CN104018040A - Automotive high-formability aluminum alloy material and preparation method thereof - Google Patents
Automotive high-formability aluminum alloy material and preparation method thereof Download PDFInfo
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Abstract
The invention provides an automotive high-formability aluminum alloy material and a preparation method thereof. The preparation method comprises the steps of selection of novel aluminum alloy components, alloy preparation and melting-casting, homogenization, hot rolling deformation, intermediate annealing or cold rolling deformation and intermediate annealing, intermediate annealing, solution treatment, quenching and multistage pre-ageing treatment. By using the double effects that a certain quantity of multi-scale particles can be formed among different solute elements in the alloy material and then oversize particles are stimulated, re-crystallized and nucleated while fine particles block the growth of the re-crystallized grains in the high-temperature heat treatment process, so that the structure of an alloy plate is formed by the fine and uniformly distributed re-crystallized grains, the anisotropy of the alloy plate is well controlled, and the stamping forming performance is relatively excellent. Meanwhile, the novel aluminum alloy with high formability and high baking varnish hardening increment is very suitable for manufacturing of automotive body outer plates, particularly manufacturing of parts having relatively high requirements for stamping formability and baking varnish hardening increment and having complex shapes.
Description
Technical field
The invention belongs to aluminium alloy technical field, relate to a kind of automobile high formability aluminum alloy materials and preparation method thereof, especially for automotive field vehicle-body outer panel with aluminium alloy to forming property and dent resistance can particular requirement and develop, before can ensureing aluminum alloy plate materials shaping, anisotropy is better controlled, and there is excellent stamping performance, and after being shaped showing excellent bake hardening characteristic in baking vanish process in short-term.
Background technology
Along with the continuous increase of automobile quantity, atmospheric pollution and climate condition constantly worsen, and countries in the world constantly strengthen consciousness energy-conservation, that reduce discharging.Therefore, how automobile lightweight and then the object that reaches energy-saving and emission-reduction have become the key issue that automotive field further develops.And aluminium alloy is owing to having advantages of numerous uniquenesses, it is the light-weighted critical material of young mobile.Comparatively speaking, 6xxx line aluminium alloy in several large series alloys (be Al ?Mg ?Si be associated gold) owing to thering is following features: heat-treatable strengthened, solidity to corrosion is good, weldability is good, be easy to surface colour and plasticity good, and what is more important this be associated gold generally to have higher bake hardening characteristic (be that molded component after mopping is again through paint baking, its intensity can obtain further lifting by a relatively large margin, and then make sheet alloy there is good anti-depression ability), all these advantages make this be associated the processing that gold is applicable to being applied to automobile body outer board very much, and there is the alloy of several trades mark to obtain widespread use at present, as AA6016, AA6111 and AA6022 etc.
Al ?Mg ?Si is associated to gold as in the research and application process of automobile body outer board, although find that this is associated gold utensil and has good stamping performance, r value generally can reach more than 0.55, still has certain gap compared with iron and steel.Therefore the stamping performance that, how further to improve this line aluminium alloy in the situation that ensureing alloy bake hardening better performances is its key point that can obtain widespread use more.Due to automobile exterior panel with Al ?Mg ?Si to be associated golden preparation process longer, the heat processing technique relating to is comparatively complicated.Therefore, along with the variation of alloying constituent and thermal process parameter, all can there is noticeable change in the texture component of sheet alloy and content, microstructure, and then cause the stamping performance of sheet alloy also can occur significantly to change.There are some researches show, if (diameter d >1 μ m) the oversize particle of some amount in alloy substrate, particle can occur deformation states alloy in high-temperature heat treatment process stimulates Recrystallization nucleation (being so-called PSN effect), cause particle to occur that a large amount of Recrystallizations, the appearance of these recrystal grains also can make the recrystallization texture of sheet alloy with rotation cubic texture Cube around
nDwith P texture be main, these texture components are comparatively favourable for improving the punching performance of sheet alloy.In addition, if consider the interior oversize particle that only exists of alloy substrate, tiny recrystal grain distribution can be very inhomogeneous so on the one hand, and the tiny recrystal grain being produced by PSN effect on the other hand is also easy to grow up in heat treatment process.Therefore, if can further introduce a certain amount of other alloying element or control heat processing technique the oversize particle and the nano level small and dispersed particle that make to exist in cold rolling state alloy substrate some amount in Composition Design process simultaneously, so cold rolling state sheet alloy necessarily can form a large amount of tiny recrystal grains and be not easy to grow up (in detail as shown in Figure 2 schematic diagram) in follow-up solution heat treatment process, finally make sheet alloy again through Pre-aging treatment can the while with stamping performance and the bake hardening performance of excellence.The present invention carries out new alloy Composition Design and preparation technology's exploitation according to this design philosophy.
