WO2015127805A1 - Alliage d'aluminium durci par cuisson à température élevée pour carrosserie d'automobile et procédé de préparation de celui-ci - Google Patents

Alliage d'aluminium durci par cuisson à température élevée pour carrosserie d'automobile et procédé de préparation de celui-ci Download PDF

Info

Publication number
WO2015127805A1
WO2015127805A1 PCT/CN2014/092726 CN2014092726W WO2015127805A1 WO 2015127805 A1 WO2015127805 A1 WO 2015127805A1 CN 2014092726 W CN2014092726 W CN 2014092726W WO 2015127805 A1 WO2015127805 A1 WO 2015127805A1
Authority
WO
WIPO (PCT)
Prior art keywords
temperature
aluminum alloy
alloy
treatment
aging
Prior art date
Application number
PCT/CN2014/092726
Other languages
English (en)
Chinese (zh)
Inventor
郭明星
庄林忠
张济山
Original Assignee
北京科技大学
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 北京科技大学 filed Critical 北京科技大学
Publication of WO2015127805A1 publication Critical patent/WO2015127805A1/fr

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—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
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon

Definitions

  • the invention belongs to the technical field of aluminum alloys, relates to a novel high-baked hardened aluminum alloy material which can be industrially applied and a preparation method thereof, and is particularly developed for the special requirements of forming properties and anti-pitching properties of aluminum alloy for exterior body of automobile body, It can ensure that the aluminum alloy sheet has a low yield strength before forming, and exhibits excellent paint hardening characteristics in the short-time baking process after forming.
  • Typical alloy series are: Al-Cu series, Al -Mg series and Al-Mg-Si series, among which Al-Mg series alloys are mainly used for the manufacture of automobile inner panels, and Al-Mg-Si series alloys are mainly used for the manufacture of automobile exterior panels.
  • alloy sheets are generally required to have the following characteristics: high formability, low resilience performance, dent resistance, corrosion resistance, and excellent surface quality.
  • high formability and low resilience generally require alloy sheets to have lower yield strength, while anti-pitching properties require alloy sheets to have higher yield strength.
  • Al-Mg series alloys cannot meet this requirement as work-hardening alloys, while Al-Mg-Si series alloys have good paint hardening properties, which can meet the requirements of high formability, low resilience and anti-pitting.
  • commercial products have been mainly used in series of alloys such as AA6016 and AA6111.
  • the paint hardening increment is only 30-40 MPa, and after a certain pre-aging treatment, the paint hardening increases. It is also generally only between 80 and 90 MPa.
  • the optimization of the Mg, Si and Cu contents of some alloys and the reasonable adjustment of the pre-aging process can increase the paint hardening to about 120 MPa.
  • the baking lacquer process is gradually developing towards a low temperature, the increase in the hardening of the paint is far from meeting the performance requirements of the new-generation automobile exterior plate for the aluminum alloy material, so it is urgent to develop a new aluminum alloy with a fast aging response type and a preparation method thereof. This enables the corresponding alloy sheet to have a more excellent paint hardening increment.
  • the MgZn 2 strengthening phase can greatly improve the strength of the Al-Zn-Mg-Cu alloy
  • a certain amount of elemental Zn can be added to the Al-Mg-Si series alloy matrix, it can be regulated by a suitable processing and heat treatment process.
  • the alloy rapidly precipitates a large number of Mg 2 Si and MgZn 2 strengthening phases or the transition of the two strengthening phases is equal, thereby achieving multi-phase synergistic precipitation and then exerting multi-phase synergistic strengthening.
  • the developed alloy should be able to exhibit excellent performance.
  • the hardening properties of the paint should be able to exhibit excellent performance.
  • the Mg content of the common solute elements of the two strengthening phases should be higher, and therefore, the corresponding Mg/Si ratio, Cu and The Zn content must be designed reasonably.
  • the invention is based on this design idea to develop a new alloy composition design and preparation process.
  • the present invention develops a new type of aluminum alloy having high paint hardening performance in view of the problem that the hardening performance of the Al-Mg-Si alloy paint for automotive exterior panels is not high enough.
  • the new alloy makes full use of the solute element Mg to interact with the solute elements Si and Zn simultaneously, and thus can rapidly form Mg 2 Si and MgZn 2 (or their corresponding transition phases) in the baking process, and finally make the alloy
  • the increase in baking hardening has been greatly increased.
  • the invention alloy is suitable for the manufacture of automobile exterior panels, in particular, it is required to have an excellent paint hardening increment after the automobile body outer panel is formed, and an automobile body outer panel material manufacturer which has been or is going to adopt a low temperature baking paint process.
  • the invention firstly selects the composition range of the new high-baked hardened aluminum alloy by component design and optimization, and then prepares the designed alloy through the process of smelting casting and studies the aging precipitation behavior, and finally determines the new aluminum with high baking hardening property.
  • the specific preparation process is as follows: FactSage phase diagram calculation ⁇ new aluminum alloy composition selection ⁇ alloy preparation and smelting casting ⁇ ingot homogenization ⁇ hot rolling deformation ⁇ intermediate annealing ⁇ cold rolling deformation ⁇ solid solution ⁇ quenching ⁇ pre-aging ⁇ stamping forming ( Or pre-deformation ⁇ ⁇ simulate baking hardening treatment (as shown in Figure 1).
