WO2021121343A1 - 一种7xxx系铝合金或板材、其制造方法、其加工方法及其应用 - Google Patents

一种7xxx系铝合金或板材、其制造方法、其加工方法及其应用 Download PDF

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Publication number
WO2021121343A1
WO2021121343A1 PCT/CN2020/137405 CN2020137405W WO2021121343A1 WO 2021121343 A1 WO2021121343 A1 WO 2021121343A1 CN 2020137405 W CN2020137405 W CN 2020137405W WO 2021121343 A1 WO2021121343 A1 WO 2021121343A1
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Prior art keywords
aluminum alloy
series aluminum
7xxx series
sheet
alloy
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PCT/CN2020/137405
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English (en)
French (fr)
Inventor
吴浩
刘成
黄鸣东
郑志凯
周泽宇
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Aluminum Corp of China Ltd
Chinalco Materials Application Research Institute Co Ltd
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Aluminum Corp of China Ltd
Chinalco Materials Application Research Institute Co Ltd
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Priority to CN202080087409.5A priority Critical patent/CN114929913A/zh
Priority to EP20901677.3A priority patent/EP4063530A4/en
Publication of WO2021121343A1 publication Critical patent/WO2021121343A1/zh
Anticipated expiration legal-status Critical
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/002—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
    • C22F1/053—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

Definitions

  • the invention belongs to the field of non-ferrous metals, and specifically relates to a 7xxx series aluminum alloy or plate.
  • the present invention also relates to the manufacturing method and processing method of the 7xxx series aluminum alloy or plate and its application in the manufacture of vehicle parts.
  • the automobile industry has developed rapidly, and the demand for lightweight automobiles is also urgently affected by the energy environment.
  • the weight of the car body accounts for about 40% of the total weight of the car.
  • the light weight of the car body plays a decisive role in the light weight of the whole vehicle.
  • the light weight of the car body has become the frontier and hot spot of the current automobile manufacturing technology.
  • the aluminum alloy automobile panels commonly used in car bodies are mainly 5xxx and 6xxx series aluminum alloys, but their strength is low, and the high-strength 7xxx series aluminum alloys have low room temperature formability, which limits their wide application in car bodies.
  • the sheet blank is heated to the required temperature, then transferred to the mold for hot forming, and then the formed part is subjected to conventional solution aging strengthening treatment to obtain the final Performance parts.
  • the process of this process is cumbersome and the cycle is long. It is difficult to ensure the dimensional accuracy of the subsequent parts after heat treatment, and the production cost is relatively high.
  • the integrated hot forming-quenching process is a composite process technology that combines heat treatment and hot forming of aluminum alloys. It combines the forming process and the heat treatment process, and relies on the same set of molds to achieve "forming" and "controllability".
  • This process improves the plasticity of the material during the forming process while ensuring the strength of the material.
  • the completely solid solution aluminum alloy sheet is quickly transferred to the water-cooled mold, and then the mold is quickly closed for forming. After the forming is completed, the mold is kept closed to complete the in-mold quenching of the part, and finally the aging treatment is performed to improve its strength.
  • This process is the most promising new process in the hot forming of high-strength aluminum alloy sheets, which can solve the problems of poor plasticity, large springback, and shape distortion during heat treatment of aluminum alloy materials.
  • the inventors of the present invention found that the integrated hot forming-quenching process technology has high requirements for the properties of 7xxx series aluminum alloy sheets, especially including short-term solid solution, low quenching sensitivity, good hot forming and age hardening, etc., but currently it is still There is no 7xxx series aluminum alloy sheet that can meet these requirements.
  • the present invention relates to the following aspects.
  • a 7xxx series aluminum alloy (preferred sheet), the chemical composition of which is Zn 5.1-10.0%, Mg 2.0-3.2%, Cu 1.2-3.0%, Fe 0-0.5%, Si 0-0.4 by weight percentage %, Ti 0-0.2%, Cr 0-0.1%, Zr 0-0.055%, Mn 0-0.25%, other grain size control elements 0-0.30%, the balance is Al.
  • the 7xxx series aluminum alloy (preferred sheet) described in any one of the foregoing or the following, the chemical composition of which is Zn 5.4-7.6%, Mg 2.0-2.7%, Cu 1.6-2.3%, Fe 0-0.4%, Si 0-0.3%, Ti 0.01-0.15%, Cr 0-0.05%, Zr 0-0.05%, Mn 0-0.25%, the other grain size control elements 0-0.25%, balance Is Al.
  • the 7xxx series aluminum alloys (preferred plates) described in any of the foregoing or the following aspects have a chemical composition in a weight percentage ratio of Zn 7.6-9.6%, Mg 2.1-3.1%, Cu 1.4-2.6%, Fe 0 -0.4%, Si 0-0.3%, Ti 0.01-0.15%, Cr 0-0.05%, Zr 0-0.05%, Mn 0-0.25%, the other grain size control elements 0-0.25%, the balance is Al.
  • the 7xxx series aluminum alloys (preferred plates) described in any of the foregoing or the following aspects have a chemical composition in a weight percentage ratio of Zn 5.1-6.7%, Mg 2.0-2.9%, Cu 1.2-2.6%, Fe 0 -0.5%, Si 0-0.4%, Cr 0-0.1%, Zr 0-0.05%, Mn 0-0.25%, the balance is Al.
  • the 7xxx series aluminum alloy (preferred sheet) described in any of the foregoing or the following aspects has a chemical composition in a weight percentage ratio of Zn 5.4-6.5%, Mg 2.0-2.7%, Cu 1.6-2.3%, Fe 0 -0.4%, Si 0-0.3%, Cr 0-0.05%, Zr 0-0.05%, Mn 0-0.15%, and the balance is Al.
  • the 7xxx series aluminum alloy sheet described in any of the foregoing or the following aspects has at least one of the following properties:
  • a method for manufacturing a 7xxx series aluminum alloy sheet comprising the steps of homogenizing, hot rolling and cold rolling a 7xxx series aluminum alloy ingot to obtain the 7xxx series aluminum alloy sheet, wherein the 7xxx series aluminum alloy sheet
  • the chemical composition of aluminum alloy ingots is proportioned by weight percentage of Zn 5.1-10.0%, Mg 2.0-3.2%, Cu 1.2-3.0%, Fe 0-0.5%, Si 0-0.4%, Ti 0-0.2%, Cr 0-0.1%, Zr 0-0.055%, Mn 0-0.30%, and the balance is Al.
  • the homogenization treatment includes: heating the 7xxx series aluminum alloy ingot to 375-460°C (preferably 400°C-450°C), and heat preservation 0- After 15h (preferably 5-10h), heat up to 465-490°C (preferably 470°C-490°C or 470°C-485°C), then keep it for 10-48h (preferably 10-36h or 16-36h), then air cooling or air cooling Cooled or cooled to room temperature with the furnace, the heating rate is 15-75°C/h (preferably 25-75°C/h or 25-50°C/h), and/or, the hot rolling treatment includes: hot rough rolling and hot rolling Finish rolling to 4-14mm (preferably 4-8mm or 6-10mm), the final rolling temperature is 200-460°C (preferably 250-350°C, 300-460°C or 350-450°C), air-cooled to room temperature after crimping, and /Or, the cold rolling treatment includes: cold rolling to 0.5-10.0mm (
  • a hot forming-quenching integrated processing method comprising combining the 7xxx series aluminum alloy sheet according to any one of the foregoing or the following aspects or the 7xxx series aluminum alloy manufactured according to the manufacturing method of any one of the foregoing or the following aspects The step of hot forming-quenching integrated processing of the plate.
  • a vehicle part (especially an automobile part), which is made of the 7xxx series aluminum alloy sheet described in any one of the foregoing or the following aspects, or is manufactured by the processing method described in any of the foregoing or the following aspects.
  • a vehicle comprising the vehicle component according to any one of the foregoing or the following.
  • the aluminum alloy sheet provided by the present invention has one of the following beneficial effects or a combination thereof.
  • Fig. 1 The grain structure of the Al alloy sheet of Example A1 after solid solution at 480°C/5min.
  • Fig. 2 The grain structure of the A3 alloy sheet of Example A3 after solid solution at 480°C/5min.
  • Fig. 3 The grain structure of the comparative C5 alloy sheet after solid solution at 480°C/5min.
  • Fig. 5 The grain structure of comparative C1 alloy sheet after solid solution at 480°C/5min.
  • Fig. 6 The grain structure of the A5 alloy sheet of the embodiment after solid solution at 480°C/5min.
  • Fig. 7 The grain structure of C2 alloy sheet of comparative example after solid solution at 480°C/5min.
  • Fig. 8 The grain structure of C3 alloy sheet of comparative example after solid solution at 480°C/5min.
  • Fig. 11 Scanning structure of C7 alloy sheet of comparative example after solid solution at 480°C/10min.
  • Fig. 12 Scanning structure of C10 alloy sheet of comparative example after solid solution at 480°C/10min.
  • Fig. 13 Scanning structure of C12 alloy sheet of comparative example after solid solution at 480°C/10min.
  • the so-called “substantially” refers to allowing deviations that are acceptable or reasonable to those skilled in the art, such as deviations within ⁇ 5%, ⁇ 1%, ⁇ 0.5%, or Within ⁇ 0.1%.
  • the temperature generally refers to the temperature of the material itself during processing (such as annealing, homogenization or hot rolling).
  • the balance is Al means “the balance is Al and unavoidable impurities”. This is obvious to those skilled in the art.
  • artificial peak aging can be performed in any manner known to those skilled in the art, and is not particularly limited. As an example, it is generally kept at 100-130°C for 5 to 48 hours.