Summary of the invention
The present invention, in order to overcome the deficiencies in the prior art, is associated the dissatisfactory problem of golden stamping performance for current automobile body outer board with Al ?Mg ?Si, develops a kind of novel aluminum alloy with excellent punching performance and higher bake hardening performance.This novel alloy makes full use of different solute elements interactions can form multiple dimensioned particle (oversize particle and fine particle etc.), these multiple dimensioned particles can remarkably influenced dislocation in hot procedure and the mode of motion of crystal boundary, and then in high-temperature heat treatment process, bring into play oversize particle to stimulate Recrystallization nucleation (PSN effect) and fine particle hinders the recrystal grain dual function mode of growing up simultaneously, finally make the tissue of sheet alloy before stamping be formed by tiny equally distributed recrystal grain.This tissue signature not only can ensure that sheet alloy anisotropy obtains fine control, and can ensure that the stamping performance of sheet alloy is comparatively excellent.In addition, the outstanding contributions of heterogeneous strengthening in the time of design of alloy, are taken into full account, can ensure that sheet alloy has higher bake hardening increment after stamping, therefore, invention alloy Al ?Mg ?Si ?added a certain amount of element Zn on the basis of Cu alloy system, design well and optimize by the content to Mg, Si, Cu and Zn main alloying element and proportioning, not only stamping performance is comparatively excellent finally to make sheet alloy, and bake hardening increment has also obtained significantly lifting.This invention alloy is applicable to being applied to the manufacture of automobile body outer board, particularly to striking out the manufacture of the Irregular Shaped Parts that performance and bake hardening increment have higher requirements.
First the present invention selects the composition range of novel high formability and high bake hardening aluminium alloy by Composition Design and optimization, then prepare designed alloy by operations such as melting and castings and microstructure evolution process, forming property and Precipitation behavior are studied, the final corresponding preparation method who determines novel aluminum alloy composition range and the sheet alloy with high formability and high bake hardening performance.Concrete preparation technology is as follows: novel aluminum alloy becomes component selections → alloy preparation and melting and casting → ingot homogenization → hot rolling deformation → process annealing (or cold roller and deformed → process annealing) → cold roller and deformed → solid solution → quenching → preageing (as shown in Figure 1).
The first object of the present invention is to propose a kind of automobile body outer board novel aluminum alloy with high formability and high bake hardening performance, the chemical composition and the mass percentage content thereof that it is characterized in that this alloy are: Zn:0.02～4.2wt%, Mg:0.4～1.5wt%, Si:0.2～1.25wt%, Cu:0.05～1.0wt%, Fe≤0.65wt%, Mn:0.05～0.5wt%, Cr≤0.25wt%, Ti≤0.25wt%, B≤0.2wt%, surplus is Al.
Preferably, the Zn of its chemical composition, Si and Cu content range are respectively Zn:.025～4.0wt%, Si:0.35～1.0wt%, Cu:0.1～0.95wt%, the Mg/Si quality of its chemical composition Mg, Si is 1.0～2.3, Fe≤0.55wt% than scope, Mn:0.06～0.4wt%.
The second object of the present invention is to propose a kind of above-mentioned preparation method of aluminum alloy materials for the automobile body outer board of high formability that has, and described preparation method comprises the following steps:
Step 1, melting and casting: first fine aluminium is all added to crucible, furnace temperature is set in to 850 DEG C, after fine aluminium fusing, add Al ?20wt%Si, Al ?50wt%Cu, Al ?20wt%Fe, Al ?10wt%Mn master alloy, and add insulating covering agent (50wt%NaCl+50wt%KCl); Continue melt heating, treat master alloy fusing, after melt temperature reaches 750 DEG C, it is stirred solute element is mixed, then after 750 DEG C of insulation 30min, set furnace temperature and make melt cool to 710 DEG C, then in melt, add pure Zn and pure Mg, and fully stir it is thoroughly dissolved; Sampling analysis composition in the time that melt temperature reaches 730 DEG C again, if component metering value is lower than design load, suitably add a certain amount of master alloy according to scaling loss situation, if component metering value, higher than design load, is suitably added a certain amount of metal fine aluminium according to excessive value and diluted; Continue to skim, add after melt rises to 740 DEG C refining agent to carry out refinery by de-gassing; Then while melt temperature being down to approximately 720 DEG C, add Al ?5wt%Ti ?1wt%B grain-refining agent and carry out agitation as appropriate, finally after this temperature insulation 10min, melt being cast in the punching block of surrounding water-cooled;
Step 2, single-stage or twin-stage homogenizing: Zn content can directly adopt single-stage homogenizing lower than the aluminium alloy of 0.5wt%, be warmed up to 540～560 DEG C of insulation 15～30h by the alloy sample after melting and casting with 20～50 DEG C/h, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 20～50 DEG C/h with stove; And Zn content is in the time of 0.5wt%～4.0wt%, adopt twin-stage homogenization process, start to heat up with 20～50 DEG C/h temperature rise rate by the alloy sample after melting and casting, treat that temperature reaches 450～490 DEG C of insulation 2～6h, continue to be warmed up to 540～560 DEG C of insulation 15～30h with 20～50 DEG C/h again, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 20～50 DEG C/h with stove;
Step 3, hot rolling deformation: the sample that step 2 is taken out carries out hot rolling: start rolling temperature is at 520～555 DEG C, and reduction in pass is 4%～36%, hot rolling total deformation > 92%, finishing temperature obtains hot rolled plate lower than 300 DEG C;
Step 4, process annealing or cold roller and deformed+process annealing: the hot rolled plate that step 3 is obtained carries out process annealing or cold roller and deformed+process annealing, then directly take out and carry out air cooling and obtain annealed state sheet material;
Step 5, cold roller and deformed: the annealed state sheet material that described step 4 is obtained carries out cold roller and deformed, described cold roller and deformed cold rolling total deformation is between 50%～85%, and reduction in pass obtains cold rolled sheet between 10%～35%;
Step 6, solution treatment: the cold rolled sheet that step 5 is obtained carries out solution treatment: in 545～560 DEG C of heat treatment furnaces, carry out the solution treatment of 1～15min, sample temperature rise rate is greater than 100 DEG C/min;
Step 7, quench treatment: the alloy sample after solution treatment is obtained to quenching state sample from solid solution temperature with the rate of temperature fall cool to room temperature that is greater than 100 DEG C/s;
Step 8, multistage Pre-aging treatment: the quenching state sample that step 7 is obtained is transferred to the isothermal preageing that carries out 1～30min in 100 DEG C～130 DEG C isothermal preageing stoves in 2～5min, then transferred to the isothermal Pre-aging treatment that carries out 5～15h in the isothermal preageing stove of 60 DEG C～90 DEG C, finally it is placed to the aluminum alloy plate materials that obtains having high formability for 14 days in room temperature.