  • a first object of the present invention is to provide a novel aluminum alloy for an automobile body outer panel having high paint hardening property, wherein the chemical composition and mass percentage of the aluminum alloy are: Zn: 0.05 to 4.0 wt%, Mg 0.5 to 1.5 Wt%, Si 0.2 to 1.2 wt%, Cu 0 to 1.0 wt%, Fe ⁇ 0.35 wt%, Mn ⁇ 0.35 wt%, Cr ⁇ 0.25 wt%, Ti ⁇ 0.25 wt%, and the balance is Al.
  • the chemical composition of the Zn, Si and Cu contents are in the range of 0.3 to 3.9 wt% of Zn, 0.4 to 1.0 wt% of Si, and 0 to 0.9 wt% of Cu.
  • the chemical composition Mg, Si has a mass ratio of Mg/Si of 1.0 to 2.0; the mass percentage of Fe and Mn is: Fe ⁇ 0.2 wt%, and Mn ⁇ 0.15 wt%.
  • a second object of the present invention is to provide a method for preparing a novel aluminum alloy material for an automobile body outer panel having high baking paint hardening property, and the preparation method comprises the following steps:
  • Step one smelting casting
  • Step three hot rolling deformation
  • Step four intermediate annealing
  • Step five cold rolling deformation
  • Step 7 Classification and quenching treatment
  • Step 8 Pre-aging treatment.
  • the two-stage homogenization of the second step is specifically: the alloy sample after the smelting and casting is started to be heated from room temperature to 460 to 485 ° C for 2 to 5 hours at a temperature increase rate of 25 to 45 ° C / h, and then to 25 ⁇ 45 °C / h continue to raise the temperature to 545 ⁇ 555 ° C for 16 ⁇ 22h, and finally at 25 ⁇ 45 ° C / h cooling rate with the furnace to cool below 100 ° C when taken out.
  • the hot rolling deformation condition of the third step is specifically: the rolling temperature is 530-550 ° C, the pass reduction is 4% to 35%, the total hot rolling deformation is >90%, and the finishing rolling temperature is ⁇ 300. °C;
  • the intermediate annealing in the fourth step is specifically: heating the alloy sample after hot rolling to a temperature of 350 ° C to 450 ° C at a heating rate of 30 ° C / h to 1200 ° C / h, holding the intermediate annealing for 1 to 3 h, and then air cooling;
  • the total cold rolling deformation of the cold rolling deformation in the step 5 is between 60% and 80%, and the pass reduction is between 20% and 35%.
  • the solution treatment of the step 6 is specifically: performing a solution treatment of 545 to 555 ° C / 1-6 min in a salt bath furnace.
  • the step quenching treatment in the step 7 is to cool the alloy sample after the solution treatment from the solution treatment temperature to a temperature decrease rate of 30 to 1900 ° C/s to 250 to 320 ° C, and then to 1 to 70 ° C.
  • the cooling rate of /s is lowered to 150 to 200 ° C, and finally cooled to room temperature at a rate of 30 to 0.17 ° C / s.
  • the pre-aging treatment of the step 8 is that the alloy sample after the quenching and quenching is transferred to the 70-130 ° C pre-aging furnace for pre-aging treatment for 10 to 16 hours in 2 to 5 minutes, and is placed at room temperature for 14 days. Or the combination of hardening after quenching The gold sample was transferred to a 60-140 ° C pre-aging furnace within 2 to 5 minutes, and the temperature was lowered to 20 to 40 ° C at a cooling rate of 1 to 16 ° C / h, and left at room temperature for 14 days.
  • a third object of the present invention is to provide a method for preparing an automobile part, characterized in that after preparing a new aluminum alloy material by the above-mentioned preparation method, the following steps are performed:
  • Step IX stamping and forming
  • Step 10 brushing and baking hardening treatment.
  • the present invention has the following advantages: the novel aluminum alloy of the present invention can fully utilize the strong interaction between Mg-Si and Mg-Zn in the matrix, and is controlled by a suitable processing and heat treatment process to make the alloy In the process of simulating baking varnish, the plate can realize rapid aging precipitation of various strengthening phases, and then the multi-phase synergistic strengthening makes the increase of alloy lacquer hardening greatly improved.
  • the alloy of the invention is very suitable for the processing and production of the aluminum alloy for the outer body of the automobile body, and the production of the aluminum alloy plate for the other parts of the body parts which have high requirements for the hardening of the baking paint, and is also suitable for the aging of the aluminum alloy. Other technical industries with higher requirements for corresponding speeds are listed.
  • Figure 1 is a flow chart showing the preparation process of the inventive alloy.
  • Fig. 2 is a schematic diagram showing the change of hardness of several solid solution quenched alloys during natural aging.
  • Figure 3 is a DSC plot of several T4 alloys.
  • Fig. 4 is a schematic diagram showing the change of hardness of several T4 alloys during 170 °C aging.
  • Fig. 5 is a schematic diagram showing the change of hardness of several T4 alloys during aging at 185 °C.
  • Fig. 6 is a schematic diagram showing the change of hardness of several T4P isothermal pre-aged alloys during natural aging.
  • Figure 7 is a DSC plot of several T4P isothermal pre-aged alloys.
  • Fig. 8 is a TEM diagram of the alloy of the 5# alloy at room temperature at a temperature of 10 ° C / min to 250 ° C.
  • Fig. 9 is a TEM diagram of the isothermal T4P state 7# alloy when it is heated from room temperature to 10 ° C / min to 250 ° C.
  • Fig. 10 is a schematic diagram showing the change of hardness of several T4P isothermal pre-aged alloys during 185 °C artificial aging.
  • the raw materials were respectively 99.9 wt% of high purity aluminum, industrial pure Mg, industrial pure Zn, intermediate alloy Al-20 wt% Si, Al-50 wt% Cu, Al-20 wt% Fe, Al-10 wt% Mn, and the like.
  • the specific smelting process in the resistance furnace is to firstly pure aluminum Add hydrazine, set the furnace temperature to 850 ° C, add pure Al-20wt%Si, Al-50wt%Cu, Al-20wt%Fe, Al-10wt%Mn intermediate alloy after melting of pure aluminum, and add cover agent (50wt %NaCl+50wt%KCl); continue to heat the melt, after the intermediate alloy melts, the melt temperature reaches 750 °C, stir it to make the solute elements evenly mixed, then set the furnace temperature to cool the melt after holding at 750 °C for 30 min.