  • the paint baking treatment can be performed in any manner known to those skilled in the art, and is not particularly limited.
  • the temperature is generally 170 to 190°C for 20 to 40 minutes.
  • the yield strength measurement method refers to the ASTM E8/E8M-16ae1 standard.
  • the tensile strength measurement method refers to the ASTM E8/E8M-16ae1 standard.
  • the elongation measurement method refers to the ASTM E8/E8M-16ae1 standard.
  • the average grain size measurement method refers to the ASTM E112-13 standard.
  • any two or more embodiments of the present invention can be combined arbitrarily, and the technical solutions formed thereby belong to a part of the original disclosure of this specification and also fall into the protection scope of the present invention.
  • a 7xxx series aluminum alloy particularly a 7xxx series aluminum alloy in the form of a sheet (ie, a 7xxx series aluminum alloy sheet).
  • the 7xxx series aluminum alloy plate is particularly suitable for integrated hot forming and quenching processing.
  • the aluminum alloy sheet has medium strength or high strength.
  • the chemical composition of the 7xxx series aluminum alloy or sheet is proportioned by weight percentages of Zn 5.1-10.0%, Mg 2.0-3.2%, Cu 1.2-3.0%, Fe 0-0.5%, Si 0-0.4%, Ti 0-0.2%, Cr 0-0.1%, Zr 0-0.055%, Mn 0-0.25%, other grain size control elements 0-0.30%, the balance is Al.
  • other grain size control elements refers to any trace element known to those skilled in the art that can be used to adjust (increase or decrease) the grain size of aluminum alloys (except Cr, Zr and Mn). ).
  • specific examples include Er, Sc, Hf, Dy, Gd, and the like.
  • the inventor of the present invention believes that by controlling the content of Fe and Si, the preparation and subsequent use costs of the entire alloy raw materials can be reduced, and the grain structure can be refined to a certain extent.
  • the inventor of the present invention also believes that based on the requirements of the hot forming-quenching integrated process for the properties of aluminum alloy materials, by strictly controlling the content of the main alloying elements Zn, Mg and Cu, the high-temperature residual phase Al 2 CuMg phase is reduced to ensure the alloy sheet In the heating and short-term holding stage of the integrated hot forming-quenching process, the remaining second phase can be quickly re-dissolved in the matrix to ensure the hot formability and subsequent mechanical properties of the alloy.
  • the inventor of the present invention also believes that by strictly controlling the content of crystal grain size control elements such as Cr, Zr, and Mn, it is possible to ensure that the alloy sheet has a lower quenching sensitivity, while controlling the grain size of the sheet, so that the sheet can be solidified at high temperature. After melt quenching, the matrix can obtain a greater degree of supersaturation and a better grain structure. After the subsequent artificial peak aging or paint treatment, the yield strength of the final alloy sheet is> 400 MPa, and the tensile strength is> 450 MPa. , Elongation> 6.5%.
  • the chemical composition of the 7xxx series aluminum alloy or sheet is proportioned by weight percentages of Zn 5.4-7.6%, Mg 2.0-2.7%, Cu 1.6-2.3%, Fe 0-0.4%, Si 0-0.3%, Ti 0.01-0.15%, Cr 0-0.05%, Zr 0-0.05%, Mn 0-0.25%, the other grain size control elements 0-0.25%, and the balance is Al.
  • the chemical composition of the 7xxx series aluminum alloy or sheet is proportioned by weight percentages of Zn 7.6-9.6%, Mg 2.1-3.1%, Cu 1.4-2.6%, Fe 0-0.4%, Si 0-0.3%, Ti 0.01-0.15%, Cr 0-0.05%, Zr 0-0.05%, Mn 0-0.25%, the other grain size control elements 0-0.25%, and the balance is Al.
  • the chemical composition of the 7xxx series aluminum alloy or sheet is proportioned by weight percentage of Zn 5.1-6.7%, Mg 2.0-2.9%, Cu 1.2-2.6%, Fe 0-0.5%, Si 0-0.4%, Cr 0-0.1%, Zr 0-0.05%, Mn 0-0.25%, and the balance is Al.
  • the chemical composition of the 7xxx series aluminum alloy or sheet is proportioned by weight percentage of Zn 5.4-6.5%, Mg 2.0-2.7%, Cu 1.6-2.3%, Fe 0-0.4%, Si 0-0.3%, Cr 0-0.05%, Zr 0-0.05%, Mn 0-0.15%, the balance is Al.
  • the other crystal grain size control elements are 0-0.15%.
  • Cr is 0-0.05%
  • Zr is 0-0.04%
  • Mn is 0-0.25%
  • the other grain size control elements are 0-0.15%.
  • Cr, Mn, Zr and the other grain size controlling elements are all grain size controlling elements, preferably Cr, Mn, and Zr. These grain size control elements may be used singly or in combination of two or more. According to an embodiment of the present invention, when used alone or in combination, the total weight percentage content of these grain size control elements (when used alone, refers to the weight percentage content of this element) is generally ⁇ 0.30%, preferably ⁇ 0.25% or ⁇ 0.15%.
  • the average grain size thereof is generally 10-100 microns, preferably 15-70 microns.
  • the thickness of the 7xxx series aluminum alloy sheet is generally 0.5-10.0 mm, preferably 1.0-4.0 mm.
  • the 7xxx series aluminum alloy sheet is particularly suitable for integrated hot forming-quenching processing.
  • the 7xxx series aluminum alloy sheet has rapid solid solution, that is, the solution treatment can be quickly completed by keeping it at 450-510°C for 5-20 minutes.
  • the 7xxx series aluminum alloy sheet has low quenching sensitivity.
  • the 7xxx series aluminum alloy sheet is a sheet in a cold rolled state, an O state or a T4 state.
  • the 7xxx series aluminum alloy sheet is kept at 450-510°C for 5-20 minutes, followed by air cooling or mold cooling or water cooling, and after artificial peak aging or paint baking treatment, its yield strength is generally> 400MPa, Preferably >480MPa.
  • the 7xxx series aluminum alloy sheet is kept at 450-510°C for 5-20 minutes, and then air-cooled or mold-cooled or water-cooled, and then subjected to artificial peak aging or paint baking treatment, the tensile strength is generally> 450 MPa , Preferably >520MPa.
  • the 7xxx series aluminum alloy sheet is kept at 450-510°C for 5-20 minutes, followed by air cooling or mold cooling or water cooling, and then after artificial peak aging or baking varnish treatment, its elongation is generally> 6.5% , Preferably >5.5%.
  • the present invention also relates to a method for manufacturing a 7xxx series aluminum alloy sheet.
  • the manufacturing method can be used to manufacture any 7xxx series aluminum alloy sheet of the present invention as described above.
  • the manufacturing method includes the steps of performing homogenization treatment, hot rolling treatment and cold rolling treatment on the 7xxx series aluminum alloy ingot to obtain the 7xxx series aluminum alloy sheet.
  • the 7xxx series aluminum alloy ingot is any one of the 7xxx series aluminum alloy ingots described above in the present invention.
  • the chemical composition of the 7xxx series aluminum alloy ingot is proportioned by weight percentage of Zn 5.1-10.0%, Mg 2.0-3.2%, Cu 1.2-3.0%, Fe 0-0.5%, Si 0-0.4% , Ti 0-0.2%, Cr 0-0.1%, Zr 0-0.055%, Mn 0-0.30%, and the balance is Al.
  • the homogenization treatment in the manufacturing method, can be performed in any manner known to those skilled in the art, and is not particularly limited.
  • the 7xxx series aluminum alloy ingot is generally heated to 375-460°C (preferably 400°C-450°C), after holding for 0-15h (preferably 5-10h), the temperature is raised to 465-490°C (preferably 470°C-490°C or 470°C-485°C), then keep the temperature for 10-48h (preferably 10-36h or 16-36h), and then cool to room temperature with air cooling or air cooling or along with furnace.
  • the heating rate of the homogenization treatment is generally 15-75°C/h, preferably 25-75°C/h or 25-50°C/h.
  • the hot rolling treatment in the manufacturing method, can be performed in any manner known to those skilled in the art, and is not particularly limited.
  • generally hot rough rolling and hot finishing rolling to 4-14 mm preferably hot rough rolling and hot finishing rolling to 4-8 mm or 6-10 mm.
  • the final rolling temperature of the hot rolling treatment is 200-460°C, preferably 250-350°C, 300-460°C, or 350-450°C.
  • the hot finish rolled sheet is crimped and air-cooled to room temperature.
  • the cold rolling treatment in the manufacturing method, can be performed in any manner known to those skilled in the art, and is not particularly limited. As an example, it is generally cold-rolled to 0.5-10.0 mm, preferably cold-rolled to 1.0-4.0 mm, to obtain the 7xxx series aluminum alloy sheet. At this time, the 7xxx series aluminum alloy sheet is a cold-rolled sheet.
  • the manufacturing method further includes the step of box-type or continuous annealing the cold-rolled 7xxx series aluminum alloy sheet to obtain the 7xxx series aluminum alloy sheet in the O state or the T4 state .
  • the box annealing can be performed in any manner known to those skilled in the art, and is not particularly limited.
  • the operating conditions generally include: placing the aluminum alloy coil in a box annealing furnace and heating it to 300-450°C at a heating rate of 25-50°C/h, holding it for 0.5-3h, and then cooling.
  • the continuous annealing can be performed in any manner known to those skilled in the art, and is not particularly limited.
  • the operating conditions of the aluminum alloy coil are generally to pass through a continuous annealing furnace with a furnace temperature of 400° C.-500° C. at a speed of 10-80 m/min, and then cool and rewind.
  • the manufacturing method further includes the step of holding the homogenized ingot at 300-480°C for 2-30 hours before the hot rolling treatment.