Process annealing in preferred described step 4 is all warmed up to 300～500 DEG C of anneal of carrying out 1～4h with the temperature rise rate of 20 DEG C/h～200 DEG C/min, then directly takes out and carries out air cooling.
In preferred described step 4 cold roller and deformed+process annealing is that cold roller and deformed reduction in pass is 10～35%, total deformation is 30～60%; Process annealing is all warmed up to 300～500 DEG C of anneal of carrying out 1～4h with the temperature rise rate of 20 DEG C/h～200 DEG C/min, then directly takes out and carries out air cooling.
Cold roller and deformed total deformation in preferred described step 5 is between 50%～75%, and reduction in pass is between 15%～30%.
Solution treatment in preferred described step 6: carry out the solution treatment of 2～8min in 545～555 DEG C of heat treatment furnaces, sample temperature rise rate is greater than 200 DEG C/min.
Quench treatment in preferred described step 7, obtains quenching state sample from solid solution temperature with the rate of temperature fall cool to room temperature that is greater than 200 DEG C/s by the alloy sample after solution treatment.
Multistage Pre-aging treatment in preferred described step 8, quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 1～15min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 6～13h in the isothermal preageing stove of 60 DEG C～80 DEG C, finally it is placed to the aluminum alloy plate materials that obtains having high formability for 14 days in room temperature.
By adopting above-mentioned technical scheme, the present invention has following superiority: automobile of the present invention can make full use of different scale particle in matrix to recrystal grain forming core, the compound interaction of growing up with high formability and high bake hardening novel aluminum alloy, thereby make the recrystallization crystal particle dimension after solution treatment tiny and even, be formed with and be beneficial to the rotation cubic texture or the P texture that improve stamping performance, or texture is weakened; In addition, invention alloy make full use of solute element Cu etc. to Mg ?Si and Mg ?Zn form the promoter action in solute atoms cluster or corresponding GP district, and make sheet alloy after Pre-aging treatment by suitable processing and thermal treatment process regulation and control, not only can show excellent stamping performance, and can show excellent bake hardening characteristic.Alloy of the present invention is applicable to being applied to processing and the production of automobile body outer board aluminium alloy very much, and stamping performance is had to the production and application of other component of particular requirement, be certainly also applicable to being applied to other technology industry that aluminium alloy forming property and aging response speed are had higher requirements.
Brief description of the drawings
Fig. 1 is alloy preparation technology schema of the present invention;
Fig. 2 different scale particle stimulates Recrystallization nucleation and (b) the lower aluminium alloy of (c) solute element concentration of growth process model diagram (a), (d) (e) (f) higher aluminium alloy of solute element concentration;
The TEM microstructure of the cold rolling state of 5# alloy 1mm in Fig. 3 embodiment 5;
Fig. 4 a is 5# alloy solid solution quenching state alloy grain size schematic diagram in embodiment 5;
Fig. 4 b is that the EBSD of 5# alloy solid solution quenching state alloy grain orientation in embodiment 5 analyzes schematic diagram;
6# alloy solid solution quenching state alloy grain size schematic diagram in Fig. 5 a embodiment 6;
In Fig. 5 b embodiment 6, the EBSD of 6# alloy solid solution quenching state alloy grain orientation analyzes schematic diagram.
Embodiment
Below in conjunction with specific embodiments, the present invention is further supplemented and described.
Fig. 1 is alloy preparation technology schema of the present invention; Preparation technology comprises the steps: as shown in the figure
Starting material adopt respectively 99.9wt% rafifinal, technical pure Mg, technical pure Zn, master alloy Al ?20wt%Si, Al ?50wt%Cu, Al ?20wt%Fe, Al ?10wt%Mn etc.Concrete fusion process in resistance furnace is, first fine aluminium is all added to crucible, furnace temperature is set in to 850 DEG C, after fine aluminium fusing, add Al ?20wt%Si, Al ?50wt%Cu, Al ?20wt%Fe, Al ?10wt%Mn master alloy, and add insulating covering agent (50wt%NaCl+50wt%KCl); Continue melt heating, treat master alloy fusing, after melt temperature reaches 750 DEG C, it is stirred solute element is mixed, then after 750 DEG C of insulation 30min, set furnace temperature and make melt cool to 710 DEG C, then in melt, add pure Zn and pure Mg, and fully stir it is thoroughly dissolved; Sampling analysis composition in the time that melt temperature reaches 730 DEG C again, if component metering value is lower than design load, suitably add a certain amount of master alloy according to scaling loss situation, if component metering value, higher than design load, is suitably added a certain amount of metal fine aluminium according to excessive value and diluted; Continue to skim, add after melt rises to 740 DEG C refining agent to carry out refinery by de-gassing; Then while melt temperature being down to approximately 720 DEG C, add Al ?5wt%Ti ?1wt%B grain-refining agent and carry out agitation as appropriate, finally after this temperature insulation 10min, melt being cast in the punching block of surrounding water-cooled.Carry out an invention the specific chemical composition of alloy in table 1.
