CN111705274A - Processing method of Al-Zn-Mg- (Cu) alloy material - Google Patents
Processing method of Al-Zn-Mg- (Cu) alloy material Download PDFInfo
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- CN111705274A CN111705274A CN202010546493.4A CN202010546493A CN111705274A CN 111705274 A CN111705274 A CN 111705274A CN 202010546493 A CN202010546493 A CN 202010546493A CN 111705274 A CN111705274 A CN 111705274A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
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Abstract
The invention provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which is used for solving the problems of excellent formability, high strength and excellent corrosion resistance of the alloy plate in the prior art. The preparation method comprises the steps of carrying out high-temperature solid solution and quenching treatment on an Al-Zn-Mg- (Cu) alloy plate, carrying out isothermal treatment at preset medium and low temperatures, carrying out isothermal aging treatment at room temperature after cooling, carrying out machining forming, and carrying out isothermal treatment at preset medium and high temperatures to obtain the Al-Zn-Mg- (Cu) alloy plate component. The alloy plate has lower strength and excellent formability through short-time medium and low temperature pre-aging treatment, and is beneficial to processing and forming; after the alloy member is formed, isothermal treatment is carried out at a high temperature, so that the strength of the member can be improved, the member has excellent corrosion resistance, the manufacturing process of the alloy member is obviously shortened, the production cost is reduced, and the alloy member can be applied to batch production.
Description
Technical Field
The invention belongs to the field of material forming and processing, and particularly relates to a processing method of an Al-Zn-Mg- (Cu) alloy material.
Background
The aluminum material with light weight and high performance is an important application requirement for realizing high-speed, energy-saving, safe and comfortable operation of vehicles, ships, aircrafts and the like, and particularly, the Al-Zn-Mg- (Cu) alloy with low density, high toughness and excellent corrosion resistance is widely used for preparing key bearing components of aerospace, automobiles, armors, high-speed trains and the like. The impact-resistant and anti-collision members of some vehicles are gradually made of light-weight high-performance aluminum alloy materials, replace steel materials with high density, are beneficial to reducing weight of the vehicles and improving collision energy absorption effects, wherein Al-Zn-Mg- (Cu) series alloy with high strength and toughness and high specific strength becomes an important base material for realizing light-weight design and manufacturing of the members. At present, part of aluminum material manufacturers and automobile manufacturers have developed application development and test and examination work of Al-Zn-Mg- (Cu) alloy plates or profiles on automobile parts.
In the prior art, Al-Zn-Mg- (Cu) alloy obtains excellent comprehensive performance through a solid solution and aging treatment method, and the alloy in a solid solution-quenching state can generate a certain sequence of precipitation phase precipitation in the aging treatment process, namely supersaturated solid solution → GP zone → η' → η (MgZn)2) It is believed that the primary strengthening phases of the Al-Zn-Mg- (Cu) based alloy are GP zones and η 'phases in which the GP zones are in perfect coherent relationship with the aluminum matrix and η' phases are in semi-coherent relationship with the aluminum matrix in both underaged and peak aged conditions, that in the overaged condition the Al-Zn-Mg- (Cu) based alloy forms primarily a η phase which is in non-coherent relationship with the aluminum matrix and is essentially free of strengthening capacity, and that the T6 peak aged (typically 120 ℃/24h) treated Al-Zn-Mg- (Cu) based alloy precipitates a large number of finely dispersed GP zones and η 'in the crystal'And the hardness and the strength of the alloy reach the highest values, but the corrosion resistance is poor. The corrosion resistance of the Al-Zn-Mg- (Cu) alloy can be obviously improved by adopting a two-stage aging heat treatment process such as T74, T73 and the like, but the alloy strength can be reduced by 10-15%, and the Al-Zn-Mg- (Cu) alloy can have high strength and good corrosion resistance by adopting a regression re-aging treatment process (three-stage aging treatment). The design and development of the Al-Zn-Mg- (Cu) alloy plates or profiles with large size and certain thickness, such as T6, T74, T73, regression and reaging treatment process, and the like, have the total aging time of 18-60h, but need to be heated and cooled repeatedly, and the process is relatively complex.