  • the homogenized ingot is kept at 380-450°C for 3-20 hours.
  • the present invention also relates to a hot forming-quenching integrated processing method, which includes combining the 7xxx series aluminum alloy sheet as described in any one of the preceding items in this specification or the manufacturing method according to any one of the preceding items in this specification
  • the manufactured 7xxx series aluminum alloy sheet undergoes a step of integrated hot forming and quenching.
  • the hot forming-quenching integrated processing can be performed in any manner known to those skilled in the art, and is not particularly limited, so detailed descriptions thereof are omitted here.
  • the vehicle component may be made of the 7xxx series aluminum alloy sheet as described in any of the preceding items in this specification.
  • the manufacturing method of the vehicle component it can be carried out in any manner known to those skilled in the art, and is not particularly limited, but in particular, the integrated hot forming-quenching process described in any of the preceding items in this specification can be mentioned. method.
  • the present invention also relates to a vehicle provided with the vehicle component described in any of the preceding items in this specification.
  • the preparation process of the 7xxx aluminum alloy cooling plate is: the alloy ingot is prepared by an industrial semi-continuous process. According to the characteristics of the trace elements contained in each ingot, the ingots are respectively homogenized.
  • the homogenization process is to make the alloy ingots in 400 After holding at °C for 10h, and then at 470°C for 24h, the heating rate is 50°C/h, and then air cooling or air cooling to room temperature; after the homogenized billet is kept at 440°C for 8h, hot rough rolling and hot finish rolling are carried out To 6mm, the final rolling temperature is 300°C, and then crimp, the alloy hot-rolled coil is air-cooled to room temperature; finally, the 6mm alloy hot-rolled coil is cold-rolled (cold rolling-intermediate annealing-cold rolling process can be selected according to the situation, that is, cold rolling Intermediate annealing state, CAC state cold-rolled sheet), crimping, and finally obtain a 2mm thick alloy cold-rolled sheet.
  • Example A1-A11 alloy composition range is: Zn 5.1-6.7%, Mg 2.0-2.9%, Cu 1.2-2.6%, Fe 0-0.5%, Si 0-0.4%, Cr 0-0.1%, Zr 0-0.05 %, Mn 0-0.25%, other grain size control elements 0-0.25%, and the balance is Al.
  • Table 1 shows the specific chemical composition and corresponding sheet state of the alloys of Examples A1-A11 and Comparative Examples C1-C6.
  • the alloy plates of Examples A1-A11 and Comparative Examples C1-C6 were subjected to rapid solution treatment at 480°C for 5 minutes (industrial production can be performed on-line continuous solution treatment), and then water-cooled (WQ) Or air cooling (AQ) two extreme cooling methods, followed by 120°C/24h T6 peak aging (PA) and 180°C/30min baking paint (BH) respectively, and test the tensile properties of the panels after different processes.
  • WQ water-cooled
  • AQ air cooling
  • PA 120°C/24h T6 peak aging
  • BH 180°C/30min baking paint
  • the yield strength of the A1-A11 alloy sheet of the embodiment is> 400 MPa
  • the tensile strength is> 450 MPa
  • the elongation is> 6.5%
  • the yield strength loss coefficient R is less than or equal to 20%.
  • the performance results are shown in Table 2.
  • the main alloying elements in the alloy plates of Example A1, Example A2 and Example A3 are basically similar, the trace elements Cr, Zr, and Mn are basically zero, the quenching sensitivity of the alloy plates is low, and the yield strength loss coefficient R ⁇ 15%.
  • the Fe and Si elements in the Example A1 alloy and the Example A2 alloy are lower than those in the Example A3 alloy, while the comparative example C5 alloy is prepared with high-purity aluminum as the raw material.
  • the Fe and Si elements in the alloy are the lowest, but the high Fe and Si content is constant. To a certain extent, it can effectively inhibit the grain growth behavior of the sheet, which is beneficial to control the grain structure; after the solution treatment of the A1 alloy, the A3 alloy and the C5 alloy sheet, the average grain size is 64 ⁇ m, 61 ⁇ m and 109 ⁇ m, respectively, as shown in Figure 1- 3 shown.
  • the strength of the C5 alloy sheet processed by each process is significantly lower than that of the example A1 alloy and the example processed by the corresponding process.
  • Example A4 alloy contains 0.0452% trace element Zr. Compared with Example A3 alloy which does not contain trace element Zr, after solution treatment, the average grain size of the A4 alloy sheet is greatly reduced to about 37 ⁇ m ( Figure 4) , But the quenching sensitivity has increased, and the yield strength loss coefficient R is 6.73% and 12.24%, which are significantly higher than those of A3 alloy plates (4.9% and 5.0%, respectively), indicating that the addition of Zr element improves alloy quenching to a certain extent Sensitivity.
  • the Zr element content in the C1 alloy of the comparative example is increased to 0.0791%, although the average grain size can be further reduced to about 25 ⁇ m (Figure 5), the quenching sensitivity is significantly increased compared to the A4 alloy sheet of the example, and the R values are respectively Increased to 22.36% and 34.55%, the strength of the air-cooled aging sample of the alloy sheet decreased significantly after solid solution.
  • the addition of trace element Zr is conducive to controlling the grain size of the plate, but it needs to be properly controlled, otherwise it will greatly increase the quenching sensitivity and significantly reduce the mechanical properties of the alloy plate.
  • Example A5 alloy and Example A7-A11 alloy all contain trace Cr element, the content is less than 0.05%.
  • the average grain size of the alloy sheet of Example A5 is compared with that of Example A3 alloy which does not contain trace elements. From 61 ⁇ m to 39 ⁇ m ( Figure 6), the quenching sensitivity of the corresponding alloy sheet is improved, but the yield strength loss coefficient R ⁇ 20%. With the increase of Cr element addition, although the average grain size of the sheet has decreased, its quenching sensitivity has also increased significantly.
  • the comparative C2 alloy (0.1241% Cr) and the comparative C3 alloy (0.1811% Cr, which are Conventional 7075 alloy sheet composition) decreased to 32 ⁇ m and 27 ⁇ m respectively ( Figure 7 and Figure 8), but the yield strength loss coefficient R increased significantly, and increased with the increase of the trace element Cr content, respectively 34.9%, 38.63, 46.54%, 53.85%, the strength of the air-cooled aging samples after the corresponding plate solid solution is significantly reduced. Therefore, the addition of the trace element Cr also needs to be cautious. The appropriate amount of Cr element can effectively control the grain structure of the plate, otherwise it will cause the alloy's quenching sensitivity to increase significantly, thereby reducing the strength of the alloy.
  • alloy compositions of Examples A7-A11 are basically similar, except that the preparation process and the thickness of the sheet are different, the alloy quenching sensitivity does not change significantly, and the mechanical properties are basically similar.
  • Example A6 alloy is added with 0.122% Mn element.
  • the addition of the same trace Mn element effectively reduces the average grain size of the alloy sheet to 24 ⁇ m ( Figure 9), but at the same time, compared to the example A3 alloy, it will slightly increase the quenching sensitivity of the alloy sheet.
  • the R values are 10.06% and 10.49%, respectively, but compared to the C2 alloy containing Cr in the same amount, the quenching sensitivity of Mn element to alloy sheet is significantly weaker than that of Cr element.
  • Increasing the Mn content to 0.263% (comparative C4 alloy) the alloy quenching sensitivity increases, and the yield strength loss coefficient R value increases.
  • the comparative C6 alloy has a lower alloy strength than the example alloy due to the lower content of the main elements Cu and Mg.
  • the strengthening phase is stable in the high temperature baking paint (BH) Poor performance, resulting in lower strength of the sample after the plate is painted; but because it does not contain trace elements such as Cr, Zr, Mn, the quenching sensitivity of the alloy plate is low.
  • Example A12-A25 alloy composition range is: Zn 7.6-9.6%, Mg 2.1-3.1%, Cu 1.4-2.6%, Fe 0-0.4%, Si 0-0.3%, Ti 0.01-0.15%, Cr 0-0.05 %, Zr 0-0.05%, Mn 0-0.25%, other grain size control elements 0-0.25%, and the balance is Al.
  • Table 3 shows the specific chemical composition and corresponding sheet state of the alloys of Examples A12-A25 and Comparative Examples C7-C12.
  • the alloy plates of Examples A12-A25 and Comparative Examples C7-C12 were subjected to rapid solution treatment at 480°C for 10 minutes (industrial production can be performed on-line continuous solution treatment), and then water-cooled (WQ) Or air cooling (AQ) two extreme cooling methods, followed by 120°C/24h T6 peak aging (PA) and 185°C/25min baking treatment (BH) respectively, and the tensile properties of the panels after different processes are tested. And calculate the corresponding strength loss coefficient R value.
  • the yield strength of the A12-A27 alloy sheet of the embodiment is more than 480 MPa, the tensile strength is more than 520 MPa, and the elongation is more than 5.5%. , Yield strength loss coefficient R ⁇ 15%.
  • the performance results are shown in Table 4.
  • the tensile properties of the A12-A25 alloy sheet of the present application are significantly higher than the C7-C12 alloy sheet of the comparative example, with a yield strength of >480 MPa, a tensile strength of >520 MPa, and an elongation of >5.5%.
  • the yield strength loss coefficient R ⁇ 15%; while the comparative C7-C12 alloy sheet due to the excessive addition of trace elements Cr, Mn and Zr, the quenching sensitivity of the alloy sheet increases, and the yield strength loss coefficient R increases significantly.
  • the yield strength loss coefficient of the sheet is R ⁇ 8%, and the alloy quenching sensitivity is relatively low.