Table 1 alloy composition (mass percent, wt%) that carries out an invention
| ? | Mg | Si | Cu | Fe | Mn | Zn | Cr | Ti | B | Al |
| 1# | 0.9 | 0.5 | 0.2 | 0.0 | 0.1 | 0.03 | ≤0.2wt％ | ≤0.01wt％ | ≤0.01wt％ | Surplus |
| 2# | 0.9 | 0.5 | 0.2 | 0.0 | 0.1 | 3.0 | ≤0.2wt％ | ≤0.01wt％ | ≤0.01wt％ | Surplus |
| 3# | 0.9 | 0.6 | 0.2 | 0.2 | 0.15 | 0.03 | ≤0.2wt％ | ≤0.01wt％ | ≤0.01wt％ | Surplus |
| 4# | 0.9 | 0.6 | 0.2 | 0.2 | 0.15 | 3.0 | ≤0.2wt％ | ≤0.01wt％ | ≤0.01wt％ | Surplus |
| 5# | 0.9 | 0.8 | 0.2 | 0.5 | 0.3 | 0.03 | ≤0.2wt％ | ≤0.01wt％ | ≤0.01wt％ | Surplus |
| 6# | 0.9 | 0.8 | 0.2 | 0.5 | 0.3 | 3.0 | ≤0.2wt％ | ≤0.01wt％ | ≤0.01wt％ | Surplus |
Invention alloy cast ingot carries out homogenizing processing in recirculated air stove, treatment process is: Zn content can directly adopt single-stage homogenizing lower than the aluminium alloy of 0.5wt%, continue to be warmed up to 540～560 DEG C of insulation 15～30h by the alloy sample after melting and casting with 20～50 DEG C/h, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 20～50 DEG C/h with stove, and Zn content is in the time of 0.5wt%～4.0wt%, adopt twin-stage homogenization process, start to heat up with 20～50 DEG C/h temperature rise rate by the alloy sample after melting and casting, treat that temperature reaches 450～490 DEG C of insulation 2～6h, continue to be warmed up to 540～560 DEG C of insulation 15～30h with 20～50 DEG C/h again, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 20～50 DEG C/h with stove, subsequently homogenizing state ingot casting is carried out to hot rolling deformation → process annealing (or cold roller and deformed+process annealing) → cold roller and deformed, then the sheet coupon cutting is put into 545～560 DEG C of heat treatment furnaces and carried out the solution treatment of 2～8min, and it is carried out to quench treatment, subsequently the sample after quenching is carried out to multistage Pre-aging treatment, finally preageing state sheet alloy is carried out to stamping performance and bake hardening performance measurement, and typicalness alloy microscopic structure characterizes.Concrete embodiment is as follows:
Embodiment 1
Carry out an invention alloy 1# after melting and casting, it is carried out to homogenizing processing, treatment process is: be warmed up to 540～560 DEG C of insulation 16h with 45 DEG C/h temperature rise rate, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 45 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; Sheet material after hot rolling is warmed up to 300～500 DEG C of anneal of carrying out 1.5h with the temperature rise rate of 40 DEG C/h, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 3min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 2min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 12h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 2 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that then it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 4 below) of sheet alloy.
Embodiment 2
Carry out an invention alloy 2# after melting and casting, it is carried out to homogenizing processing, treatment process is: start to heat up with 25 DEG C/h temperature rise rate, treat that temperature reaches 450～490 DEG C of insulation 3h, continue to be warmed up to 540～560 DEG C of insulation 16h with 25 DEG C/h again, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 25 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; Sheet material after hot rolling is warmed up to 300～500 DEG C of anneal of carrying out 1.5h with the temperature rise rate of 40 DEG C/h, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 3min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 2min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 12h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 2 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that then it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 4 below) of sheet alloy.
Embodiment 3
Carry out an invention alloy 3# after melting and casting, it is carried out to homogenizing processing, treatment process is: begin to warm to 540～560 DEG C of insulation 22h with 45 DEG C/h temperature rise rate, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 45 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; Sheet material after hot rolling is warmed up to 300～500 DEG C of anneal of carrying out 2.5h with the temperature rise rate of 100 DEG C/h, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 5min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 5min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 9h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 2 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that then it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 4 below) of sheet alloy.
Embodiment 4
Carry out an invention alloy 4# after melting and casting, it is carried out to homogenizing processing, treatment process is: start to heat up with 25 DEG C/h temperature rise rate, treat that temperature reaches 450～490 DEG C of insulation 4h, continue to be warmed up to 540～560 DEG C of insulation 22h with 25 DEG C/h again, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 25 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; Sheet material after hot rolling is warmed up to 300～500 DEG C of anneal of carrying out 2.5h with the temperature rise rate of 100 DEG C/h, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 5min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 5min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 9h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 2 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that then it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 4 below) of sheet alloy.
Embodiment 5
Carry out an invention alloy 5# after melting and casting, it is carried out to homogenizing processing, treatment process is: begin to warm to 540～560 DEG C of insulation 29h with 45 DEG C/h temperature rise rate, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 45 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; Sheet material after hot rolling is warmed up to 300～500 DEG C of anneal of carrying out 3.5h with the temperature rise rate of 150 DEG C/min, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 7min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 10min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 7h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 2 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that finally it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 4 below) of sheet alloy, adopt TEM to carry out microstructure analysis (as shown in Figure 3) to the cold rolling state of 5# alloy simultaneously, and adopt EBSD to analyze grain-size and the texture distribution situation (as shown in Fig. 4 a and b) of 5# sheet alloy.