  • cover agent 50wt %NaCl+50wt%KCl
  • Table 1 shows the chemical composition of the alloy of the invention (mass percentage, wt%)
  • the invention ingot is homogenized in a circulating air furnace, and the treatment process is as follows: the alloy ingot is placed in a circulating air furnace, the power is turned on, and the temperature is started at a heating rate of 20 to 50 ° C / h until the temperature reaches 450 to 490. °C for 2 ⁇ 6h, and then continue to raise the temperature to 540 ⁇ 560 ° C for 16 ⁇ 25h at 20 ⁇ 50 ° C / h, and finally take the sample at 20 ⁇ 50 ° C / h cooling rate when the furnace is cooled to 100 ° C; Subsequently, the homogenized ingot is subjected to hot rolling deformation ⁇ intermediate annealing ⁇ cold rolling deformation.
  • a part of the sample is taken directly from the homogenized state, a part is taken from the cold rolling state, and then the cut block test is taken.
  • the sample was placed in a salt bath furnace at 540 to 560 ° C for a solution treatment for 1 to 7 minutes; then, a step quenching treatment was carried out to cool the alloy sample after the solution treatment from the solution treatment temperature to room temperature.
  • the pre-aging, pre-deformation, simulated paint hardening treatment is carried out on the graded quenched samples, and the DSC analysis, microhardness and tensile properties of different alloy samples are analyzed to analyze the precipitation behavior of the alloy and the change of the hardening of the paint. .
  • the specific implementation is as follows:
  • alloys 1#, 2#, 3#, 5#, 6#, 7#, 8#, 9#, and 10# are smelted and cast, they are homogenized, and the treatment process is: 25 to 45
  • the temperature rise rate of °C/h starts to increase. After the temperature reaches 460 ⁇ 485°C, the temperature is kept for 2 ⁇ 5h, and then the temperature is raised to 545 ⁇ 555°C for 16 ⁇ 22h at 25 ⁇ 45°C/h, and then 25 ⁇ 45°C/h.
  • the temperature drop rate was taken as the furnace was cooled to 100 ° C. Then, the sample is directly cut out on the homogenized block material and placed in a 545-555 ° C salt bath furnace for 1 to 6 minutes of solution treatment.
  • the alloy sample after solution treatment is subjected to fractional quenching treatment, and the temperature is lowered from the solution treatment temperature to a temperature drop rate of 30 to 1900 ° C/s to 250 to 320 ° C, and then the temperature is lowered at a temperature drop rate of 1 to 70 ° C / s to 150 ⁇ 200 ° C, and finally cooled to room temperature at a rate of 30 ° C / s ⁇ 0.17 ° C / s, and then placed in natural aging conditions for 14 days, compare the hardness changes of various alloys during natural aging (see Figure 2) Shown). In addition, DSC analysis was carried out on 14-day natural aging 5#, 6# and 7# samples.
  • the specific implementation scheme was: cutting a disk with a diameter of 3 mm ⁇ 1 mm and a mass of about 15 mg, using a differential scanning calorimeter Q2000 (DSC) Differential thermal analysis was carried out using high purity Al as a standard and heating from 20 ° C to 400 ° C at a heating rate of 10 ° C / min. Based on this, the difference in aging precipitation behavior of alloys with different compositions was further analyzed (see Figure 3 for details).
  • alloys 1#, 2#, 3#, 5#, 6#, 7#, 8#, 9#, and 10# are smelted and cast, they are homogenized, and the treatment process is: 25 to 45
  • the temperature rise rate of °C/h starts to increase. After the temperature reaches 460 ⁇ 485°C, the temperature is kept for 2 ⁇ 5h, and then the temperature is raised to 545 ⁇ 555°C for 16 ⁇ 22h at 25 ⁇ 45°C/h, and then 25 ⁇ 45°C/h.
  • the temperature drop rate was taken as the furnace was cooled to 100 ° C. Then, the sample is directly cut out on the homogenized block material and placed in a 545-555 ° C salt bath furnace for 1 to 6 minutes of solution treatment.
  • the alloy sample after solution treatment is cooled from the solution treatment temperature to a temperature drop rate of 30 to 1900 ° C / s to 250 to 320 ° C, and then cooled to 150 to 200 ° C at a temperature reduction rate of 1 to 70 ° C / s. Finally, the temperature was lowered to room temperature at a rate of 30 ° C / s to 0.17 ° C / s.
  • the multi-stage quenched samples were placed at room temperature for 14 days (T4 state), and then subjected to artificial aging at 170 ° C and 185 ° C for different time to analyze the difference in aging precipitation behavior of the alloy (see Figure 4 and Figure 5 for details). ).
  • alloys 1#, 2#, 3#, 5#, 6#, 7#, 8#, 9#, and 10# are smelted and cast, they are homogenized, and the treatment process is: 25 to 45
  • the temperature rise rate of °C/h starts to increase. After the temperature reaches 460 ⁇ 485°C, the temperature is kept for 2 ⁇ 5h, and then the temperature is raised to 545 ⁇ 555°C for 16 ⁇ 22h at 25 ⁇ 45°C/h, and then 25 ⁇ 45°C/h.
  • the temperature drop rate was taken as the furnace was cooled to 100 ° C. Then, the sample is directly cut out on the homogenized block material and placed in a 545-555 ° C salt bath furnace for 1 to 6 minutes of solution treatment.
  • the alloy sample after solution treatment is cooled from the solution treatment temperature to a temperature drop rate of 30 to 1900 ° C / s to 250 to 320 ° C, and then cooled to 150 to 200 ° C at a temperature reduction rate of 1 to 70 ° C / s. Finally, The temperature was lowered to room temperature at a rate of 30 ° C / s to 0.17 ° C / s. Subsequently, the quenched sample is transferred to an isothermal pre-aging furnace at 70-130 ° C for pre-aging treatment for 10-16 h in 2 to 5 min, and placed at room temperature for 14 days (T4P state) to compare the natural aging of various alloys.
  • alloys 1#, 2#, 3#, 4#, 5#, 6#, 7#, 8#, 9#, and 10# are smelted and cast, they are homogenized, and the treatment process is as follows: 25 to 45 ° C / h heating rate began to heat up, until the temperature reached 460 ⁇ 485 ° C insulation 2 ⁇ 5h, and then continue to 25 ⁇ 45 ° C / h to 545 ⁇ 555 ° C insulation 16 ⁇ 22h, then 25 ⁇ 45 ° C The cooling rate of /h was taken out when the furnace was cooled to 100 °C.