  • Example A16-A21 alloy similar to the example A4 alloy added with less than 0.05% of Zr element, the yield strength loss coefficient R of the water-cooled and air-cooled baking paint of the alloy sheet increased slightly, indicating that the addition of Zr element has a slight increase in the quenching sensitivity of the alloy. improve.
  • Zr content such as the comparative alloy C7-C9 alloy
  • the yield strength loss coefficient R of the sheet is significantly increased.
  • the R value of the comparative C7 alloy with the highest Zr content is as high as 24.23% and 35.44%, and the quenching sensitivity increases sharply. , There has been a significant loss of strength.
  • Example A22 and Example A23 are Cr-containing alloys with contents of 0.048% and 0.044%, respectively. Similar to the example A16-A21 alloy, the yield strength loss coefficient of the water-cooled and air-cooled paint (ie WQ+BH and AQ+BH) of the alloy sheet R has also risen slightly, but the impact is relatively small. With the increase of Cr content, such as the comparative examples C10 and C11 alloys, the Cr content is 0.212% and 0.125%, respectively, and the corresponding R value of the alloy sheet increases sharply, reaching 30.02%, 41.40%, 27.67%, and 38.42%, respectively.
  • Example A24 and Example A25 contain 0.131% and 0.245% Mn respectively.
  • Mn the yield strength loss coefficient R of the alloy sheet water-cooled and air-cooled paint (ie WQ+BH and AQ+BH) also appears A slight increase, the mechanical properties are not very obvious.
  • the Mn content increased to 0.336%, the alloy quenching sensitivity deteriorated significantly, the corresponding R value of the plate increased to 25.32% and 37.13%, and the alloy strength was greatly reduced.
  • Example A15 (without trace elements), C7 (containing 0.121% Zr), C10 (containing 0.212% Cr) and C12 (containing 0.336% Mn) alloy plates are solid-solved at 480°C for 10 minutes and then air-cooled to room temperature.
  • the structure of the alloy plates (Scanning electron microscope organization) are shown in Figure 10-13.
  • the dispersion formed has a strong control effect on the grain structure. Although it can effectively reduce the average grain size of the alloy, it has a greater impact on the quenching sensitivity of the plate, which is not conducive to the alloy.
  • the mechanical properties need to be added in an appropriate amount to adjust the grain structure according to the actual grain size requirements.

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Abstract

一种7xxx系铝合金或板材及其制造方法、加工方法和其在车辆部件制造中的应用，所述7xxx系铝合金或板材的化学成分按重量百分比配比为Zn 5.1-10.0％，Mg 2.0-3.2％，Cu 1.2-3.0％，Fe 0-0.5％，Si 0-0.4％，Ti 0-0.2％，Cr 0-0.1％，Zr 0-0.055％，Mn 0-0.25％，其它晶粒尺寸控制元素0-0.30％，余量为Al。所述7xxx系铝合金板材特别适用于热成形-淬火一体化加工。

Description

一种7xxx系铝合金或板材、其制造方法、其加工方法及其应用 技术领域
本发明属于有色金属领域，具体涉及一种7xxx系铝合金或板材。本发明还涉及所述7xxx系铝合金或板材的制造方法、加工方法及其在车辆部件制造中的应用。
背景技术
近几年，汽车业迅速发展，汽车轻量化需求受到能源环境等影响也十分迫切。汽车车身重量占汽车总重量的40％左右，汽车车身轻量化对于整车轻量化起着决定性的作用，车身轻量化已经成为目前汽车制造技术的前沿与热点。目前，常用于车身的铝合金汽车板主要是5xxx和6xxx系铝合金，但其强度较低，而高强度7xxx系铝合金的室温成形性能较低，限制了其在车身中的广泛应用。
传统的热成形工艺为了保证板材的成形性和零件强度，将板材坯料加热至所需温度后，转移至模具中进行热成形，随后再对成形零件进行常规的固溶时效强化处理，以获得最终性能的零件。这种工艺的工序繁琐，周期较长，后续零件热处理后尺寸精度难以保证，生产成本相对较高。热成形-淬火一体化工艺是针对铝合金的热处理和热成形相结合的复合工艺技术，将成形过程和热处理过程相结合，依靠同一套模具实现“成形”和“控性”。该工艺在保证材料强度的同时，提高材料成形过程中的塑性。将完全固溶后的铝合金板材快速转移到水冷模具上，然后快速合模成形，成形完成后保持合模以完成零件模内淬火，最后进行时效处理以提高其强度。该工艺是高强铝合金板材热成形中最具前景的新工艺，能够解决铝合金材料成形塑性差、回弹大，热处理时形状畸变的问题。
迄今为止，虽然热成形-淬火一体化工艺技术已经进行商业化应用，但目前主要应用报道主要集中在高强钢、5xxx和6xxx系铝合金，如AA5754、AA6016、AA6111等，通过铝合金热冲压工艺提 升原有板材的成形性，以生产形状更为复杂的零件。已知的是，5xxx和6xxx铝合金零部件强度都小于300MPa，无法满足于车身结构件高强度的性能需求。力学性能更好的7xxx系高强铝合金主要应用于航空航天领域，较少在车身中使用，因此相关的研究和应用尚属于起步阶段。
发明内容
本发明的发明人发现，热成形-淬火一体化工艺技术对于7xxx系铝合金板材的属性要求很高，特别包括短时固溶性、低淬火敏感性、良好热成形和时效硬化等，但是目前尚不存在能够满足这些要求的7xxx系铝合金板材。
本发明的发明人经过刻苦的研究，发现了一种7xxx系铝合金，该铝合金具有特定的合金组成，并且由其制造的板材特别适用于热成形-淬火一体化工艺。本发明基于该发现而完成。
具体而言，本发明涉及以下方面的内容。
1.一种7xxx系铝合金(优选板材)，其化学成分按重量百分比配比为Zn 5.1-10.0％，Mg 2.0-3.2％，Cu 1.2-3.0％，Fe 0-0.5％，Si 0-0.4％，Ti 0-0.2％，Cr 0-0.1％，Zr 0-0.055％，Mn 0-0.25％，其它晶粒尺寸控制元素0-0.30％，余量为Al。
2.前述或后述任一方面所述的7xxx系铝合金(优选板材)，其化学成分按重量百分比配比为Zn 5.4-7.6％，Mg 2.0-2.7％，Cu1.6-2.3％，Fe 0-0.4％，Si 0-0.3％，Ti 0.01-0.15％，Cr 0-0.05％，Zr 0-0.05％，Mn 0-0.25％，所述其它晶粒尺寸控制元素0-0.25％，余量为Al。