Embodiment 6
Carry out an invention alloy 6# after melting and casting, it is carried out to homogenizing processing, treatment process is: start to heat up with 25 DEG C/h temperature rise rate, treat that temperature reaches 450～490 DEG C of insulation 5h, continue to be warmed up to 540～560 DEG C of insulation 29h with 20～50 DEG C/h again, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 25 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; Sheet material after hot rolling is warmed up to 300～500 DEG C of anneal of carrying out 3.5h with the temperature rise rate of 150 DEG C/min, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 7min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 10min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 7h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 2 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that finally it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 4 below) of sheet alloy, adopts EBSD to analyze grain-size and the texture distribution situation (as shown in Fig. 5 a and b) of 6# sheet alloy simultaneously.
Embodiment 7
Carry out an invention alloy 1# after melting and casting, it is carried out to homogenizing processing, treatment process is: begin to warm to 540～560 DEG C of insulation 16h with 45 DEG C/h temperature rise rate, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 45 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; First hot-rolled sheet is carried out a certain amount of cold roller and deformed, reduction in pass is 10～35%, and total deformation is 30～60%; Then cold rolled sheet is warmed up to 300～500 DEG C of anneal of carrying out 1.5h with the temperature rise rate of 40 DEG C/h, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 3min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 2min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 12h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 3 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that then it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 5 below) of sheet alloy.
Embodiment 8
Carry out an invention alloy 2# after melting and casting, it is carried out to homogenizing processing, treatment process is: start to heat up with 25 DEG C/h temperature rise rate, treat that temperature reaches 450～490 DEG C of insulation 3h, continue to be warmed up to 540～560 DEG C of insulation 16h with 25 DEG C/h again, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 25 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; First hot-rolled sheet is carried out a certain amount of cold roller and deformed, reduction in pass is 10～35%, and total deformation is 30～60%; Then cold rolled sheet is warmed up to 300～500 DEG C of anneal of carrying out 1.5h with the temperature rise rate of 40 DEG C/h, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 3min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 2min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 12h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 3 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that then it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 5 below) of sheet alloy.
Embodiment 9
Carry out an invention alloy 3# after melting and casting, it is carried out to homogenizing processing, treatment process is: begin to warm to 540～560 DEG C of insulation 22h with 45 DEG C/h temperature rise rate, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 45 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; First hot-rolled sheet is carried out a certain amount of cold roller and deformed, reduction in pass is 10～35%, and total deformation is 30～60%; Then cold rolled sheet is warmed up to 300～500 DEG C of anneal of carrying out 2.5h with the temperature rise rate of 100 DEG C/h, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 5min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 5min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 9h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 3 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that then it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 5 below) of sheet alloy.
Embodiment 10
Carry out an invention alloy 4# after melting and casting, it is carried out to homogenizing processing, treatment process is: start to heat up with 25 DEG C/h temperature rise rate, treat that temperature reaches 450～490 DEG C of insulation 4h, continue to be warmed up to 540～560 DEG C of insulation 22h with 25 DEG C/h again, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 25 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; First hot-rolled sheet is carried out a certain amount of cold roller and deformed, reduction in pass is 10～35%, and total deformation is 30～60%; Then cold rolled sheet is warmed up to 300～500 DEG C of anneal of carrying out 2.5h with the temperature rise rate of 100 DEG C/h, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 5min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 5min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 9h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 3 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that then it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 5 below) of sheet alloy.
Embodiment 11
Carry out an invention alloy 5# after melting and casting, it is carried out to homogenizing processing, treatment process is: begin to warm to 540～560 DEG C of insulation 29h with 45 DEG C/h temperature rise rate, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 45 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; First hot-rolled sheet is carried out a certain amount of cold roller and deformed, reduction in pass is 10～35%, and total deformation is 30～60%; Then cold rolled sheet is warmed up to 300～500 DEG C of anneal of carrying out 3.5h with the temperature rise rate of 150 DEG C/min, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 7min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 10min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 7h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 3 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that then it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 5 below) of sheet alloy.
Embodiment 12
Carry out an invention alloy 6# after melting and casting, it is carried out to homogenizing processing, treatment process is: start to heat up with 25 DEG C/h temperature rise rate, treat that temperature reaches 450～490 DEG C of insulation 5h, continue to be warmed up to 540～560 DEG C of insulation 29h with 25 DEG C/h again, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 25 DEG C/h with stove.After homogenizing, by ingot casting crop milling face, reheat 520～555 DEG C for hot rolling, reduction in pass is 4%～36%, hot rolling total deformation > 92%, and finishing temperature is lower than 300 DEG C; First hot-rolled sheet is carried out a certain amount of cold roller and deformed, reduction in pass is 10～35%, and total deformation is 30～60%; Then cold rolled sheet is warmed up to 300～500 DEG C of anneal of carrying out 3.5h with the temperature rise rate of 150 DEG C/min, carries out coolingly in air cooling mode, be then cold rolled to 1mm thick, reduction in pass is in 10～30%, and total deformation is 50～75%; And then on cold rolled sheet, directly cut sample and be placed in 545～555 DEG C of heat treatment furnaces and carry out 7min solution treatment, sample temperature rise rate is greater than 200 DEG C/min.Subsequently by the alloy sample after solution treatment from solid solution temperature to be greater than the rate of temperature fall cool to room temperature of 200 DEG C/s.Subsequently quenching state sample is transferred in 2～5min to the isothermal preageing that carries out 10min in 110 DEG C～130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 7h in the isothermal preageing stove of 60 DEG C～80 DEG C, and placed 14 days (T4P preageing state) in room temperature.Then multistage preageing state sample is divided into two groups, one group of sample directly forms performance and other mechanical property measurement (as shown in Table 3 below), and first another group sample carries out 2%～5% preliminary draft, the simulation paint baking that then it is carried out to 185 DEG C/20min is analyzed the bake hardening increment (as shown in Table 5 below) of sheet alloy.