The forming heat treatment process of the aluminum alloy member is generally as follows: plate → solution treatment → quenching → pre-stretching and straightening → forming → age hardening treatment, thereby obtaining the aluminum alloy member with higher strength. Because the Al-Zn-Mg- (Cu) alloy material has higher strength, the plate, the section or the pipe has great difficulty or is difficult to realize further deep processing in further deep processing such as stamping, bending, bulging and the like, so that the deep processing yield is low, and the Al-Zn-Mg- (Cu) alloy material cannot be widely applied to the aspect of light-weight manufacturing of key structural components such as vehicles and the like. Meanwhile, after being assembled, aluminum alloy parts such as a vehicle body frame, a covering plate, an anti-collision beam and the like which are manufactured by stamping or extrusion and the like are subjected to integral treatment such as anodic oxidation, paint spraying, paint baking and the like, and the paint baking treatment can influence the type, appearance, size and the like of a strengthening phase in an age-hardening aluminum alloy matrix, so that the final service performance of the aluminum alloy parts is influenced. For the manufacturing of punch forming parts, the aluminum alloy plate is required to have lower strength and excellent formability before punch forming, but the Al-Zn-Mg- (Cu) alloy has obvious natural aging phenomenon after solution treatment and quenching, so that the strength of the quenched Al-Zn-Mg- (Cu) alloy plate is increased along with the prolonging of the room temperature storage time, namely the Al-Zn-Mg- (Cu) alloy plate after natural aging has high and unstable strength, and the problems of large control difficulty, low forming quality and the like in the punch forming process are caused.
Meanwhile, after the body frame and the main components (such as covering parts, collision parts and the like) of transportation equipment such as automobiles and the like are assembled on a production line, painting and baking finish treatment at a certain temperature can be carried out, so that the aging precipitation behavior of the aging hardening type aluminum alloy can be obviously influenced in the component forming process, the baking finish treatment and the like, and if the forming and heat treatment processes are improperly controlled, the forming quality is not high or the final component is difficult to have high strength and good corrosion resistance, so that the safety service of the component is greatly influenced.
Disclosure of Invention
In order to realize high-quality forming of an Al-Zn-Mg- (Cu) alloy plate member and have high strength and good corrosion resistance, the embodiment of the invention provides a preparation method of the Al-Zn-Mg- (Cu) (including Al-Zn-Mg and Al-Zn-Mg-Cu) alloy plate member, and the alloy strength is reduced through medium-low temperature isothermal treatment, so that the alloy plate has lower strength and excellent formability, and is beneficial to subsequent processing and forming; after molding, isothermal treatment is carried out at a high temperature, the strength of the member is improved, the member has corrosion resistance, the manufacturing process of the Al-Zn-Mg- (Cu) alloy member is obviously shortened, and the production cost is reduced.
In order to achieve the above purpose, the technical solution adopted by the embodiment of the present invention is as follows:
a processing method of an Al-Zn-Mg/Al-Zn-Mg-Cu alloy material comprises the following steps:
step 1, carrying out high-temperature solid solution and quenching treatment on Al-Zn-Mg/Al-Zn-Mg-Cu alloy to obtain quenched alloy;
step 2, carrying out isothermal treatment on the quenched alloy at 70-140 ℃ for a preset time, and then carrying out air cooling or water cooling to room temperature;
step 3, carrying out isothermal treatment on the alloy at room temperature at-10-40 ℃ for a preset time to obtain a naturally aged alloy;
and 5, carrying out isothermal treatment on the treated alloy at the temperature of 160-190 ℃ for a preset time, and then carrying out air cooling to room temperature to obtain the Al-Zn-Mg/Al-Zn-Mg-Cu alloy material with high strength and corrosion resistance.
As a preferred embodiment of the present invention, the processing method further includes, between step 3 and step 5:
and 4, processing the alloy after natural aging into a member with a required shape to obtain the alloy with a specific shape.
As a preferred embodiment of the invention, the high-temperature solution treatment is carried out by heating in a salt bath furnace, an air furnace or an aluminum alloy air cushion furnace; the quenching treatment adopts water quenching or gas quenching, and the cooling rate is 1-5 ℃/s.
As a preferred embodiment of the present invention, the high-temperature solution treatment in step 1 adopts a first-stage solution treatment process, and the solution treatment system is as follows: the solution treatment temperature is 430-490 ℃, and the solution treatment time is 0.5-5 h.
As a preferred embodiment of the present invention, the high-temperature solution treatment in step 1 adopts a two-stage solution treatment process, and the solution treatment system is as follows: the temperature of the first-stage solution treatment is 380-450 ℃, and the time of the solution treatment is 1-5 h; the temperature of the second stage solution treatment is 430-480 ℃, and the time of the solution treatment is 0.5-5 h.
In a preferred embodiment of the present invention, the member processed into the desired shape in the step 4 has a deformation amount of 1 to 15%. 7. The method for processing an Al-Zn-Mg/Al-Zn-Mg-Cu based alloy material according to claim 6, wherein said processing in step 4 includes pre-stretching, punching, bending and bulging.