3.前述或后述任一方面所述的7xxx系铝合金(优选板材)，其化学成分按重量百分比配比为Zn 7.6-9.6％，Mg 2.1-3.1％，Cu 1.4-2.6％，Fe 0-0.4％，Si 0-0.3％，Ti 0.01-0.15％，Cr 0-0.05％，Zr 0-0.05％，Mn 0-0.25％，所述其它晶粒尺寸控制元素0-0.25％，余量为Al。
4.前述或后述任一方面所述的7xxx系铝合金(优选板材)，其化学成分按重量百分比配比为Zn 5.1-6.7％，Mg 2.0-2.9％，Cu 1.2-2.6％，Fe 0-0.5％，Si 0-0.4％，Cr 0-0.1％，Zr 0-0.05％，Mn 0-0.25％，余量为Al。
5.前述或后述任一方面所述的7xxx系铝合金(优选板材)，其化学成分按重量百分比配比为Zn 5.4-6.5％，Mg 2.0-2.7％，Cu 1.6-2.3％，Fe 0-0.4％，Si 0-0.3％，Cr 0-0.05％，Zr 0-0.05％，Mn 0-0.15％，余量为Al。
6.前述或后述任一方面所述的7xxx系铝合金(优选板材)，其中Fe 0.05-0.4％，Si 0.05-0.3％，Cr 0.001-0.05％，Zr 0.001-0.04％，Mn 0.001-0.15％，所述其它晶粒尺寸控制元素0-0.15％。
7.前述或后述任一方面所述的7xxx系铝合金(优选板材)，其中Cr 0-0.05％，Zr 0-0.04％，Mn 0-0.15％，所述其它晶粒尺寸控制元素0-0.15％，和/或，Cr、Mn、Zr和所述其它晶粒尺寸控制元素(优选Cr、Mn和Zr，比如单独存在、或者两种或多种同时存在)的总重量百分比含量≤0.25％(优选≤0.20％或≤0.15％)。
8.前述或后述任一方面所述的7xxx系铝合金板材，在450-510℃保温5-20min后，其平均晶粒尺寸为10-100微米(优选15-70微米)，和/或，其厚度为0.5-10.0mm(优选1.0-4.0mm)。
9.前述或后述任一方面所述的7xxx系铝合金板材，具有至少一项以下性能：
(1)适用于热成形-淬火一体化加工，
(2)具备快速固溶性，在450-510℃保温5-20min能快速完成固溶处理，
(3)具备低淬火敏感性，
(4)是冷轧态、O态或T4态板材。
10.前述或后述任一方面所述的7xxx系铝合金板材，在450-510℃保温5-20min，随后空冷或模具冷却或水冷，再经人工 峰时效或烤漆处理之后，其屈服强度＞400MPa(优选＞480MPa)、抗拉强度＞450MPa(优选＞520MPa)、延伸率＞6.5％(优选＞5.5％)。
11.一种7xxx系铝合金板材的制造方法，包括对7xxx系铝合金铸锭进行均匀化处理、热轧处理和冷轧处理而获得所述7xxx系铝合金板材的步骤，其中所述7xxx系铝合金铸锭的化学成分按重量百分比配比为Zn 5.1-10.0％，Mg 2.0-3.2％，Cu 1.2-3.0％，Fe 0-0.5％，Si 0-0.4％，Ti 0-0.2％，Cr 0-0.1％，Zr 0-0.055％，Mn 0-0.30％，余量为Al。
12.前述或后述任一方面所述的制造方法，其中所述均匀化处理包括：将所述7xxx系铝合金铸锭升温至375-460℃(优选400℃-450℃)，保温0-15h(优选5-10h)之后，升温至465-490℃(优选470℃-490℃或470℃-485℃)，然后保温10-48h(优选10-36h或16-36h)，随后空冷或风冷或随炉冷却至室温，升温速率为15-75℃/h(优选25-75℃/h或25-50℃/h)，和/或，所述热轧处理包括：热粗轧和热精轧至4-14mm(优选4-8mm或6-10mm)，终轧温度为200-460℃(优选250-350℃、300-460℃或350-450℃)，卷曲之后空冷至室温，和/或，所述冷轧处理包括：冷轧至0.5-10.0mm(优选1.0-4.0mm)，得到所述7xxx系铝合金板材(冷轧态)，和/或，所述制造方法还包括将所述冷轧态的7xxx系铝合金板材进行箱式或连续退火的步骤，以得到O态或T4态的所述7xxx系铝合金板材，和/或，所述制造方法还包括在所述热轧处理之前，将所述经过均匀化处理的铸锭在300-480℃(优选380-460℃)保温2-30h(优选3-20h)的步骤。
13.一种热成形-淬火一体化加工方法，包括将前述或后述任一方面所述的7xxx系铝合金板材或者按照前述或后述任一方面所述的制造方法制造的7xxx系铝合金板材进行热成形-淬火一体化加工的步骤。
14.一种车辆部件(特别是汽车零部件)，由前述或后述任一方面所述的7xxx系铝合金板材制成或者通过前述或后述任一方面 所述的加工方法进行制造。
15.一种车辆，具备前述或后述任一方面所述的车辆部件。
技术效果
本发明提供的铝合金板材具有以下有益效果之一或其组合。
(1)适用于热成形-淬火一体化加工。
(2)优异的短时固溶性。
(3)优异的淬火敏感性。
(4)优异的时效硬化或烤漆硬化性。
(5)优异的热成形性。
附图说明
图1实施例A1合金板材经480℃/5min固溶后的晶粒组织。
图2实施例A3合金板材经480℃/5min固溶后的晶粒组织。
图3对比例C5合金板材经480℃/5min固溶后的晶粒组织。
图4实施例A4合金板材经480℃/5min固溶后的晶粒组织。
图5对比例C1合金板材经480℃/5min固溶后的晶粒组织。
图6实施例A5合金板材经480℃/5min固溶后的晶粒组织。
图7对比例C2合金板材经480℃/5min固溶后的晶粒组织。
图8对比例C3合金板材经480℃/5min固溶后的晶粒组织。
图9实施例A6合金板材经480℃/5min固溶后的晶粒组织。
图10实施例A15合金板材经480℃/10min固溶后扫描组织。
图11对比例C7合金板材经480℃/10min固溶后扫描组织。
图12对比例C10合金板材经480℃/10min固溶后扫描组织。
图13对比例C12合金板材经480℃/10min固溶后扫描组织。
具体实施方式
下面对本发明的具体实施方式进行详细说明，但是需要指出的是，本发明的保护范围并不受这些具体实施方式的限制，而是由附 录的权利要求书来确定。
本说明书提到的所有出版物、专利申请、专利和其它参考文献全都引于此供参考。除非另有定义，本说明书所用的所有技术和科学术语都具有本领域技术人员常规理解的含义。在有冲突的情况下，以本说明书的定义为准。
当本说明书以词头“本领域技术人员公知”、“现有技术”或其类似用语来导出材料、物质、方法、步骤、装置或部件等时，该词头导出的对象涵盖本申请提出时本领域常规使用的那些，但也包括目前还不常用，却将变成本领域公认为适用于类似目的的那些。
在本说明书的上下文中，所谓“基本上”指的是允许存在对于本领域技术人员而言可以接受或认为合理的偏差，比如偏差在±5％以内、±1％以内、±0.5％以内或者±0.1％以内。
在本说明书的上下文中，在没有特别指明的情况下，在描述7xxx系铝合金板材的制造方法时，温度一般指的是处理(比如退火、均匀化或热轧)时材料本身的温度。
在本说明书的上下文中，在没有特别指明的情况下，表述“余量为Al”指的是“余量为Al和不可避免的杂质”。这对于本领域技术人员而言是显然的。
在本说明书的上下文中，人工峰时效可以按照本领域技术人员公知的任何方式进行，并没有特别的限定。作为举例而言，一般100～130℃保温5～48h。
在本说明书的上下文中，烤漆处理可以按照本领域技术人员公知的任何方式进行，并没有特别的限定。作为举例而言，一般170～190℃保温20～40min。
在本说明书的上下文中，屈服强度的测量方法是参照ASTM E8/E8M-16ae1标准。
在本说明书的上下文中，抗拉强度的测量方法是参照ASTM E8/E8M-16ae1标准。
在本说明书的上下文中，延伸率的测量方法是参照ASTM  E8/E8M-16ae1标准。
在本说明书的上下文中，平均晶粒尺寸的测量方法是参照ASTM E112-13标准。
在没有明确指明的情况下，本说明书内所提到的所有百分数、份数、比率等都是以重量为基准的，而且压力是表压。
在本说明书的上下文中，本发明的任何两个或多个实施方式都可以任意组合，由此而形成的技术方案属于本说明书原始公开内容的一部分，同时也落入本发明的保护范围。
根据本发明的一个实施方式，涉及一种7xxx系铝合金，特别是板材形式的7xxx系铝合金(即，7xxx系铝合金板材)。所述7xxx系铝合金板材特别适用于热成形-淬火一体化加工。一般而言，该铝合金板材具有中强度或高强度。
根据本发明的一个实施方式，所述7xxx系铝合金或板材的化学成分按重量百分比配比为Zn 5.1-10.0％，Mg 2.0-3.2％，Cu 1.2-3.0％，Fe 0-0.5％，Si 0-0.4％，Ti 0-0.2％，Cr 0-0.1％，Zr 0-0.055％，Mn 0-0.25％，其它晶粒尺寸控制元素0-0.30％，余量为Al。
在本说明书的上下文中，所谓“其它晶粒尺寸控制元素”，指的是本领域技术人员公知可以用于调节(增加或降低)铝合金晶粒尺寸的任何微量元素(除了Cr、Zr和Mn)。为此，作为所述其它晶粒尺寸控制元素，具体比如可以举出Er、Sc、Hf、Dy、Gd等。这些其它晶粒尺寸控制元素可以单独使用一种，也可以两种或更多种组合使用。
在不受任何理论限制的情况下，本发明的发明人认为，通过控制Fe、Si含量，可以降低整个合金原材料制备和后续使用成本，并有一定的细化晶粒组织的效果。另外，本发明的发明人还认为，基于热成形-淬火一体化工艺对铝合金材料属性要求，通过严控主合金元素Zn、Mg和Cu含量，减少高温残留相Al 2CuMg相，确保合金板材在热成形-淬火一体化工艺的加热和短时保温阶段，残留第 二相能快速回溶基体中，保证合金热成形性和后续力学性能。而且，本发明的发明人还认为，通过严格控制Cr、Zr和Mn等晶粒尺寸控制元素的含量，确保合金板材具备较低的淬火敏感性，同时控制板材晶粒尺寸，使板材在高温固溶模冷淬火后，基体能获得较大的过饱和度，具备较优的晶粒组织，并在后续的人工峰时效或烤漆处理后，最终合金板材的屈服强度＞400MPa、抗拉强度＞450MPa、延伸率＞6.5％。