Table 2 embodiment 1 ?in 6 several sheet alloys in the mechanical property of T4P state
Table 3 embodiment 7 ?in 12 several sheet alloys in the mechanical property of T4P state
Table 4 embodiment 1 ?several sheet alloy T4P states and simulation baking vanish state mechanical property in 6
Table 5 embodiment 7 ?several sheet alloy isothermal T4P states and simulation baking vanish state mechanical property in 12
Because alloying constituent, heat processing technique and heat treating regime etc. are all associated golden stamping performance to Al ?Mg ?Si and bake hardening increment has impact, particularly along with solute element change in concentration in alloy substrate, corresponding processing and thermal treatment process must be carried out certain adjustment, just may make in alloy substrate, can be distributed with before solid solution the particle of a certain amount of different scale, and then alloy recrystallization process and Texture evolution process produce the desired impact effect of the present invention.Fig. 2 shows the present invention and intends the schematic diagram that utilizes multiple dimensioned particle to regulate and control recrystallization crystal particle dimension and form.In figure, black line or dotted line represent the deformation bands forming in deformation process, and black point-like and black irregular pattern represent the different scale particle distributing in matrix, and grey irregular pattern represents recrystal grain.For the lower alloy of content of solute, although also can be distributed with the particle of some amount in cold rolling state alloy substrate, particle is mainly Mg
2si and Al
15mn
3si
2phase.These size of particles are also little, also not little (reaching nano level), so these particles can not be brought into play PSN effect and make a large amount of recrystal grain forming cores around particle in high-temperature heat treatment process, can not significantly hinder growing up of recrystal grain, finally make the increase of alloy along with heat treatment time, the recrystal grain that starts to form is grown up (if Fig. 2 (a) is (b) as shown in (c)) fast.And for the higher alloy of solute element concentration, make can be distributed with in alloy substrate the different scale particle of some amount by suitable processing and thermal treatment process regulation and control, comprise thick Al (Fe, Mn) Si phase and tiny Mg
2si, Al
6mn or Al
15mn
3si
2equate, alloy after cold roller and deformed because oversize particle strain energy storage is around larger, in high-temperature heat treatment process, can bring out a large amount of recrystal grain forming cores (as shown in Fig. 2 (e)), simultaneously owing to being also distributed with more small and dispersed particle in alloy substrate (as Al
6mn or Al
15mn
3si
2phase) grow up and there is certain inhibition for recrystal grain, finally make alloy recrystallization grain-size tiny evenly, and increase and then affect the Texture evolution process of sheet alloy inside because this inhibition also can make grain orientation rotation difficulty, finally make texture component that alloy substrate contains and content more be conducive to the raising of alloy punching forming property.The present invention carries out design of alloy according to this design philosophy exactly, and by suitable heat processing technique etc., tissue and performance are regulated and controled.First embodiment 1～6 carries out process annealing after all adopting hot rolling, and then carries out the cold rolling 1mm that is machined to of certain deflection, and alloy sheet material carries out follow-up solution hardening and Pre-aging treatment etc. subsequently, and alloy over-all properties is as shown in table 2.As can be seen from Table 2, along with the increase of solute element concentration, the particle kind that distributes in alloy substrate is more and particle size range is larger (if Fig. 3 (a) is (b) as shown in the particle distribution figure in cold rolling state alloy substrate), more approach the design philosophy that the present invention utilizes different scale particle regulation and control alloy structure and performance at first, also constantly increase even if therefore just can observe its corresponding forming property r value in the ever-increasing situation of alloy strength, reach as high as more than 0.6.To 5# with 6# alloy solid solution state is carried out corresponding EBSD grain-size and textile analysis can be found, in 5# alloy substrate, average grain size is only 15 μ m left and right, corresponding texture component also differs greatly with conventional aluminum alloy heat texture component after treatment, mainly comprises that winding is to cube orientation Cube that has rotated 18 °
nD18, Goss{011}<100> texture, Copper{112}<111> texture and P{011}<122> texture, its corresponding volume fraction is respectively: 9.95,4.20,4.54 and 6.36% (as Fig. 4 (a) (b) as shown in).Rotation cubic texture Cube in these texture components
nD18all be conducive to raising and the anisotropic reduction of alloy punching forming property with P texture.But in the time that alloy substrate contains the Zn element of some amount (as the 6# alloy in embodiment 6), the grain-size of this alloy not only further declines, average grain size is only 14 μ m, and what is more important is through composition and process optimization, even if the faint texture of observing in 5# alloy substrate also disappears, grain orientation in alloy substrate be substantially random orientation (as Fig. 5 (a) (b) as shown in), this is very beneficial for reducing the anisotropy of sheet alloy and improves its corresponding stamping performance (as shown in table 2).