As a preferred embodiment of the present invention, the Al-Zn-Mg/Al-Zn-Mg-Cu based alloy material is a plate or a tube having a thickness of 0.5 to 4.0 mm.
As a preferred embodiment of the present invention, the preset time of the isothermal treatment in step 2 is 10-120 min; the moderate temperature treatment time in the step 3 is 7-20 days; and in the step 5, the isothermal treatment is carried out for 10-50 min.
The technical scheme provided by the embodiment of the invention has the following beneficial effects:
the processing method of the Al-Zn-Mg- (Cu) alloy material is characterized in that after high-temperature solid solution and quenching, the Al-Zn-Mg- (Cu) alloy material is subjected to short-time medium-low temperature preaging treatment without repeated heating regression treatment, and after the Al-Zn-Mg- (Cu) alloy material is subjected to room-temperature environmental temperature treatment, the Al-Zn-Mg- (Cu) alloy material is low in strength, high in elongation after fracture and excellent in plastic deformation capacity, and is beneficial to forming and processing in various modes; after molding or directly carrying out isothermal treatment at a high temperature, the strength of the member is improved, and the member has corrosion resistance; meanwhile, the process method is simple and convenient to operate, short in forming treatment time, good in combination of heat treatment effect and processing process flow characteristics, capable of remarkably shortening the manufacturing process of the Al-Zn-Mg- (Cu) alloy component, reducing production cost and capable of being applied to batch production.
Drawings
In order to more clearly illustrate the technical solutions in the embodiments of the present invention, the drawings needed to be used in the description of the embodiments will be briefly introduced below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings based on these drawings without creative efforts.
FIG. 1 is a schematic flow chart of a processing method of an Al-Zn-Mg- (Cu) alloy material according to an embodiment of the present invention;
FIG. 2A is a graph of tensile engineering stress-strain curves of 7075 aluminum alloy sheet (naturally aged at 37 ℃ C.) according to example 2 of the present invention;
FIG. 2B is a graph of the tensile engineering stress-strain curve of the 7075 aluminum alloy sheet (natural aging at 0 ℃) in example 2 of the present invention;
FIG. 2C is a graph of tensile engineering stress-strain curves of 7075 aluminum alloy sheet (room temperature naturally aged) of example 2 in accordance with the present invention;
FIG. 2D is a graph of the tensile engineering stress-strain curve of a 7075 aluminum alloy sheet (100 deg.C/30 min preaging) of example 2 of the present invention;
FIG. 3 is a microscopic TEM photograph of an aluminum alloy specimen of example 2 of the present invention;
FIG. 4 is a cross-sectional view of a 7075 aluminum alloy intergranular corrosion specimen in example 2 of the present invention;
FIG. 5A is a stress-strain curve of the tensile engineering of the 7075 aluminum alloy sheet of example 3 of the present invention (room temperature natural aging +190 deg.C/30 min bake);
FIG. 5B is a stress-strain curve of the tensile engineering of the 7075 aluminum alloy sheet of example 3 of the present invention (room temperature natural aging +190 deg.C/10 min bake);
FIG. 5C is a stress-strain curve of the tensile engineering of the 7075 aluminum alloy sheet of example 3 of the present invention (room temperature natural aging +170 deg.C/30 min bake);
FIG. 6A is a stress-strain curve of the tensile engineering of the 7075 aluminum alloy plate (room temperature natural aging + 10% pre-stretching +180 ℃/30min baking) of example 4 of the present invention;
FIG. 6B is a stress-strain curve of the tensile engineering of the 7075 aluminum alloy plate (room temperature natural aging + 5% pre-stretching +180 ℃/30min baking) of example 4 of the present invention;
FIG. 7A is a graph of room temperature tensile engineering stress-strain curves for 7050 aluminum alloy sheet of example 6 of the present invention (baked at 120 deg.C/24 h);
FIG. 7B is a room temperature tensile engineering stress-strain plot of the 7050 aluminum alloy sheet of example 6 of the present invention (room temperature natural aging +180 deg.C/30 min bake).
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, embodiments of the present invention will be described in detail with reference to the accompanying drawings.