  • the sample is directly cut out on the homogenized block material and placed in a 545-555 ° C salt bath furnace for 1 to 6 minutes of solution treatment.
  • the alloy sample after solution treatment is cooled from the solution treatment temperature to a temperature drop rate of 30 to 1900 ° C / s to 250 to 320 ° C, and then cooled to 150 to 200 ° C at a temperature reduction rate of 1 to 70 ° C / s.
  • the temperature was lowered to room temperature at a rate of 30 ° C / s to 0.17 ° C / s.
  • the multi-stage quenched sample was transferred to a 70-130 ° C isothermal pre-aging furnace for pre-aging treatment for 10-16 h in 2 to 5 min, and placed at room temperature for 14 days (T4P state), and then subjected to 185 ° C.
  • the aging precipitation behavior of the alloy was analyzed by artificial aging at different times (see Figure 8 for details).
  • the homogenization treatment is carried out, and the treatment process is as follows: the temperature rise starts at a heating rate of 25 to 45 ° C / h, and the temperature is maintained at 460 to 485 ° C for 2 to 5 hours, and then The temperature was further increased at 25 to 45 ° C / h to 545 ⁇ 555 ° C for 16 ⁇ 22h, and then the sample was taken out at a cooling rate of 25 ⁇ 45 ° C / h with the furnace down to 100 ° C.
  • the sample is directly cut out on the homogenized block material and placed in a salt bath furnace at 545-555 ° C for 1 to 6 minutes for solution treatment (ie, 1-6 min in a salt bath furnace at 545-555 ° C). Solution treatment).
  • the alloy sample after solution treatment is cooled from the solution treatment temperature to a temperature drop rate of 30 to 1900 ° C / s to 250 to 320 ° C, and then cooled to 150 to 200 ° C at a temperature reduction rate of 1 to 70 ° C / s. Finally, the temperature was lowered to room temperature at a rate of 30 ° C / s to 0.17 ° C / s.
  • the multi-stage quenched alloy sample is transferred to a 60-140 ° C pre-aging furnace within 2 to 5 minutes, and the temperature is lowered to 20-40 ° C at a cooling rate of 1-16 ° C / h, and left at room temperature for 14 days, then The aging precipitation behavior of the alloy was analyzed by 185 ° C / 20 min artificial aging (see Table 2 for details).
  • the homogenization treatment is carried out, and the treatment process is as follows: the temperature rise starts at a heating rate of 25 to 45 ° C / h, and the temperature is maintained at 460 to 485 ° C for 2 to 5 hours, and then Continue to heat up at 25 ⁇ 45 ° C / h The temperature is maintained at 545-555 ° C for 16-22 h, and then the sample is taken out at a cooling rate of 25-45 ° C / h with the furnace cooling to 100 ° C.
  • the ingot is cut into a face and reheated to 530-550 °C for hot rolling, the pass reduction is 4% to 35%, the total hot rolling deformation is >90%, and the final rolling temperature is ⁇ 300 °C;
  • the hot rolled sheet is heated to 350-450 ° C at a heating rate of 30 ° C / h to 1200 ° C / h for 1 ⁇ 3 h annealing, and then cold rolled to 1 mm thick, the pass reduction is 20 ⁇ 35%, the total deformation is 60-80%; then directly cut the sample on the cold-rolled sheet placed in a 545-555 °C salt bath furnace for 1 ⁇ 6min solution treatment.
  • the alloy sample after solution treatment is cooled from the solution treatment temperature to a temperature drop rate of 30 to 1900 ° C / s to 250 to 320 ° C, and then cooled to 150 to 200 ° C at a temperature reduction rate of 1 to 70 ° C / s. Finally, the temperature was lowered to room temperature at a rate of 30 ° C / s to 0.17 ° C / s. Subsequently, the multi-stage quenched sample was transferred to an isothermal pre-aging furnace at 70-130 ° C for 2 to 16 hours for isothermal pre-aging treatment for 10 to 16 hours, and left at room temperature for 14 days (T4P state).
  • Stamping, painting and baking hardening are the real production steps of typical automotive parts (such as door panels). Since the deformation of typical automotive parts during stamping and forming process is mostly 2 to 5%, the surface must be first formed after stamping. Brushing, baking after painting, the baking process is generally 185 ° C / 20 min, the alloy strength will increase during the baking process.
  • the pre-stretching of the isothermal pre-aged samples can be carried out to simulate the stamping forming process of typical parts, and then the simulated baking treatment of 185 ° C / 20 min is performed.
  • the paint hardening increment of the alloy sheet is analyzed (see Table 3 for details).
  • the treatment process is as follows: the temperature rise starts at a temperature increase rate of 25 to 45 ° C / h, and the temperature is maintained at 460 to 485 ° C for 2 to 5 hours, and then The temperature is further increased at 25 to 45 ° C / h to 545 ⁇ 555 ° C for 16 ⁇ 22h, and then the sample is taken off at a cooling rate of 25 ⁇ 45 ° C / h with the furnace to 100 ° C.
  • the ingot is cut into a face and reheated to 530-550 °C for hot rolling, the pass reduction is 4% to 35%, the total hot rolling deformation is >90%, and the final rolling temperature is ⁇ 300 °C;
  • the hot rolled sheet is heated to 350-450 ° C at a heating rate of 30 ° C / h to 1200 ° C / h for 1 ⁇ 3 h annealing, and then cold rolled to 1 mm thick, the pass reduction is 20 ⁇ 35%, the total deformation is 60-80%; then directly cut the sample on the cold-rolled sheet placed in a 545-555 °C salt bath furnace for 1 ⁇ 6min solution treatment.
  • the alloy sample after solution treatment is cooled from the solution treatment temperature to a temperature drop rate of 30 to 1900 ° C / s to 250 to 320 ° C, and then cooled to 150 to 200 ° C at a temperature reduction rate of 1 to 70 ° C / s. Finally, the temperature was lowered to room temperature at a rate of 30 ° C / s to 0.17 ° C / s.
  • the above-mentioned multi-stage quenched alloy sample is transferred to a 60-140 ° C pre-aging furnace in 2 to 5 minutes, and the temperature is lowered to 20 to 40 ° C at a cooling rate of 1 to 16 ° C / h, and left at room temperature for 14 days.
  • Pre-stretching of the pre-aging samples was carried out by 2% to 5%, and finally, the 185 ° C / 20 min simulated baking varnish treatment was carried out to analyze the lacquer hardening increment of the alloy sheets. (See Table 4 for details).