In addition, can be found by table 2, adopt the preparation technology in embodiment 1～6, although the stamping performance of 4#, 5# and 6# alloy is better, the stamping performance of 1#, 2# and 3# alloy relatively low (r value is generally lower than 0.6).Therefore, for developed new series aluminium alloy, must develop and a kind ofly more be conducive to improve this and be associated the preparation technology of golden stamping performance, and to adopt suitable heat processing technique regulation and control texture component and content and then put forward heavy alloyed stamping performance be also one of means that generally adopt at present.Embodiment 7 ?12 first carry out the cold roller and deformed of certain deflection after all adopting hot rolling, and then carry out process annealing, be machined to 1mm by cold rolling annealed state sheet alloy more subsequently, and alloy sheet material carries out follow-up solution hardening and Pre-aging treatment etc., alloy over-all properties is as shown in table 3.As can be seen from Table 3,1# ?6# alloy after this art breading, its corresponding r value is all significantly improved, and the r value of 1# alloy brings up to 0.595 by 0.571 in embodiment 1, and larger (bringing up to 0.727 by 0.617 in embodiment 6) of 6# alloy increase rate.As can be seen here, make full use of different scale particle and be aided with the regulation and control of certain heat processing technique the stamping performance that can significantly promote Al ?Mg ?Si and be associated gold, its r value is once brought up to more than 0.7 by 0.6 of routine, and the alloy of developing and preparation technology are applicable to being applied to the punching of Complex Automobile Parts.
Because automobile board is except there are certain requirements stamping performance, the bake hardening increment of going back alloy sheet material has higher requirement, otherwise can be because automobile component intensity deforms or the problem such as depression compared with low in actual application.Invention alloy, after the multistage isothermal Pre-aging treatment in embodiment 1～12, more all shows very excellent bake hardening increment (as shown in table 4 and table 5) after certain predeformation and 185 DEG C/20min simulation paint baking.But with do not add Zn element Al ?Mg ?Si be associated metallographic ratio, add a certain amount of element Zn and substantially all can show good bake hardening increment through multistage isothermal Pre-aging treatment again.This be mainly due to add after element Zn can with alloy substrate in Mg element form Mg ?Zn solute element cluster or formation and Al ?Zn ?Mg be associated similar strengthening phase in gold (as η ' etc.), thereby make invention alloy can make full use of heterogeneous complex intensifying effect (comprise Mg ?Si, Mg ?Zn solute atoms cluster, β " and η ' equates), finally show excellent bake hardening increment.The bake hardening increment of invention alloy reaches as high as 157MPa, and this increment is far away higher than the current AA6016 of commercial production and the bake hardening increment of AA6111 alloy (being only 80～90MPa).
In sum, the present invention is by Composition Design, processing and optimization of Heat Treatment Process, and then make to be distributed with in alloy substrate the different scale particle of certain content, after the inhibition that utilizes the hormesis (being PSN effect) of oversize particle to recrystal grain forming core and small and dispersed particle to grow up to recrystal grain makes sheet alloy solution hardening, recrystal grain is tiny evenly, corresponding texture is taking rotation cube and P texture as main, even there is not texture, finally make T4P state sheet alloy show excellent stamping performance.In addition, by suitable preageing technique, to interactional fine regulation and control between each main alloying element Mg, Si, Cu and Zn in novel aluminum alloy, the invention alloy finally also making has very excellent bake hardening increment equally.Therefore, alloy of the present invention and technique are not only applicable to being applied to the manufacture of automobile body outer board aluminium alloy very much, thereby accelerate automotive light weight technology process, and also there is certain directive significance for other field with exploitation, processing and the application of high formability and quick aging response type aluminium alloy, be worth automobile production producer and aluminium alloy processing enterprise to be paid attention to this invention alloy and relevant preparation technology, make it can be promoted and apply in this field as early as possible.
Although illustrated and described embodiments of the invention, for the ordinary skill in the art, be appreciated that without departing from the principles and spirit of the present invention and can carry out multiple variation, amendment, replacement and modification to these embodiment, scope of the present invention is by claims and be equal to and limit.
Claims (9)
1. an automobile high formability aluminum alloy materials, the chemical composition and the mass percentage content thereof that it is characterized in that this alloy are: Zn:0.02～4.2wt%, Mg:0.4～1.5wt%, Si:0.2～1.25wt%, Cu:0.05～1.0wt%, Fe≤0.65wt%, Mn:0.05 ~ 0.5wt%, Cr≤0.25wt%, Ti≤0.25wt%, B≤0.2wt%, surplus is Al.
2. automobile according to claim 1 high formability aluminum alloy materials, it is characterized in that: Zn, Si and Cu content range in its chemical composition are respectively Zn:0.025～4.0wt%, Si:0.35～1.0 wt%, Cu:0.1～0.95wt%, the Mg/Si quality of its chemical composition Mg, Si is 1.0～2.3 than scope, Fe≤0.55wt%, Mn:0.06 ~ 0.4wt%.