The invention provides a processing method of an Al-Zn-Mg- (Cu) alloy material according to the characteristics of the Al-Zn-Mg- (Cu) alloy material, which is a forming-heat treatment method capable of improving the forming processing capability of the Al-Zn-Mg- (Cu) alloy material and realizing heat treatment strengthening (such as baking finish) after forming processing. Wherein, after the Al-Zn-Mg- (Cu) alloy plate in the quenching state after solid solution is subjected to medium-low temperature isothermal treatment, a large amount of fine atom clusters (or GP zones) can be formed in an aluminum matrix, so that the alloy is hardened to a lower degree, then in the process of room temperature heat preservation treatment, the GP zones grow up, and simultaneously, a part of the GP zones with small sizes can be separated out from the matrix and are dispersed in the aluminum matrix. Because the GP zone is coherent with the matrix, the GP zone is easier to be cut by dislocation, the dislocation sliding free path is increased, the plastic deformation capacity of the alloy is improved, the Al-Zn-Mg- (Cu) alloy plate has lower strength, excellent plastic deformation capacity and performance stability, and good forming processing such as stamping, bending, bulging and the like is realized. After the formed part is subjected to medium-high temperature isothermal treatment (also called baking finish treatment or baking treatment), the larger GP zone can be converted into eta' precipitation phase, and the fine GP zone is further grown. Because the eta 'phase and the matrix are half coherent, the dislocation slip resistance in the plastic deformation process can be obviously improved, and the eta' phase is a main strengthening phase of Al-Zn-Mg- (Cu) alloy and can obviously improve the alloy strength. Meanwhile, an intercrystalline corrosion test shows that the Al-Zn-Mg- (Cu) alloy material has better pitting corrosion resistance and intercrystalline corrosion resistance.
The invention provides a processing method of an Al-Zn-Mg- (Cu) alloy material by combining the tissue evolution rule of the Al-Zn-Mg- (Cu) alloy under the conventional heat treatment process and the production flow of a typical automobile component, based on the tissue characteristics of the Al-Zn-Mg- (Cu) alloy and the response behavior of the Al-Zn-Mg- (Cu) alloy to heat treatment, which comprises the following steps:
step 1, carrying out high-temperature solid solution and quenching treatment on the Al-Zn-Mg- (Cu) alloy to obtain a quenched alloy.
The alloy material in the invention can be a plate, a section or a pipe, wherein the plate is preferably a thin plate. In the step of high-temperature solid solution, a one-stage or two-stage solid solution treatment process is adopted. Wherein, the first-stage solution treatment system comprises the following steps: the solution treatment temperature is 430-490 ℃, and the solution treatment time is 0.5-5 h; the two-stage solution treatment system comprises: the temperature of the first-stage solution treatment is 380-450 ℃, and the time of the solution treatment is 1-5 h; the temperature of the second stage solution treatment is 430-480 ℃, and the time of the solution treatment is 0.5-5 h. The high-temperature solid solution is heated by a salt bath furnace, an air furnace or an aluminum alloy air cushion furnace, the quenching treatment adopts water quenching or gas quenching, and the cooling rate is 1-5 ℃/s. Preferably, the thickness of the Al-Zn-Mg- (Cu) alloy plate or pipe is 0.5-4.0 mm.
And 2, carrying out isothermal treatment on the quenched alloy at a preset medium-low temperature for a preset heat preservation time, and then air-cooling or water-cooling to room temperature. Preferably, the preset medium-low temperature in the step is 70-140 ℃, and the preset heat preservation time is 10-120 min. In the step, the medium-low temperature short-time isothermal pretreatment is carried out, so that a large amount of fine and dispersed atom clusters or primary metastable phases are precipitated in the quenched Al-Zn-Mg- (Cu) alloy matrix, the room-temperature environmental storage/natural age hardening phenomenon of the quenched Al-Zn-Mg- (Cu) alloy is weakened or inhibited, the alloy plate has lower strength and good forming capability, and a tissue foundation is created for final medium-high temperature treatment or baking finish hardening and the like.
And 3, carrying out isothermal treatment on the alloy at room temperature for a preset time in a temperature environment close to room temperature to obtain the naturally aged alloy. Preferably, the temperature of the isothermal treatment in the step, which is close to room temperature, is-10 ℃ to 40 ℃, and the preset time of the isothermal treatment is 7 to 20 days.
And 5, carrying out isothermal treatment on the pre-aged alloy at the temperature of 160-190 ℃ for preset time, and then air-cooling to room temperature to obtain the Al-Zn-Mg- (Cu) alloy material. Preferably, the preset medium-high temperature in the step is 160-190 ℃, and the isothermal treatment preset time is 10-50 min. The intermediate-high temperature isothermal treatment in the step improves the strength of the alloy and has good corrosion resistance.
