating temperature is 470-510 ℃, the outlet speed of the extruded section is 7-14m/min, the extrusion outlet temperature is 540-570 ℃, and the heating temperature of an extrusion die is 490-510 ℃;
⑤ cooling, wherein the extruded section is cooled by super strong wind, and the cooling system is uniformly distributed up and down and left and right;
⑥, stretching, namely stretching the extruded semi-finished product of the aluminum alloy section, wherein the stretching deformation is controlled to be 1-3%;
⑦ natural aging and artificial aging treatment, namely standing the extruded and stretched section for 7-60 days for natural aging, and then performing artificial aging treatment, wherein the artificial aging treatment adopts a two-stage aging process, the first-stage aging temperature is 90-110 ℃, and the second-stage aging temperature is 150-165 ℃.
7. The method for manufacturing the high-strength 7000-series aluminum alloy section for the automobile body as claimed in claim 6, wherein the three-stage homogenization annealing process in step ③ is 300 ℃/4h +400 ℃/5h +500 ℃/5h, and the temperature rise rate of each stage is 50 ℃/h.
8. The method of making a high strength 7000 series aluminum alloy section for automotive bodies as claimed in claim 6, wherein said cooling rate of step ⑤ is 30-50 ℃/s.
9. The method of making a high strength 7000 series aluminum alloy section for automotive bodies as claimed in claim 6, wherein said natural aging time of step ⑦ is 14-28 days.
10. The manufacturing method of the high-strength 7000-series aluminum alloy profile for the automobile body according to any one of claims 6 to 9, wherein the raw materials comprise the following alloy elements in percentage by mass: 0.115 to 0.125 percent of Si, 0.115 to 0.125 percent of Fe, 0.06 to 0.07 percent of Cu, 0.07 to 0.08 percent of Mn, 0.82 to 0.88 percent of Mg, 0.075 to 0.85 percent of Cr, 5.85 to 5.95 percent of Zn, 0.18 to 0.20 percent of Zr, 0.02 to 0.04 percent of Ti, less than or equal to 0.05 percent of other single elements, less than or equal to 0.15 percent of other elements, and the balance of aluminum; wherein the Zn/Mg ratio is controlled to be 7-8.
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113388764A (en) * | 2021-06-15 | 2021-09-14 | 广东澳美铝业有限公司 | High-strength 7-series aluminum alloy for automobile anti-collision beam and automobile anti-collision beam |
| CN113528907A (en) * | 2021-07-06 | 2021-10-22 | 福建祥鑫股份有限公司 | Ultrahigh-strength aluminum alloy material and pipe manufacturing method thereof |
| CN113846279A (en) * | 2021-09-26 | 2021-12-28 | 浙江大学 | Ultrafast aging process for 7075 aluminum alloy and application thereof |
| CN114480929A (en) * | 2020-11-13 | 2022-05-13 | 烟台南山学院 | Automobile skylight guide rail cantilever section bar and preparation method thereof |
| CN114941094A (en) * | 2022-03-23 | 2022-08-26 | 中亿丰金益(苏州)科技有限公司 | High-strength 7-series aluminum alloy section and processing method and application thereof |
| CN115216673A (en) * | 2022-07-27 | 2022-10-21 | 昆山晶微新材料研究院有限公司 | High-strength corrosion-resistant 5-series alloy and preparation method thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6128744B2 (en) * | 1982-12-18 | 1986-07-02 | Aishin Seiki Kk | |
| US20100089506A1 (en) * | 2006-09-04 | 2010-04-15 | Trenda Guenther | Aluminum Alloy of the AlZnMg Type and Method of Producing It |
| CN103205617A (en) * | 2013-03-27 | 2013-07-17 | 成都阳光铝制品有限公司 | 7003T5 aluminum alloy applied to manufacturing high-speed rail vehicle body and production technology thereof |
| CN104018041A (en) * | 2014-06-26 | 2014-09-03 | 龙口市丛林铝材有限公司 | High-speed rail train aluminum profile and preparation method thereof |
| CN106319308A (en) * | 2016-11-23 | 2017-01-11 | 马鞍山市新马精密铝业股份有限公司 | Manufacturing method of 7000-series aluminum alloy section for vehicular bodies |
| CN106756330A (en) * | 2016-11-23 | 2017-05-31 | 马鞍山市新马精密铝业股份有限公司 | The aluminium alloy extrusions and manufacture method of a kind of body of a motor car |
-
2020
- 2020-04-07 CN CN202010265792.0A patent/CN111270115A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6128744B2 (en) * | 1982-12-18 | 1986-07-02 | Aishin Seiki Kk | |
| US20100089506A1 (en) * | 2006-09-04 | 2010-04-15 | Trenda Guenther | Aluminum Alloy of the AlZnMg Type and Method of Producing It |
| CN103205617A (en) * | 2013-03-27 | 2013-07-17 | 成都阳光铝制品有限公司 | 7003T5 aluminum alloy applied to manufacturing high-speed rail vehicle body and production technology thereof |
| CN104018041A (en) * | 2014-06-26 | 2014-09-03 | 龙口市丛林铝材有限公司 | High-speed rail train aluminum profile and preparation method thereof |
| CN106319308A (en) * | 2016-11-23 | 2017-01-11 | 马鞍山市新马精密铝业股份有限公司 | Manufacturing method of 7000-series aluminum alloy section for vehicular bodies |
| CN106756330A (en) * | 2016-11-23 | 2017-05-31 | 马鞍山市新马精密铝业股份有限公司 | The aluminium alloy extrusions and manufacture method of a kind of body of a motor car |
Non-Patent Citations (1)
| Title |
|---|
| 吴生绪等: "《变形铝合金及其模锻成形技术手册》", 31 January 2014, 机械工业出版社 * |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114480929A (en) * | 2020-11-13 | 2022-05-13 | 烟台南山学院 | Automobile skylight guide rail cantilever section bar and preparation method thereof |
| CN113388764A (en) * | 2021-06-15 | 2021-09-14 | 广东澳美铝业有限公司 | High-strength 7-series aluminum alloy for automobile anti-collision beam and automobile anti-collision beam |
| CN113528907A (en) * | 2021-07-06 | 2021-10-22 | 福建祥鑫股份有限公司 | Ultrahigh-strength aluminum alloy material and pipe manufacturing method thereof |
| CN113846279A (en) * | 2021-09-26 | 2021-12-28 | 浙江大学 | Ultrafast aging process for 7075 aluminum alloy and application thereof |
| CN114941094A (en) * | 2022-03-23 | 2022-08-26 | 中亿丰金益(苏州)科技有限公司 | High-strength 7-series aluminum alloy section and processing method and application thereof |
| CN114941094B (en) * | 2022-03-23 | 2023-08-29 | 中亿丰金益(苏州)科技有限公司 | High-strength 7-series aluminum alloy profile and processing method and application thereof |
| CN115216673A (en) * | 2022-07-27 | 2022-10-21 | 昆山晶微新材料研究院有限公司 | High-strength corrosion-resistant 5-series alloy and preparation method thereof |
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Application publication date: 20200612 |