  • the alloy composition, microstructure and heat treatment process all have an effect on the precipitation behavior of the Al-Mg-Si alloy, in order to eliminate the influence of the deformation structure formed during hot working and cold working on the precipitation behavior of the alloy, it is better to ensure
  • the new aluminum alloy composition with high paint hardening performance is optimized, and the alloys used in different heat treatment states are taken from the ingot sample after homogenization treatment.
  • the hardness changes of the aluminum alloys treated in the different heat treatment processes of Examples 1 to 5, the corresponding DSC curves and the TEM structure are shown in Figures 2-10. It can be seen from Fig.
  • the sample after solution hardening will increase in hardness with the aging time during the natural aging process (for the increase of the strength of the automobile sheet, the alloy will be lowered. Sheet forming performance). Although some alloys have a small increase in hardness, the increase in strength indicates that a large number of coarse solute clusters are formed (as shown by the DSC back-melting peak in Figure 3). These solute clusters can significantly reduce the subsequent high-temperature artificial aging precipitation rate of the alloy (for automobiles). The plate will significantly reduce the hardening increase during the baking process, and the above two deterioration effects caused by the increase in strength during the natural aging process are strictly controlled in the production process of the automobile sheet).
  • the T4 alloys were subjected to artificial aging at 170 ° C and 185 ° C for different times. It can be seen from Fig. 4 and Fig. 5 that the T4 alloy not only has a relatively slow age hardening rate during artificial aging, but also the most critical. The hardness of some alloys appeared after 20min aging (as shown in Table 2). Of course, some alloys (such as alloys with a certain amount of Zn added) have a higher hardness. From the DSC curve shown in Fig. 3, it can be seen that the addition of a certain amount of elemental Zn enables the precipitation peak of the ⁇ ′′ phase having a peak temperature of about 250 ° C to move toward the low temperature direction (as shown in Fig. 3).
  • the type of aluminum alloy proposes a pre-aging process suitable for the alloy to improve the room temperature stability and the hardening of the paint.
  • T4 state 5# alloy and T4P state 7# alloy were raised from room temperature to 250 ° C at 10 ° C / min (precipitation of precipitated phase during simulated DSC heating). It can be seen from Fig. 8 and Fig. 9 that there are two different types of precipitated phases in the matrix of the two alloys.
  • the number of fine punctiform precipitates in the T4P state 7# alloy increased from room temperature to 250 °C, and the results showed that the new aluminum alloy can be optimized by composition and heat treatment process.
  • the T4P isothermal pre-age alloy is further subjected to high temperature artificial aging (Example 4), it can be seen from Fig. 10 that the aging precipitation rate of all the alloys is higher than that of the T4 alloy, and some alloys have hardness. Double peak phenomenon, which is mainly due to the precipitation of two or more strengthening phases.
  • the hardness of the alloy increased significantly after aging at 185 ° C / 20 min for a short period of time, and the maximum hardness increased by 25 HV (as shown in Figure 10 and Table 2).
  • the hardness of the alloy also increased significantly after aging at 185 ° C / 20 min (see Table 2).
  • the results of the above studies indicate that the developed alloys may exhibit very good paint hardening increments if used in the production of automotive sheets.
  • the new aluminum alloy developed can exhibit multi-phase synergistic precipitation and multi-phase synergistic strengthening, and has better rapid aging response characteristics, it is very suitable for the manufacture of aluminum alloy for automobile body outer panel, therefore, for 4
  • the # and 7# alloys were subjected to hot working (hot rolling deformation), cold working deformation (cold rolling deformation), and multi-stage heat treatment (solution treatment, stage quenching treatment, pre-aging treatment) (as in Example 6 and Example 7).
  • the alloys of the invention were subjected to the isothermal and temperature-lowering pre-aging treatments in the two examples, and then exhibited excellent emulsion hardening increments after subsequent 185 ° C / 20 min simulated baking treatment (as shown in Tables 3 and 4). .
  • the simulated paint hardening increment of this component alloy sheet can reach 144 and 158 MPa. This paint hardening increase is much higher than the current commercially available AA6016 and AA6111 alloy paint hardening increments.
  • the invention is optimized by composition design, processing and heat treatment process, and the interaction between the main alloying elements Mg, Si, Cu and Zn in the novel aluminum alloy is well regulated, so that the alloy is During the aging process, multiphase synergistic precipitation can be exhibited to enable the alloy matrix to obtain multiphase synergistic strengthening, and finally the developed aluminum alloy is pre-aged. After treatment, not only the strength is low, but also the performance stability is good, which is very advantageous for stamping and forming different shapes of automobile parts.
  • the Al-Mg-Si alloy with a conventional automobile body outer panel has an even more excellent paint hardening increment.
  • the alloy and process of the invention are not only very suitable for the manufacture of aluminum alloy for automobile exterior panels, thereby accelerating the process of lightweighting of automobiles, and also have certain development, processing and application of fast aging-responsive aluminum alloys for other fields.
  • the guiding significance is worthy of the attention of automobile manufacturers and aluminum alloy processing enterprises to pay attention to the invention alloy and related preparation process, so that it can be promoted and applied in this field as soon as possible.