Further, the method for processing an Al-Zn-Mg- (Cu) -based alloy material according to an embodiment of the present invention may further include:
and 4, processing the pre-aged alloy into a member with a required shape to obtain the pre-aged alloy with a specific shape. In this step, the deformation amount of the member processed into a desired shape is 1 to 15%. The processing includes pre-stretching, stamping, bending, bulging and the like.
After the medium-low temperature isothermal aging of the step 2 and the natural aging at room temperature of the step 3, the strength of the alloy is reduced, and the forming and processing process of the alloy material is more facilitated, so that in the step, the alloy can be processed into the required alloy component under good processing performance according to the requirement of the component. And (5) carrying out isothermal treatment at medium and high temperature in step 5, so that the machined and molded component has high strength and good corrosion resistance.
The processing method of the Al-Zn-Mg- (Cu) alloy material provided by the embodiment of the invention can be matched with a stamping/extrusion forming, heat treatment and baking varnish production line of light-weight thin-wall components (such as automobile bumpers, anti-collision beams, B columns and the like) of the Al-Zn-Mg- (Cu) alloy, and can remarkably shorten the manufacturing process of the Al-Zn-Mg- (Cu) alloy component and obtain a high-strength and corrosion-resistant thin-wall component while obtaining good formability.
The present invention will be described in further detail below with reference to several specific examples in order to better illustrate embodiments of the present invention.
Example 1
The embodiment provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which comprises the following steps:
101, performing solution treatment on a 7075 aluminum alloy plate with the thickness of 2.4mm in a salt bath furnace at 475 +/-3 ℃ for 1h, and then directly performing water quenching;
102, respectively carrying out isothermal pre-aging treatment at 90 +/-1 ℃, 100 +/-1 ℃, 110 +/-1 ℃, 120 +/-1 ℃ and 130 +/-1 ℃, wherein the pre-aging time is 10min, 20min, 30min, 40min, 60min and 120min at each pre-aging treatment temperature;
step 103, after the pre-aging is completed, cooling the plate to room temperature, and carrying out room temperature isothermal treatment (natural aging, about 25 ℃) for 14 days at room temperature;
and 105, finally, performing middle-high temperature or simulated paint baking heat preservation treatment on the board subjected to the room-temperature isothermal treatment for 14 days in a forced air drying oven at the temperature of 180 +/-1 ℃/30 min.
The microhardness (HV, load 200g, load time 15 seconds) of the pre-aged, naturally aged, simulated baked-paint alloy sheets was determined and the associated test data are shown in Table 1.
TABLE 1
Example 2
The embodiment provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which comprises the following steps:
101, performing solution treatment on a 7075 aluminum alloy plate with the thickness of 2.4mm in a salt bath furnace at 475 +/-3 ℃ for 1h, and then directly performing water quenching;
102, performing medium-temperature isothermal heat preservation pre-aging treatment at 100 +/-1 ℃ for 30 min;
103, carrying out isothermal treatment on the pre-aged plate at 0 ℃, 25 ℃ (room temperature) and 37 ℃ for 14 days (natural aging process in an environment close to room temperature) respectively;
and step 105, respectively carrying out 180 +/-1 ℃/30min simulated baking varnish heat preservation treatment on the board subjected to isothermal treatment for 14 days at the temperature of 0 ℃, 25 ℃ and 37 ℃ in a forced air drying oven.