根据本发明的一个实施方式，所述7xxx系铝合金或板材的化学成分按重量百分比配比为Zn 5.4-7.6％，Mg 2.0-2.7％，Cu 1.6-2.3％，Fe 0-0.4％，Si 0-0.3％，Ti 0.01-0.15％，Cr 0-0.05％，Zr 0-0.05％，Mn 0-0.25％，所述其它晶粒尺寸控制元素0-0.25％，余量为Al。
根据本发明的一个实施方式，所述7xxx系铝合金或板材的化学成分按重量百分比配比为Zn 7.6-9.6％，Mg 2.1-3.1％，Cu 1.4-2.6％，Fe 0-0.4％，Si 0-0.3％，Ti 0.01-0.15％，Cr 0-0.05％，Zr 0-0.05％，Mn 0-0.25％，所述其它晶粒尺寸控制元素0-0.25％，余量为Al。
根据本发明的一个实施方式，所述7xxx系铝合金或板材的化学成分按重量百分比配比为Zn 5.1-6.7％，Mg 2.0-2.9％，Cu 1.2-2.6％，Fe 0-0.5％，Si 0-0.4％，Cr 0-0.1％，Zr 0-0.05％，Mn 0-0.25％，余量为Al。
根据本发明的一个实施方式，基于热成形-淬火一体化工艺对铝合金板材的固溶性和淬火敏感性要求优选的是，所述7xxx系铝合金或板材的化学成分按重量百分比配比为Zn 5.4-6.5％，Mg 2.0-2.7％，Cu 1.6-2.3％，Fe 0-0.4％，Si 0-0.3％，Cr 0-0.05％，Zr 0-0.05％，Mn 0-0.15％，余量为Al。
根据本发明的一个实施方式，在所述7xxx系铝合金或板材中，Fe 0.05-0.4％，Si 0.05-0.3％，Cr 0.001-0.05％，Zr 0.001-0.04％，Mn 0.001-0.15％，所述其它晶粒尺寸控制元素0-0.15％。
根据本发明的一个实施方式，在所述7xxx系铝合金或板材中，Cr 0-0.05％，Zr 0-0.04％，Mn 0-0.25％，所述其它晶粒尺寸控制元素0-0.15％。
根据本发明，Cr、Mn、Zr和所述其它晶粒尺寸控制元素都是晶粒尺寸控制元素，优选Cr、Mn和Zr。这些晶粒尺寸控制元素可以单独使用一种，也可以两种或更多种组合使用。根据本发明的一个实施方式，在单独或组合使用时，这些晶粒尺寸控制元素的总重量百分比含量(单独使用时，指的是该种元素的重量百分比含量)一般为≤0.30％，优选≤0.25％或≤0.15％。
根据本发明的一个实施方式，所述7xxx系铝合金板材在450-510℃保温5-20min后，其平均晶粒尺寸一般为10-100微米，优选15-70微米。
根据本发明的一个实施方式，所述7xxx系铝合金板材的厚度一般为0.5-10.0mm，优选1.0-4.0mm。
根据本发明的一个实施方式，所述7xxx系铝合金板材特别适用于热成形-淬火一体化加工。
根据本发明的一个实施方式，所述7xxx系铝合金板材具备快速固溶性，即在450-510℃保温5-20min能快速完成固溶处理。
根据本发明的一个实施方式，所述7xxx系铝合金板材具备低淬火敏感性。
根据本发明的一个实施方式，所述7xxx系铝合金板材是冷轧态、O态或T4态板材。
根据本发明的一个实施方式，所述7xxx系铝合金板材在450-510℃保温5-20min，随后空冷或模具冷却或水冷，再经人工峰时效或烤漆处理之后，其屈服强度一般＞400MPa，优选＞480MPa。
根据本发明的一个实施方式，所述7xxx系铝合金板材在450-510℃保温5-20min，随后空冷或模具冷却或水冷，再经人工峰时效或烤漆处理之后，其抗拉强度一般＞450MPa，优选＞520MPa。
根据本发明的一个实施方式，所述7xxx系铝合金板材在 450-510℃保温5-20min，随后空冷或模具冷却或水冷，再经人工峰时效或烤漆处理之后，其延伸率一般＞6.5％，优选＞5.5％。
根据本发明的一个实施方式，还涉及一种7xxx系铝合金板材的制造方法。所述制造方法可以用于制造本发明如前文所述的任意一种7xxx系铝合金板材。
根据本发明的一个实施方式，所述制造方法包括对7xxx系铝合金铸锭进行均匀化处理、热轧处理和冷轧处理而获得所述7xxx系铝合金板材的步骤。在此，所述7xxx系铝合金铸锭是本发明如前文所述的任意一种7xxx系铝合金的铸锭。举例而言，所述7xxx系铝合金铸锭的化学成分按重量百分比配比为Zn 5.1-10.0％，Mg 2.0-3.2％，Cu 1.2-3.0％，Fe 0-0.5％，Si 0-0.4％，Ti 0-0.2％，Cr 0-0.1％，Zr 0-0.055％，Mn 0-0.30％，余量为Al。
根据本发明的一个实施方式，在所述制造方法中，所述均匀化处理可以按照本领域技术人员公知的任何方式进行，并没有特别的限定。作为举例而言，一般将所述7xxx系铝合金铸锭升温至375-460℃(优选400℃-450℃)，保温0-15h(优选5-10h)之后，升温至465-490℃(优选470℃-490℃或470℃-485℃)，然后保温10-48h(优选10-36h或16-36h)，随后空冷或风冷或随炉冷却至室温。在此，所述均匀化处理的升温速率一般为15-75℃/h，优选25-75℃/h或25-50℃/h。
根据本发明的一个实施方式，在所述制造方法中，所述热轧处理可以按照本领域技术人员公知的任何方式进行，并没有特别的限定。作为举例而言，一般热粗轧和热精轧至4-14mm，优选热粗轧和热精轧至4-8mm或6-10mm。在此，所述热轧处理的终轧温度为200-460℃，优选250-350℃、300-460℃或350-450℃。然后，将热精轧板材卷曲之后空冷至室温。
根据本发明的一个实施方式，在所述制造方法中，所述冷轧处理可以按照本领域技术人员公知的任何方式进行，并没有特别的限定。作为举例而言，一般冷轧至0.5-10.0mm，优选冷轧至1.0-4.0mm， 以得到所述7xxx系铝合金板材。此时，所述7xxx系铝合金板材是冷轧态板材。
根据本发明的一个实施方式，所述制造方法还包括将所述冷轧态的7xxx系铝合金板材进行箱式或连续退火的步骤，以得到O态或T4态的所述7xxx系铝合金板材。在此，所述箱式退火可以按照本领域技术人员公知的任何方式进行，并没有特别的限定。作为举例而言，其操作条件一般包括：将铝合金卷放入在箱式退火炉中以25-50℃/h升温速率加热到300-450℃，保温0.5-3h，然后冷却。另外，所述连续退火可以按照本领域技术人员公知的任何方式进行，并没有特别的限定。作为举例而言，其操作条件一般将铝合金带卷以10-80m/min速度通过炉温为400℃-500℃的连续退火炉，随后冷却收卷。
根据本发明的一个实施方式，所述制造方法还包括在所述热轧处理之前，将所述经过均匀化处理的铸锭在300-480℃保温2-30h的步骤。优选的是，将所述经过均匀化处理的铸锭在380-450℃保温3-20h。
根据本发明的一个实施方式，还涉及一种热成形-淬火一体化加工方法，包括将本说明书如前任一项所述的7xxx系铝合金板材或者按照本说明书如前任一项所述的制造方法制造的7xxx系铝合金板材进行热成形-淬火一体化加工的步骤。在此，所述热成形-淬火一体化加工可以按照本领域技术人员公知的任何方式进行，并没有特别的限定，由此在此省略其详细说明。
根据本发明的一个实施方式，还涉及一种车辆部件，特别是汽车部件。在此，所述车辆部件可以由本说明书如前任一项所述的7xxx系铝合金板材制成。另外，作为所述车辆部件的制造方法，可以按照本领域技术人员公知的任何方式进行，并没有特别的限定，但特别可以举出本说明书如前任一项所述的热成形-淬火一体化加工方法。
根据本发明的一个实施方式，还涉及一种车辆，其具备本说明 书如前任一项所述的车辆部件。
实施例
以下将通过实施例和比较例对本发明进行进一步的详细描述，但本发明不限于以下实施例。
所述7xxx铝合金冷却板材制备工艺为：合金铸锭采用工业半连续工艺制备，根据各铸锭所含微量元素特点，分别对铸锭进行均匀化处理，均匀化工艺为将合金铸锭在400℃保温10h，再在470℃保温24h后，升温速率为50℃/h，随后空冷或风冷至室温；将均匀化后坯料在440℃进行8h的保温后，进行热粗轧及热精轧至6mm，终轧温度300℃，然后卷曲，将合金热轧卷空冷至室温；最后对6mm后合金热轧卷进行冷轧(可根据情况选择冷轧—中间退火—冷轧工艺，即冷轧中间退火态，CAC态冷轧板)、卷曲，最终得到2mm厚度的合金冷轧板材。亦可将冷轧卷选择性进行箱式或连续退火，得到O态或T4态板材。
实施例A1-A11合金成分范围为：Zn 5.1-6.7％，Mg 2.0-2.9％，Cu 1.2-2.6％，Fe 0-0.5％，Si 0-0.4％，Cr 0-0.1％，Zr 0-0.05％，Mn 0-0.25％，其它晶粒尺寸控制元素0-0.25％，余量为Al。实施例A1-A11与对比例C1-C6合金的具体化学成分及相应的板材状态等如表1所示。
基于热成形-淬火一体化工艺特点，对实施例A1-A11与对比例C1-C6合金板材进行480℃快速固溶处理5min后(工业生产可进行在线连续固溶处理)，进行水冷(WQ)或空冷(AQ)两种极端冷却方式，随后分别进行120℃/24h的T6峰时效(PA)和180℃/30min的烤漆处理(BH)，对不同工艺处理后的板材进行拉伸性能测试，同时，引入合金板材空冷时效对水冷时效屈服强度的损失系数R,即：(水冷试样屈服强度-空冷试样屈服强度)/水冷试样屈服强度，相应计算式为R＝(WQ-AQ)/WQ，单位为％。经拉伸测试和计算，所述实施例A1-A11合金板材的屈服强度＞400MPa、抗拉强度＞450MPa、延伸率＞6.5％，屈服强度损失系数R≤20％。其性能结果 如表2所示。
表1实施例A1-A11和对比例C1-C6合金板材成分
合金素 Zn Mg Cu Fe Si Cr Zr Mn Al 状态
A1(实施例1) 5.63 2.73 1.59 0.10 0.02 0.0021 0.0003 0.005 余量 2mm冷轧态