Abstract

La présente invention concerne un nouveau matériau d'alliage d'aluminium utilisé dans une carrosserie d'automobile présentant une propriété de durcissement par cuisson à température élevée, les composants du matériau comprenant : 0,05 à 4,0 % en masse de Zn, 0,5 à 1,5 % en masse de Mg, 0,2 à 1,2 % en masse de Si, 0 à 1,0 % en masse de Cu, Fe ≤ 0,35 % en masse, Mn ≤ 0,35 % en masse, Cr ≤ 0,25 % en masse, Ti ≤ 0,25 % en masse, et le reste étant constitué de Al. Le procédé de préparation de celui-ci comprend : la fusion et la coulée, l'homogénéisation en deux étapes, la déformation par laminage à chaud, le recuit intermédiaire, la déformation par laminage à froid, le traitement dans une solution, le traitement par trempe graduelle, et le traitement de pré-vieillissement.
PCT/CN2014/092726 2014-02-25 2014-12-01 Alliage d'aluminium durci par cuisson à température élevée pour carrosserie d'automobile et procédé de préparation de celui-ci WO2015127805A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN2014100648921 2014-02-25
CN201410064892.1A CN103757507B (zh) 2014-02-25 2014-02-25 一种汽车车身外板用高烤漆硬化铝合金材料及其制备方法

Publications (1)

Publication Number Publication Date
WO2015127805A1 true WO2015127805A1 (fr) 2015-09-03

Family

ID=50524821

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2014/092726 WO2015127805A1 (fr) 2014-02-25 2014-12-01 Alliage d'aluminium durci par cuisson à température élevée pour carrosserie d'automobile et procédé de préparation de celui-ci

Country Status (2)

Country Link
CN (1) CN103757507B (fr)
WO (1) WO2015127805A1 (fr)

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105543741A (zh) * 2015-12-17 2016-05-04 西南铝业（集团）有限责任公司 一种铝合金的中间退火工艺及汽车覆盖件用铝合金
EP3486343A1 (fr) * 2017-11-16 2019-05-22 Amag Rolling GmbH Alliage d'aluminium durcissable
US10513766B2 (en) 2015-12-18 2019-12-24 Novelis Inc. High strength 6XXX aluminum alloys and methods of making the same
US10538834B2 (en) 2015-12-18 2020-01-21 Novelis Inc. High-strength 6XXX aluminum alloys and methods of making the same
CN112491217A (zh) * 2020-12-04 2021-03-12 无锡通伟电力设备有限公司 一种电动机用铝端环的加工方法
CN113215460A (zh) * 2021-04-16 2021-08-06 中南大学 一种低密度高强耐损伤铝锂合金热轧板材及其制备方法
CN114411002A (zh) * 2022-01-25 2022-04-29 西安交通大学 一种铝合金的制备方法
CN114807688A (zh) * 2022-04-13 2022-07-29 中铝瑞闽股份有限公司 一种具有高耐久性的汽车车身用6系铝合金板带材及其制备方法
CN115011848A (zh) * 2022-05-11 2022-09-06 北京理工大学 一种高纯铝合金导线及其制备方法
CN115094256A (zh) * 2022-06-23 2022-09-23 南京启智浦交科技开发有限公司 一种提高车身结构铝合金板材室温成形性能的梯度组织调控方法
CN115323203A (zh) * 2022-08-31 2022-11-11 南京工程学院 高强度汽车车身用Al-Mg-Si合金的Cu和Sn复合微合金化材料及制备工艺和应用
CN115652151A (zh) * 2022-12-14 2023-01-31 中铝材料应用研究院有限公司 一种适用于热冲压成形成性一体化工艺的6xxx系铝合金板材及其制备方法和应用
CN115874123A (zh) * 2021-09-28 2023-03-31 宝山钢铁股份有限公司 提高6016铝合金烤漆硬化增量的多级协同处理方法
US11932928B2 (en) 2018-05-15 2024-03-19 Novelis Inc. High strength 6xxx and 7xxx aluminum alloys and methods of making the same