The room temperature tensile properties (including tensile strength (sigma) of the alloy sheet in a simulated paint-baked state) were measured at 0 ℃, 25 ℃ (room temperature), 37 ℃ for 14 days of isothermal treatmentb) Yield strength (sigma)0.2) Elongation ()) and electrical conductivity, and Table 2 shows the aluminum alloy plate 7075 and the aluminum alloy T6 in different states during the processing of the present example,
Room temperature tensile properties (some include tensile properties in different directions along the sheet); table 3 shows the conductivity values of the aluminum alloys in the present example, example 3 and example 6 in different heat treatment states; table 4 shows the work hardening index n value and the plastic strain ratio r value of the aluminum alloy sheets of the present example and typical aluminum alloy sheets (including 7020, 7081, 60166111 types); table 5 shows the intergranular corrosion depths and grades for the processed 7075 aluminum alloy plate members and T6 in this example. FIG. 2A is a graph of tensile engineering stress-strain curves of 7075 aluminum alloy sheet (naturally aged at 37 ℃ C.) according to example 2 of the present invention; FIG. 2B is a graph of the tensile engineering stress-strain curve of the 7075 aluminum alloy sheet (natural aging at 0 ℃) in example 2 of the present invention; FIG. 2C is a graph of tensile engineering stress-strain curves of 7075 aluminum alloy sheet (room temperature naturally aged) of example 2 in accordance with the present invention; FIG. 2D is a graph of the tensile engineering stress-strain curve of a 7075 aluminum alloy sheet (100 deg.C/30 min preaging) of example 2 of the present invention; FIG. 3 is a microscopic TEM photograph of an aluminum alloy specimen of example 2 of the present invention; FIG. 4 is a cross-sectional view of a 7075 aluminum alloy intergranular corrosion specimen in example 2 of the present invention;
as shown in tables 2 to 5 and FIGS. 2A to 2D and FIGS. 3 and 4, the 7075 aluminum alloy plate had a tensile elongation at room temperature of 20.0% or more after being isothermally treated at 0 to 37 ℃ for 14 days, wherein the tensile elongation at 0 ℃ and 25 ℃ after being isothermally treated for 14 days was approximately 23.0%, which was equivalent to the elongation of 6111 aluminum alloy in a naturally aged state (about 22.0%). Meanwhile, the measurement results of the work hardening index n value and the plastic strain ratio r value which represent the forming capability of the alloy plate shown in the table 4 show that the forming capability of the 7075 aluminum alloy plate subjected to pretreatment of 100 ℃/30min and isothermal treatment of 25 ℃ for 14 days is equivalent to that of 6016-T4P and 6111-T4 alloy materials. Meanwhile, after the board is subjected to the isothermal treatment at the temperature of 0-37 ℃ for 14 days and is subjected to simulated paint baking treatment, the yield strength increment exceeds 100MPa, wherein the yield strength increment under the isothermal treatment conditions at the temperature of 0 ℃ and 25 ℃ respectively reaches 130MPa and 120MPa, and is superior to the paint baking hardening increment of aluminum alloy boards for automobile body covering parts such as 6016, 6111 and the like.
Meanwhile, Table 3 shows that after the aluminum alloy is pretreated at 100 ℃/30min and isothermally treated at 0-37 ℃ for 14 days and then is subjected to varnish baking at 180 ℃/30min, the conductivity values of the 7075 aluminum alloy are all higher than those of the conventional T6 state, and the 7075 aluminum alloy obtained by the processing method of the embodiment has better corrosion resistance. Further, the intercrystalline corrosion performance of the 7075 aluminum alloy plate in the state of 100 ℃/30min pretreatment +25 ℃ isothermal treatment for 14 days +180 ℃/30min baking finish is measured according to the national standard GB/7998-. FIG. 3 shows the intergranular precipitation during different treatment stages and in the T6 peak aging state (120. + -. 1 ℃/24 h). The 7075 aluminum alloy treated by the method has obviously better strength than the conventional 6000 series aluminum alloy material and has good corrosion resistance.
From the above, after the 7075 aluminum alloy plate is pretreated at 100 +/-1 ℃/30min and subjected to isothermal treatment at 0-37 ℃ for 14 days, the 7075 aluminum alloy plate not only has good plastic deformation capacity or forming capacity, but also shows excellent baking varnish hardening capacity, which indicates that the 7075 aluminum alloy plate material can be used for forming vehicle structural parts with certain shapes and can be adapted to a typical vehicle manufacturing and processing production line.
TABLE 2
TABLE 3
TABLE 4
In Table 4, "W" represents the quenched state; "T4" represents the natural aged state; "T4P" represents the pre-aged + naturally aged state.
TABLE 5
In Table 5, the national standard GB/7998-.
Example 3
The embodiment provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which comprises the following steps:
101, performing solution treatment on a 7075 aluminum alloy plate with the thickness of 2.4mm in a salt bath furnace at 475 +/-3 ℃ for 1h, and then directly performing water quenching;
102, performing medium-temperature isothermal heat preservation pre-aging treatment at 100 +/-1 ℃ for 30 min;
103, carrying out isothermal treatment on the pre-aged plate for 14 days at 25 ℃ (room temperature) (natural aging process);
and 105, respectively carrying out simulated baking varnish heat preservation treatment on the plate in the natural aging state at 170 +/-1 ℃/30min, 190 +/-1 ℃/10min and 190 +/-1 ℃/30min in a blast drying oven.