3. the preparation method with high formability aluminum alloy materials according to the automobile described in claim 1 ~ 2 any one, described preparation method comprises the following steps:
Step 1, melting and casting: first fine aluminium is all added to crucible, furnace temperature is set in to 850 DEG C, after fine aluminium fusing, add Al-20wt%Si, Al-50wt%Cu, Al-20wt%Fe, Al-10wt%Mn master alloy, and add insulating covering agent (50wt%NaCl+50wt%KCl); Continue melt heating, treat master alloy fusing, after melt temperature reaches 750 DEG C, it is stirred solute element is mixed, then after 750 DEG C of insulation 30min, set furnace temperature and make melt cool to 710 DEG C, then in melt, add pure Zn and pure Mg, and fully stir it is thoroughly dissolved; Sampling analysis composition in the time that melt temperature reaches 730 DEG C again, if component metering value is lower than design load, suitably add a certain amount of master alloy according to scaling loss situation, if component metering value, higher than design load, is suitably added a certain amount of metal fine aluminium according to excessive value and diluted; Continue to skim, add after melt rises to 740 DEG C refining agent to carry out refinery by de-gassing; Then while melt temperature being down to approximately 720 DEG C, add Al-5wt%Ti-1wt%B grain-refining agent and carry out agitation as appropriate, finally after this temperature insulation 10min, melt being cast in the punching block of surrounding water-cooled;
Step 2, single-stage or twin-stage homogenizing: Zn content directly adopts single-stage homogenizing lower than the aluminium alloy of 0.5wt%, be warmed up to 540 ~ 560 DEG C of insulation 15 ~ 30h by the alloy sample after melting and casting with 20 ~ 50 DEG C/h, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 20 ~ 50 DEG C/h with stove; And Zn content is in the time of 0.5wt% ~ 4.0wt%, adopt twin-stage homogenization process, start to heat up with 20 ~ 50 DEG C/h temperature rise rate by the alloy sample after melting and casting, treat that temperature reaches 450 ~ 490 DEG C of insulation 2 ~ 6h, continue to be warmed up to 540 ~ 560 DEG C of insulation 15 ~ 30h with 20 ~ 50 DEG C/h again, and then take out sample while being cooled to 100 DEG C with the rate of temperature fall of 20 ~ 50 DEG C/h with stove;
Step 3, hot rolling deformation: the sample that step 2 is taken out carries out hot rolling: start rolling temperature is at 520 ~ 555 DEG C, and reduction in pass is 4% ~ 36%, hot rolling total deformation > 92%, finishing temperature obtains hot rolled plate lower than 300 DEG C;
Step 4, process annealing or cold roller and deformed+process annealing: the hot rolled plate that step 3 is obtained carries out process annealing or cold roller and deformed+process annealing, then directly take out and carry out air cooling and obtain annealed state sheet material;
Step 5, cold roller and deformed: the annealed state sheet material that described step 4 is obtained carries out cold roller and deformed, described cold roller and deformed cold rolling total deformation is between 50% ~ 85%, and reduction in pass obtains cold rolled sheet between 10% ~ 35%;
Step 6, solution treatment: the cold rolled sheet that step 5 is obtained carries out solution treatment: in 545 ~ 560 DEG C of heat treatment furnaces, carry out the solution treatment of 1 ~ 15min, sample temperature rise rate is greater than 100 DEG C/min;
Step 7, quench treatment: the alloy sample after solution treatment is obtained to quenching state sample from solid solution temperature with the rate of temperature fall cool to room temperature that is greater than 100 DEG C/s;
Step 8, multistage Pre-aging treatment: the quenching state sample that step 7 is obtained is transferred to the isothermal preageing that carries out 1 ~ 30min in 100 DEG C ~ 130 DEG C isothermal preageing stoves in 2 ~ 5min, then transferred to the isothermal Pre-aging treatment that carries out 5 ~ 15h in the isothermal preageing stove of 60 DEG C ~ 90 DEG C, finally it is placed to the aluminum alloy plate materials that obtains having high formability for 14 days in room temperature.
4. the preparation method of high formability aluminum alloy materials for automobile as claimed in claim 3, it is characterized in that: the process annealing in described step 4 is all warmed up to 300 ~ 500 DEG C of anneal of carrying out 1 ~ 4h with the temperature rise rate of 20 DEG C/h ~ 200 DEG C/min, then directly take out and carry out air cooling.
5. the preparation method of high formability aluminum alloy materials for automobile as claimed in claim 3, is characterized in that: in described step 4 cold roller and deformed+process annealing is that cold roller and deformed reduction in pass is 10 ~ 35%, total deformation is 30 ~ 60%; Process annealing is all warmed up to 300 ~ 500 DEG C of anneal of carrying out 1 ~ 4h with the temperature rise rate of 20 DEG C/h ~ 200 DEG C/min, then directly takes out and carries out air cooling.
6. the preparation method of high formability aluminum alloy materials for automobile as claimed in claim 3, is characterized in that: the cold roller and deformed total deformation in described step 5 is between 50% ~ 75%, and reduction in pass is between 15% ~ 30%.
7. the preparation method of high formability aluminum alloy materials for automobile as claimed in claim 3, it is characterized in that: the solution treatment in described step 6: in 545 ~ 555 DEG C of heat treatment furnaces, carry out the solution treatment of 2 ~ 8min, sample temperature rise rate is greater than 200 DEG C/min.
8. the preparation method of high formability aluminum alloy materials for automobile as claimed in claim 3, it is characterized in that: the quench treatment in described step 7, obtains quenching state sample from solid solution temperature with the rate of temperature fall cool to room temperature that is greater than 200 DEG C/s by the alloy sample after solution treatment.
9. the preparation method of high formability aluminum alloy materials for automobile as claimed in claim 3, it is characterized in that: the multistage Pre-aging treatment in described step 8, quenching state sample is transferred in 2 ~ 5min to the isothermal preageing that carries out 1 ~ 15min in 110 DEG C ~ 130 DEG C isothermal preageing stoves, then transferred to the isothermal Pre-aging treatment that carries out 6 ~ 13h in the isothermal preageing stove of 60 DEG C ~ 80 DEG C, finally it is placed to the aluminum alloy plate materials that obtains having high formability for 14 days in room temperature.
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