Families Citing this family (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103789583B (zh) * 2014-01-22 2016-06-08 北京科技大学 快速时效响应型Al-Mg-Si-Cu-Zn系合金及其制备方法
CN103757507B (zh) * 2014-02-25 2016-04-27 北京科技大学 一种汽车车身外板用高烤漆硬化铝合金材料及其制备方法
CN104313413B (zh) * 2014-10-24 2016-08-24 北京科技大学 一种Al-Mg-Zn系合金及其合金板材的制备方法
CN104561681A (zh) * 2014-12-22 2015-04-29 河南明泰铝业股份有限公司 汽车车身用6016铝合金薄板及其生产方法
CN105181733A (zh) * 2015-08-06 2015-12-23 江苏安瑞达新材料有限公司 一种利用dsc模拟聚烯烃流延基膜退火处理的方法
CN105839036B (zh) * 2016-04-27 2017-10-27 贵州航天风华精密设备有限公司 一种铝镁合金的热处理方法
CN106191574B (zh) * 2016-08-25 2018-03-16 广西南南铝加工有限公司 一种6系铝合金及其预拉伸板材的制备工艺
CN106350713B (zh) * 2016-08-25 2018-07-20 广西南南铝加工有限公司 一种Al-Mg-Si合金及其板材的制备工艺
CN107385291B (zh) * 2017-06-22 2019-01-29 烟台南山学院 一种高性能Al-Zn-Mg-Cu-Zr-Ce-Ti合金及其制备工艺
CN107119216B (zh) * 2017-06-27 2019-04-05 中南大学 一种高强耐腐蚀铝合金及其制备方法
CN107699755B (zh) * 2017-09-28 2019-09-20 山东南山铝业股份有限公司 一种车身用铝合金及其制备方法
ES2955293T3 (es) * 2017-10-23 2023-11-29 Novelis Inc Aleaciones de aluminio de alta resistencia, altamente conformables y métodos para su fabricación
CN108239712A (zh) * 2018-03-04 2018-07-03 广西平果百矿高新铝业有限公司 一种航空用6082铝合金板材及其生产工艺
CN109468504A (zh) * 2018-11-21 2019-03-15 安徽鑫铂铝业股份有限公司 一种耐腐蚀汽车轻量化铝型材
CN112626429B (zh) * 2019-10-08 2022-10-21 有研工程技术研究院有限公司 一种提高6000系铝合金板材抗时效稳定性的方法
CN110592447A (zh) * 2019-10-17 2019-12-20 徐州一宁铝业科技有限公司 一种铝合金板的制造工艺及铝合金板
CN112195376A (zh) * 2020-09-11 2021-01-08 中铝材料应用研究院有限公司 一种高强度汽车车身用6xxx系铝合金板材及其制备方法
CN114277325B (zh) * 2020-09-27 2022-11-08 中国科学院金属研究所 提高Al-Mg-Si-Zn系铝合金或其复合材料时效硬化能力的热处理工艺
CN112522551B (zh) * 2020-11-04 2022-04-26 佛山科学技术学院 一种Ag微合金化快速时效响应的铝合金及其制备方法和应用
CN112522550B (zh) * 2020-11-04 2022-10-04 佛山科学技术学院 一种快速时效响应的铝合金及其制备方法和应用
CN112322947B (zh) * 2020-11-11 2021-09-07 西北工业大学 一种汽车用高强塑性Al-Mg-Si-Zn合金及其制备方法
CN114908305B (zh) * 2021-02-09 2023-04-11 宝山钢铁股份有限公司 一种提高6000系铝合金板带成形性的联合热处理方法及制造方法
CN115874122B (zh) * 2021-09-28 2024-04-05 宝山钢铁股份有限公司 提高6451铝合金烤漆硬化增量的低温预时效处理方法
CN113981281B (zh) * 2021-10-15 2022-08-09 华峰铝业有限公司 一种高强度快速时效铝合金及其制备方法
CN114058885B (zh) * 2021-11-16 2022-12-09 中铝材料应用研究院有限公司 6xxx系铝合金板材及其制备方法和焊接方法
CN114959386B (zh) * 2022-05-30 2022-11-15 中国第一汽车股份有限公司 快速时效响应的铝合金及其热处理工艺

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06272000A (ja) * 1993-03-16 1994-09-27 Sky Alum Co Ltd 成形性および焼付硬化性に優れたアルミニウム合金板の製造方法
WO2012059419A1 (fr) * 2010-11-05 2012-05-10 Aleris Aluminum Duffel Bvba Pièce automobile formée faite à partir d'un produit d'alliage d'aluminium et son procédé de fabrication
EP2581218A1 (fr) * 2012-09-12 2013-04-17 Aleris Aluminum Duffel BVBA Procédé de fabrication d'un composant structurel d'automobile de tôle d'alliage d'aluminium AA7xxx-série
CN103173661A (zh) * 2013-02-27 2013-06-26 北京科技大学 一种汽车车身用铝合金板材及其制备方法
CN103509980A (zh) * 2013-10-12 2014-01-15 北京科技大学 Al-Mg-Si-Cu-Zn系铝合金、其制备方法及其应用
CN103757507A (zh) * 2014-02-25 2014-04-30 北京科技大学 一种汽车车身外板用高烤漆硬化铝合金材料及其制备方法
CN103789583A (zh) * 2014-01-22 2014-05-14 北京科技大学 快速时效响应型Al-Mg-Si-Cu-Zn系合金及其制备方法
CN104018040A (zh) * 2014-06-23 2014-09-03 北京科技大学 一种汽车用高成形性铝合金材料及其制备方法

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0543974A (ja) * 1991-08-16 1993-02-23 Nkk Corp 焼付硬化性及びプレス成形性に優れたアルミニウム合金板及びその製造方法
AUPO084796A0 (en) * 1996-07-04 1996-07-25 Comalco Aluminium Limited 6xxx series aluminium alloy
CN101880801B (zh) * 2010-06-13 2012-07-18 东北大学 一种汽车车身用铝合金及其板材制造方法
CN101935785B (zh) * 2010-09-17 2012-03-28 中色科技股份有限公司 一种高成形性汽车车身板用铝合金
CN103255324B (zh) * 2013-04-19 2017-02-08 北京有色金属研究总院 一种适合于汽车车身板制造的铝合金材料及制备方法

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06272000A (ja) * 1993-03-16 1994-09-27 Sky Alum Co Ltd 成形性および焼付硬化性に優れたアルミニウム合金板の製造方法
WO2012059419A1 (fr) * 2010-11-05 2012-05-10 Aleris Aluminum Duffel Bvba Pièce automobile formée faite à partir d'un produit d'alliage d'aluminium et son procédé de fabrication
EP2581218A1 (fr) * 2012-09-12 2013-04-17 Aleris Aluminum Duffel BVBA Procédé de fabrication d'un composant structurel d'automobile de tôle d'alliage d'aluminium AA7xxx-série
CN103173661A (zh) * 2013-02-27 2013-06-26 北京科技大学 一种汽车车身用铝合金板材及其制备方法
CN103509980A (zh) * 2013-10-12 2014-01-15 北京科技大学 Al-Mg-Si-Cu-Zn系铝合金、其制备方法及其应用
CN103789583A (zh) * 2014-01-22 2014-05-14 北京科技大学 快速时效响应型Al-Mg-Si-Cu-Zn系合金及其制备方法
CN103757507A (zh) * 2014-02-25 2014-04-30 北京科技大学 一种汽车车身外板用高烤漆硬化铝合金材料及其制备方法
CN104018040A (zh) * 2014-06-23 2014-09-03 北京科技大学 一种汽车用高成形性铝合金材料及其制备方法