Room temperature tensile properties (including tensile strength (σ b), yield strength (σ 0.2), elongation ()) and electrical conductivity were measured for three different baked-finish alloy sheets, and table 3 is the electrical conductivity values for the aluminum alloys of examples 2, examples, and 6 in different heat-treated states; table 6 shows the room temperature tensile properties of the 7075 aluminum alloy sheets obtained in this example and example 4; FIG. 5A is a stress-strain curve of the tensile engineering of the 7075 aluminum alloy sheet of example 3 of the present invention (room temperature natural aging +190 deg.C/30 min bake); FIG. 5B is a stress-strain curve of the tensile engineering of the 7075 aluminum alloy sheet of example 3 of the present invention (room temperature natural aging +190 deg.C/10 min bake); FIG. 5C is a stress-strain curve of the 7075 aluminum alloy sheet of example 3 of the present invention (room temperature natural aging +170 deg.C/30 min bake) tensile engineering.
As shown in table 3, table 6 and fig. 5A to 5C, lowering the medium-high temperature treatment temperature (simulated paint bake temperature) failed to achieve higher strength and paint bake hardening increment of the alloy as compared to example 2.
Example 4
The embodiment provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which comprises the following steps:
101, performing solution treatment on a 7075 aluminum alloy plate with the thickness of 2.4mm in a salt bath furnace at 475 +/-3 ℃ for 1h, and then directly performing water quenching;
102, carrying out isothermal heat preservation preaging treatment at 100 +/-1 ℃ for 30 min;
103, carrying out isothermal treatment on the pre-aged plate for 14 days at 25 ℃ (room temperature) (natural aging process);
104, performing pre-stretching processing on the plate in the natural aging state by 5% and 10% of deformation respectively;
and 105, finally, performing simulated baking finish heat preservation treatment on the pre-stretched plate at 180 +/-1 ℃/30min in a blast drying oven.
The room-temperature tensile properties (including tensile strength (σ b), yield strength (σ 0.2) and elongation ()) of the two alloy plates with different pre-stretching deformation amounts after simulated paint baking are measured, the relevant test data are shown in table 6, and fig. 6A is a stress-strain curve diagram of the tensile engineering of the 7075 aluminum alloy plate (room-temperature natural aging + 10% pre-stretching +180 ℃/30min baking) in the example 4 of the invention; FIG. 6B is a stress-strain curve of the tensile engineering of the 7075 aluminum alloy sheet of example 4 of the present invention (room temperature natural aging + 5% pre-stretching +180 ℃/30min bake). As shown in Table 6, FIG. 6A and FIG. 6B, the pre-stretching deformation increased by 5% or 10% after natural aging resulted in a significant increase in yield strength of the final simulated as-baked alloy, and the increase in baking finish hardening was also significantly higher than that obtained in example 2. The method of the embodiment can not only ensure that the Al-Zn-Mg- (Cu) alloy plate or section can obtain high strength and good corrosion resistance after short-time heat treatment, but also can further improve the strength of the alloy and the hardening increment of baking finish by combining with the forming processing step, and the short-time processing capacity can be suitable for the production and manufacturing process of vehicle body components.
TABLE 6
In Table 6,. sigma.0.2As yield strength, σbTensile Strength, elongation at Break, Δ σ0.2Yield strength bake increment.
Example 5
The embodiment provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which comprises the following steps:
101, performing solution treatment on a 7050 aluminum alloy plate with the thickness of 2.0mm in a salt bath furnace at 475 +/-3 ℃ for 30min, and then directly performing water quenching;
102, carrying out isothermal heat preservation preaging treatment at 90 +/-1 ℃, 100 +/-1 ℃, 110 +/-1 ℃, 120 +/-1 ℃ and 130 +/-1 ℃, wherein the treatment time is 10min, 20min, 30min, 40min, 60min and 120min at each isothermal pre-treatment temperature;
103, carrying out isothermal treatment on the pre-aged plate for 14 days at 25 ℃ (room temperature) (natural aging process);
and 105, performing simulated baking finish heat preservation treatment on the plate in the natural aging state at 180 +/-1 ℃/30min in a blast drying oven.
The microhardness of the alloy plate in the pre-treatment state, the natural aging state and the simulated paint-baking state was measured, and Table 7 shows the microhardness (HV, load 200g, loading time 15 seconds) of the 7050 aluminum alloy plate treated in this example.
TABLE 7
Example 6
The embodiment provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which comprises the following steps:
101, performing solution treatment on a 7050 aluminum alloy plate with the thickness of 2.0mm in a salt bath furnace at 475 +/-3 ℃ for 30min, and then directly performing water quenching;
102, carrying out isothermal heat preservation preaging treatment at 100 +/-1 ℃ for 30 min;
103, carrying out isothermal treatment on the pre-aged plate for 14 days at 25 ℃ (room temperature) (natural aging process);
and 105, performing simulated baking finish heat preservation treatment on the plate in the natural aging state at 180 +/-1 ℃/30min in a blast drying oven.