A2(实施例2) 6.11 2.40 2.19 0.09 0.02 0.0027 0.0002 0.004 余量 2mm冷轧态
A3(实施例3) 5.52 2.59 1.72 0.30 0.20 0.0015 0.0003 0.004 余量 2mm冷轧态
A4(实施例4) 5.52 2.53 1.70 0.21 0.12 0.0015 0.0452 0.004 余量 2mm冷轧态
A5(实施例5) 5.69 2.66 1.69 0.23 0.13 0.0442 0.0002 0.005 余量 2mm冷轧态
A6(实施例6) 5.73 2.72 1.82 0.25 0.12 0.0024 0.0003 0.122 余量 2mm冷轧态
A7(实施例7) 5.71 2.68 1.79 0.24 0.11 0.0481 0.0001 0.004 余量 1mm冷轧态
A8(实施例8) 5.65 2.70 1.73 0.21 0.14 0.0425 0.0003 0.003 余量 4mm冷轧态
A9(实施例9) 5.70 2.68 1.64 0.24 0.11 0.0441 0.0002 0.005 余量 2mm CAC态
A10(实施例10) 5.69 2.63 1.67 0.23 0.13 0.0472 0.0003 0.004 余量 2mm O态
A11(实施例11) 5.59 2.71 1.70 0.26 0.14 0.0435 0.0001 0.003 余量 2mm T4态
C1(对比例1) 5.60 2.60 1.60 0.10 0.03 0.0032 0.0791 0.004 余量 2mm冷轧态
C2(对比例2) 5.75 2.65 1.72 0.24 0.12 0.1241 0.0006 0.004 余量 2mm冷轧态
C3(对比例3) 5.71 2.56 1.60 0.10 0.03 0.1811 0.0002 0.004 余量 2mm冷轧态
C4(对比例4) 5.71 2.73 1.79 0.21 0.13 0.0019 0.0003 0.263 余量 2mm冷轧态
C5(对比例5) 5.67 2.54 1.52 0.02 0.01 0.0054 0.0001 0.003 余量 2mm冷轧态
C6(对比例6) 5.49 1.42 0.28 0.25 0.12 0.0011 0.0002 0.003 余量 2mm冷轧态
表2实施例A1-A11和对比例C1-C6合金板材的性能结果
Figure PCTCN2020137405-appb-000001
Figure PCTCN2020137405-appb-000002
Figure PCTCN2020137405-appb-000003
由表2可知，本申请实施例A1-A11合金板材拉伸性能明显高于对比例C1-C6合金板材，屈服强度＞400MPa、抗拉强度＞450MPa、延伸率＞6.5％，屈服强度损失系数R≤20％。
实施例A1合金、实施例A2合金和实施例A3合金板材中主合金元素基本相近，微量元素Cr、Zr、Mn基本为零，合金板材淬火敏感性较低，屈服强度损失系数R≤15％。
实施例A1合金和实施例A2合金中Fe、Si元素比实施例A3合金低，而对比例C5合金以高纯铝为原料制备，合金中Fe、Si元素最低，但高Fe、Si含量在一定程度上能有效抑制板材晶粒长大行为，有利于调控晶粒组织；A1合金、A3合金和C5合金板材经固溶处理后，平均晶粒尺寸分别为64μm、61μm和109μm，如图1-3所示。同时，虽然对比例C5合金板材屈服强度损失系数R≤20％，但由于其晶粒尺寸较大，导致各工艺处理的C5合金板材强度均明显低于相应工艺处理的实施例A1合金、实施例A2合金和实施例A3合金板材强度。
实施例A4合金中含有0.0452％微量元素Zr，相比不含微量元素Zr的实施例A3合金，经固溶处理后，A4合金板材平均晶粒尺寸大幅度降低，约为37μm(如图4)，但淬火敏感性有所提高，其屈服强度损失系数R分别为6.73％和12.24％，明显高于A3合金板材(分别4.9％和5.0％)，说明Zr元素添加，在一定程度上提高合金淬火敏感性。如对比例C1合金中Zr元素含量提高至0.0791％，虽然平均晶粒尺寸能进一步降低至25μm左右(如图5)，但其淬火敏感性相比于实施例A4合金板材明显增加，R值分别增加至22.36％和34.55％，合金板材固溶后空冷时效试样强度显著下降。 对于微量元素Zr的添加，有利于控制板材晶粒尺寸，但需要适当控制，否则会大幅度提高淬火敏感性，可以显著降低合金板材的力学性能。
实施例A5合金、实施例A7-A11合金均含有微量Cr元素，含量约在0.05％以内，如图6所示实施例A5合金板材的平均晶粒尺寸相比不含微量元素的实施例A3合金由61μm降至39μm(图6)，相应合金板材淬火敏感性有所提高，但屈服强度损失系数R＜20％。随着Cr元素添加量的增加，虽然板材平均晶粒尺寸有所降低，但其淬火敏感性随之显著增加，如对比例C2合金(0.1241％Cr)和对比例C3合金(0.1811％Cr,为常规的7075合金板材成分)，板材平均晶粒尺寸分别降至32μm和27μm(图7和图8)，但其屈服强度损失系数R显著增加，并随着微量元素Cr含量增加而增加，分别为34.9％、38.63和46.54％、53.85％，相应的板材固溶后空冷时效试样强度显著降低。因此对于微量元素Cr的添加同样需要保持谨慎，适量的Cr元素有效调控板材晶粒组织，否则会导致合金淬火敏感性显著上升，从而降低合金的强度。
此外，实施例A7-A11合金成分基本相近，只是制备工艺和板材厚度存在差异，合金淬火敏感性未出现显著变化，力学性能基本相近。
实施例A6合金为添加0.122％Mn元素，同样微量Mn元素的加入，有效降低合金板材平均晶粒尺寸至24μm(图9)，但同时相比实施例A3合金会轻微增加合金板材淬火敏感性，其R值分别为10.06％和10.49％，但相比等量的对比例C2含Cr合金，Mn元素对合金板材淬火敏感性恶化明显弱于Cr元素。提高Mn含量至0.263％(对比例C4合金)，合金淬火敏感性增加，屈服强度损失系数R值增加。
对比例C6合金相比11组实施例合金合金，由于主元素Cu、Mg含量较低，合金强度明显低于实施例合金，同时由于Cu元素含量较低，在高温烤漆(BH)中强化相稳定性较差，造成板材烤漆后 试样的强度较低；但由于不含Cr、Zr、Mn等微量元素，合金板材的淬火敏感性较低。
实施例A12-A25合金成分范围为：Zn 7.6-9.6％，Mg 2.1-3.1％，Cu 1.4-2.6％，Fe 0-0.4％，Si 0-0.3％，Ti 0.01-0.15％，Cr 0-0.05％，Zr 0-0.05％，Mn 0-0.25％，其它晶粒尺寸控制元素0-0.25％，余量为Al。实施例A12-A25与对比例C7-C12合金的具体化学成分及相应的板材状态等如表3所示。
表3实施例A12-A25和对比例C7-C12合金板材成分
合金 Zn Mg Cu Fe Si Cr Zr Mn Al 状态
A12(实施例12) 7.76 2.13 2.09 0.09 0.03 0.0021 0.0002 0.0022 余量 2mm冷轧态
A13(实施例13) 7.73 2.23 1.93 0.24 0.12 0.0025 0.0002 0.0043 余量 2mm冷轧态
A14(实施例14) 8.18 2.10 1.52 0.09 0.031 0.0057 0.0003 0.0034 余量 2mm冷轧态
A15(实施例15) 9.01 2.38 2.23 0.09 0.032 0.0057 0.0002 0.0036 余量 2mm冷轧态
A16(实施例16) 8.37 2.55 1.95 0.17 0.084 0.0060 0.0450 0.0058 余量 2mm冷轧态
A17(实施例17) 8.98 2.86 1.99 0.17 0.081 0.0059 0.0490 0.0060 余量 1mm冷轧态
A18(实施例18) 9.22 2.91 1.96 0.17 0.076 0.0061 0.0430 0.0056 余量 4mm冷轧态
A19(实施例19) 8.70 2.69 2.50 0.18 0.076 0.0067 0.0400 0.0059 余量 2mm CAC态
A20(实施例20) 8.94 2.77 1.54 0.18 0.076 0.0061 0.0480 0.0060 余量 2mm O态
A21(实施例21) 8.91 2.14 2.02 0.19 0.073 0.0059 0.0460 0.0058 余量 2mm T4态
A22(实施例22) 8.99 2.83 2.19 0.17 0.082 0.0480 0.0003 0.0060 余量 2mm冷轧态
A23(实施例23) 8.95 2.73 1.98 0.16 0.078 0.0440 0.0004 0.0055 余量 2mm冷轧态
A24(实施例24) 9.19 2.53 2.09 0.15 0.081 0.0052 0.0002 0.1310 余量 2mm冷轧态
A25(实施例25) 8.91 2.59 1.98 0.16 0.078 0.0050 0.0003 0.2450 余量 2mm冷轧态
C7(对比例7) 8.95 2.13 2.21 0.18 0.083 0.0053 0.1210 0.0051 余量 2mm冷轧态
C8(对比例8) 9.01 2.09 2.11 0.16 0.081 0.0051 0.0920 0.0051 余量 2mm冷轧态
C9(对比例9) 8.93 2.19 2.22 0.19 0.083 0.0049 0.0750 0.0051 余量 2mm冷轧态
C10(对比例10) 8.99 2.10 2.13 0.15 0.075 0.212 0.0003 0.0056 余量 2mm冷轧态
C11(对比例11) 9.11 2.23 2.19 0.18 0.080 0.125 0.0004 0.0061 余量 2mm冷轧态