Cited By (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105543741A (zh) * 2015-12-17 2016-05-04 西南铝业（集团）有限责任公司 一种铝合金的中间退火工艺及汽车覆盖件用铝合金
US10513766B2 (en) 2015-12-18 2019-12-24 Novelis Inc. High strength 6XXX aluminum alloys and methods of making the same
US10538834B2 (en) 2015-12-18 2020-01-21 Novelis Inc. High-strength 6XXX aluminum alloys and methods of making the same
US11920229B2 (en) 2015-12-18 2024-03-05 Novelis Inc. High strength 6XXX aluminum alloys and methods of making the same
EP3486343A1 (fr) * 2017-11-16 2019-05-22 Amag Rolling GmbH Alliage d'aluminium durcissable
US11851736B2 (en) 2017-11-16 2023-12-26 Amag Rolling Gmbh Hardenable aluminum alloy
US11932928B2 (en) 2018-05-15 2024-03-19 Novelis Inc. High strength 6xxx and 7xxx aluminum alloys and methods of making the same
CN112491217A (zh) * 2020-12-04 2021-03-12 无锡通伟电力设备有限公司 一种电动机用铝端环的加工方法
CN112491217B (zh) * 2020-12-04 2023-10-24 无锡通伟电力设备有限公司 一种电动机用铝端环的加工方法
CN113215460A (zh) * 2021-04-16 2021-08-06 中南大学 一种低密度高强耐损伤铝锂合金热轧板材及其制备方法
CN115874123A (zh) * 2021-09-28 2023-03-31 宝山钢铁股份有限公司 提高6016铝合金烤漆硬化增量的多级协同处理方法
CN115874123B (zh) * 2021-09-28 2024-04-05 宝山钢铁股份有限公司 提高6016铝合金烤漆硬化增量的多级协同处理方法
CN114411002A (zh) * 2022-01-25 2022-04-29 西安交通大学 一种铝合金的制备方法
CN114807688B (zh) * 2022-04-13 2023-10-13 中铝瑞闽股份有限公司 一种具有高耐久性的汽车车身用6系铝合金板带材及其制备方法
CN114807688A (zh) * 2022-04-13 2022-07-29 中铝瑞闽股份有限公司 一种具有高耐久性的汽车车身用6系铝合金板带材及其制备方法
CN115011848A (zh) * 2022-05-11 2022-09-06 北京理工大学 一种高纯铝合金导线及其制备方法
CN115094256A (zh) * 2022-06-23 2022-09-23 南京启智浦交科技开发有限公司 一种提高车身结构铝合金板材室温成形性能的梯度组织调控方法
CN115323203A (zh) * 2022-08-31 2022-11-11 南京工程学院 高强度汽车车身用Al-Mg-Si合金的Cu和Sn复合微合金化材料及制备工艺和应用
CN115652151A (zh) * 2022-12-14 2023-01-31 中铝材料应用研究院有限公司 一种适用于热冲压成形成性一体化工艺的6xxx系铝合金板材及其制备方法和应用

Also Published As

Publication number Publication date
CN103757507A (zh) 2014-04-30
CN103757507B (zh) 2016-04-27

Similar Documents

Publication Publication Date Title
WO2015127805A1 (fr) Alliage d'aluminium durci par cuisson à température élevée pour carrosserie d'automobile et procédé de préparation de celui-ci
WO2015109893A1 (fr) Alliage de séries al-mg-si-cu-zn de type à réaction de viellissement rapide et son procédé de préparation
CA2907160C (fr) Materiau d'alliage d'aluminium convenant a la fabrication de panneaux de chassis d'automobile et methodes de production associees
WO2021008428A1 (fr) Alliage d'aluminium-lithium à haute résistance et son procédé de préparation
JP4964586B2 (ja) 高強度Ａｌ−Ｚｎ合金およびそのような合金製品の製造方法
CN106350716B (zh) 一种高强度外观件铝合金材料及其制备方法
CN100453671C (zh) 一种汽车用Al-Mg-Si-Cu合金及其加工工艺
CN103173661B (zh) 一种汽车车身用铝合金板材及其制备方法
CN111575548B (zh) 综合性能优异的6系铝合金汽车外板及其制备方法
CN108994267B (zh) 一种能够提升加工成形性与时效强化效果的6xxx系铝轧板制备方法
CN110629075A (zh) 一种高强度高延伸率铝合金板材及其制造方法
CN104018040A (zh) 一种汽车用高成形性铝合金材料及其制备方法
JP2013167004A (ja) 焼付け塗装硬化性に優れたアルミニウム合金板
CN112458344B (zh) 一种高强耐蚀的铝合金及其制备方法和应用
JP2008045192A (ja) 成形時のリジングマーク性に優れたアルミニウム合金板
CN104975207A (zh) 一种AlMgSi系铝合金材料、铝合金板及其制造方法
CN111074121B (zh) 铝合金及其制备方法
US10704128B2 (en) High-strength corrosion-resistant aluminum alloys and methods of making the same
CN103255323A (zh) 一种Al-Mg-Zn-Cu合金及其制备方法
CN110396628B (zh) 一种铝合金及其制备方法
CN112522552B (zh) 一种耐蚀的铝合金及其制备方法和应用
JP3845312B2 (ja) 成形加工用アルミニウム合金板およびその製造方法
CN112626384A (zh) 一种中强高塑性的铝合金及其制备方法和应用
CN112877554A (zh) 一种高强韧易焊耐蚀Al-Mg-Zn-Cu合金制备方法
TWI674324B (zh) 鋁錳合金之製造方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 14883653

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 14883653

Country of ref document: EP

Kind code of ref document: A1