C12(对比例12) 8.83 1.98 2.22 0.17 0.073 0.0049 0.0005 0.3360 余量 2mm冷轧态
基于热成形-淬火一体化工艺特点，对实施例A12-A25与对比例C7-C12合金板材进行480℃快速固溶处理10min后(工业生产可进行在线连续固溶处理)，进行水冷(WQ)或空冷(AQ)两种极端冷却方式，随后分别进行120℃/24h的T6峰时效(PA)和185℃/25min的烤漆处理(BH)，对不同工艺处理后的板材进行拉 伸性能测试，并计算出相应强度损失系数R值。经测试和计算，所述实施例A12-A27合金板材的屈服强度＞480MPa、抗拉强度＞520MPa、延伸率＞5.5％。，屈服强度损失系数R≤15％。其性能结果如表4所示。
表4实施例A12-A25和对比例C7-C12合金板材性能结果
Figure PCTCN2020137405-appb-000004
Figure PCTCN2020137405-appb-000005
Figure PCTCN2020137405-appb-000006
由表4可知，本申请实施例A12-A25合金板材拉伸性能明显高于对比例C7-C12合金板材，屈服强度＞480MPa、抗拉强度＞520MPa、延伸率＞5.5％。，屈服强度损失系数R≤15％；而对比例C7-C12合金板材由于微量元素Cr、Mn和Zr过量添加，合金板材淬火敏感性提高，屈服强度损失系数R显著增加。
实施例A12-A15合金，由于没有添加Cr、Mn和Zr等微量元素，板材屈服强度损失系数R＜8％，合金淬火敏感性相对较低。
实施例A16-A21合金，类似于实施例A4合金添加了约0.05％以内的Zr元素，合金板材水冷、空冷烤漆的屈服强度损失系数R出现轻微上升，说明Zr元素的加入合金淬火敏感性有所提高。同样，随着Zr含量的增加，如对比例合金C7-C9合金，板材屈服强度损失系数R显著提高，其中Zr含量最高的对比例C7合金R值高达24.23％和35.44％，淬火敏感性急剧增加，强度出现了明显的损失。
实施例A22和实施例A23为含Cr合金，含量分别为0.048％和0.044％，类似实施例A16-A21合金，合金板材水冷、空冷烤漆(即WQ+BH和AQ+BH)的屈服强度损失系数R也出现了轻微上升，但影响相对较小。随着Cr含量的增加，如对比例C10和C11合金，其Cr含量分别为0.212％和0.125％，合金板材对应R值急剧增大，分别达到30.02％、41.40％和27.67％、38.42％，相应的强度急剧衰退，其AQ+PA试样屈服强度小于400MPa，AQ+BH试样屈服强度更低，Cr元素的过量加入显著恶化合金淬火敏感性。
实施例A24和实施例A25合金分别含0.131％和0.245％Mn元素，同理Mn元素的添加，合金板材水冷、空冷烤漆(即WQ+BH和AQ+BH)的屈服强度损失系数R也出现了轻微上升，力学性能影响并不十分明显。但Mn含量提高到0.336％，合金淬火敏感性显著恶化，板材 相应的R值提高至25.32％和37.13％，合金强度出现大幅度了大幅度降低。
实施例A15(不含微量元素)、C7(含0.121％Zr)、C10(含0.212％Cr)和C12(含0.336％Mn)合金板材经480℃固溶10min后空冷至室温，其合金板材组织(扫描电镜组织)分别如图10-13所示。明显发现实施例A15合金板材组织晶内、晶界较为干净，除残留的块状Al 7Cu 2Fe相以外，无其他残留第二相存在(如图10)；但对于添加微量元素Cr、Zr、Mn的对比例C7、C10和C12合金板材，合金板材淬火敏感性提高，板材组织中除了残留的Al 7Cu 2Fe相外，同时有细小的第二相颗粒存在(如图11-13)。
因此，对于Cr、Mn、Zr等微量元素添加，形成的弥散相对晶粒组织有较强的调控作用，虽能有效降低合金平均晶粒尺寸，但对板材淬火敏感性影响较大，不利于合金力学性能，需根据实际晶粒尺寸需求，适量添加以调控晶粒组织。
以上所述仅为本发明的优选实施方式，应当指出，对于本技术领域的普通技术人员来说，在不脱离本发明原理的前提下，还可以做出若干改进和优化，这些改进和优化也应视为本发明的保护范围。

Claims (15)

  1. 一种7xxx系铝合金(优选板材)，其化学成分按重量百分比配比为Zn 5.1-10.0％，Mg 2.0-3.2％，Cu 1.2-3.0％，Fe 0-0.5％，Si 0-0.4％，Ti 0-0.2％，Cr 0-0.1％，Zr 0-0.055％，Mn 0-0.25％，其它晶粒尺寸控制元素0-0.30％，余量为Al。
  2. 权利要求1所述的7xxx系铝合金(优选板材)，其化学成分按重量百分比配比为Zn 5.4-7.6％，Mg 2.0-2.7％，Cu 1.6-2.3％，Fe 0-0.4％，Si 0-0.3％，Ti 0.01-0.15％，Cr 0-0.05％，Zr 0-0.05％，Mn 0-0.25％，所述其它晶粒尺寸控制元素0-0.25％，余量为Al。
  3. 权利要求1所述的7xxx系铝合金(优选板材)，其化学成分按重量百分比配比为Zn 7.6-9.6％，Mg 2.1-3.1％，Cu 1.4-2.6％，Fe 0-0.4％，Si 0-0.3％，Ti 0.01-0.15％，Cr 0-0.05％，Zr 0-0.05％，Mn 0-0.25％，所述其它晶粒尺寸控制元素0-0.25％，余量为Al。
  4. 权利要求1-3任一项所述的7xxx系铝合金(优选板材)，其化学成分按重量百分比配比为Zn 5.1-6.7％，Mg 2.0-2.9％，Cu 1.2-2.6％，Fe 0-0.5％，Si 0-0.4％，Cr 0-0.1％，Zr 0-0.05％，Mn 0-0.25％，余量为Al。
  5. 权利要求1-4任一项所述的7xxx系铝合金(优选板材)，其化学成分按重量百分比配比为Zn 5.4-6.5％，Mg 2.0-2.7％，Cu 1.6-2.3％，Fe 0-0.4％，Si 0-0.3％，Cr 0-0.05％，Zr 0-0.05％，Mn 0-0.15％，余量为Al。
  6. 权利要求1-5任一项所述的7xxx系铝合金(优选板材)，其中Fe 0.05-0.4％，Si 0.05-0.3％，Cr 0.001-0.05％，Zr 0.001-0.04％，Mn 0.001-0.15％，所述其它晶粒尺寸控制元素0-0.15％。
  7. 权利要求1-6任一项所述的7xxx系铝合金(优选板材)，其中Cr 0-0.05％，Zr 0-0.04％，Mn 0-0.15％，所述其它晶粒尺寸控制元素0-0.15％，和/或，Cr、Mn、Zr和所述其它晶粒尺寸控制元素(优选Cr、Mn和Zr，比如单独存在、或者两种或多种同时存 在)的总重量百分比含量≤0.25％(优选≤0.20％或≤0.15％)。
  8. 权利要求1-7任一项所述的7xxx系铝合金板材，在450-510℃保温5-20min后，其平均晶粒尺寸为10-100微米(优选15-70微米)，和/或，其厚度为0.5-10.0mm(优选1.0-4.0mm)。
  9. 权利要求1-8任一项所述的7xxx系铝合金板材，具有至少一项以下性能：
    (1)适用于热成形-淬火一体化加工，
    (2)具备快速固溶性，在450-510℃保温5-20min能快速完成固溶处理，
    (3)具备低淬火敏感性，
    (4)是冷轧态、O态或T4态板材。
  10. 权利要求1-9任一项所述的7xxx系铝合金板材，在450-510℃保温5-20min，随后空冷或模具冷却或水冷，再经人工峰时效或烤漆处理之后，其屈服强度＞400MPa(优选＞480MPa)、抗拉强度＞450MPa(优选＞520MPa)、延伸率＞6.5％(优选＞5.5％)。
  11. 一种7xxx系铝合金板材的制造方法，包括对7xxx系铝合金铸锭进行均匀化处理、热轧处理和冷轧处理而获得所述7xxx系铝合金板材的步骤，其中所述7xxx系铝合金铸锭的化学成分按重量百分比配比为Zn 5.1-10.0％，Mg 2.0-3.2％，Cu 1.2-3.0％，Fe 0-0.5％，Si 0-0.4％，Ti 0-0.2％，Cr 0-0.1％，Zr 0-0.055％，Mn 0-0.30％，余量为Al。
  12. 权利要求11所述的制造方法，其中所述均匀化处理包括：将所述7xxx系铝合金铸锭升温至375-460℃(优选400℃-450℃)，保温0-15h(优选5-10h)之后，升温至465-490℃(优选470℃-490℃或470℃-485℃)，然后保温10-48h(优选10-36h或16-36h)，随后空冷或风冷或随炉冷却至室温，升温速率为15-75℃/h(优选25-75℃/h或25-50℃/h)，和/或，所述热轧处理包括：热粗轧和热精轧至4-14mm(优选4-8mm或6-10mm)，终轧温度为200-460℃(优选250-350℃、300-460℃或350-450℃)，卷曲之后空冷至室 温，和/或，所述冷轧处理包括：冷轧至0.5-10.0mm(优选1.0-4.0mm)，得到所述7xxx系铝合金板材(冷轧态)，和/或，所述制造方法还包括将所述冷轧态的7xxx系铝合金板材进行箱式或连续退火的步骤，以得到O态或T4态的所述7xxx系铝合金板材，和/或，所述制造方法还包括在所述热轧处理之前，将所述经过均匀化处理的铸锭在300-480℃(优选380-450℃)保温2-30h(优选3-20h)的步骤。
  13. 一种热成形-淬火一体化加工方法，包括将权利要求1-10任一项所述的7xxx系铝合金板材或者按照权利要求11或12所述的制造方法制造的7xxx系铝合金板材进行热成形-淬火一体化加工的步骤。
  14. 一种车辆部件(特别是汽车零部件)，由权利要求1-10任一项所述的7xxx系铝合金板材制成或者通过权利要求13所述的加工方法进行制造。
  15. 一种车辆，具备权利要求14所述的车辆部件。
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