Measuring the room temperature tensile property (including the tensile strength (sigma) of the alloy plate in the natural aging state (100 ℃/30min +14 days room temperature natural aging +180 ℃/30min) and the simulated paint baking state (100 ℃/30min +14 days room temperature natural aging +180 ℃/30min)b) Yield strength (sigma)0.2) Elongation ()), and electrical conductivity. For comparison, a rolled 7050 aluminum alloy sheet having a thickness of 2.0mm was subjected to solution treatment in a salt bath furnace at 475. + -. 3 ℃ for 30min, then directly water quenched, and then subjected to isothermal aging treatment at 120. + -. 1 ℃/24h (T6 peak aging treatment), and room-temperature tensile properties (including tensile strength (. sigma.)) of the alloy sheet were measuredb) Yield strength (sigma)0.2)、Elongation ()) and electrical conductivity. The relevant test data are shown in table 3, table 8 and fig. 5, and table 8 shows the room temperature tensile property results of the 7050 aluminum alloy plate treated in the embodiment in the 0 ° direction; FIG. 7A is a graph of room temperature tensile engineering stress-strain curves for 7050 aluminum alloy sheet of example 6 of the present invention (baked at 120 deg.C/24 h); FIG. 7B is a room temperature tensile engineering stress-strain plot of the 7050 aluminum alloy sheet of example 6 of the present invention (room temperature natural aging +180 deg.C/30 min bake).
As shown in tables 3 and 8 and fig. 7A and 7B, the 7050 aluminum alloy plate in the natural aging state also has good room-temperature tensile plasticity and forming performance, and the baking varnish hardening increment is equivalent to that of the 7075 aluminum alloy plate in example 2, namely, the 7075 aluminum alloy plate has good simulated baking varnish hardening capacity. Meanwhile, the table 3 shows that after the pretreatment of 100 ℃/30min and the isothermal treatment of 25 ℃ (room temperature) for 14 days and the baking finish treatment of 180 ℃/30min, the conductivity value of the 7050 aluminum alloy is higher than the conventional conductivity value of T6 states, which indicates that the 7050 aluminum alloy obtained by the treatment of the embodiment has better corrosion resistance.
TABLE 8
Example 7
The embodiment provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which comprises the following steps:
101, performing two-stage solution treatment on a 7050 aluminum alloy pipe with the thickness of 2.0mm, wherein the temperature of the first-stage solution treatment is 380 ℃, and the time of the solution treatment is 1 h; the temperature of the second-stage solution treatment is 430 ℃, and the time of the solution treatment is 5 h; then directly quenching with water to obtain a quenched alloy;
102, carrying out isothermal heat preservation preaging treatment on the quenched alloy at 70 ℃, wherein the treatment time is 120 min;
103, carrying out isothermal treatment on the pipe subjected to the pre-aging treatment at-10 ℃ for 20 days (natural aging process);
104, performing bulging processing on the pipe, wherein the deformation is 1%;
and 105, performing simulated baking finish heat preservation treatment at 160 ℃/50min on the pipe in the natural aging state and after bulging in a blast drying oven to obtain the alloy pipe with high strength and corrosion resistance.
Example 8
The embodiment provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which comprises the following steps:
101, subjecting a 7075 aluminum alloy plate with the thickness of 4mm to primary solution treatment for 0.5h at 490 ℃; then directly quenching with water to obtain a quenched alloy;
102, carrying out isothermal heat preservation preaging treatment on the quenched alloy at 140 ℃, wherein the treatment time is 100 min;
103, carrying out isothermal treatment on the pre-aged plate at 40 ℃ for 7 days (natural aging process);
104, according to a model of a required component, stretching, stamping and bending the plate, wherein the deformation amount is 15%;
and 105, performing simulated baking finish heat preservation treatment at 190 ℃/30min on the plate member which is in a natural aging state and is processed and formed in a blast drying oven, and obtaining the alloy plate member with high strength and corrosion resistance.
Example 9
The embodiment provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which comprises the following steps:
101, subjecting a 7075 aluminum alloy plate with the thickness of 0.5mm to primary solution treatment for 5 hours at 430 ℃; then directly quenching with water to obtain a quenched alloy;
102, carrying out isothermal heat preservation preaging treatment on the quenched alloy at 120 ℃, wherein the treatment time is 10 min;
103, carrying out isothermal treatment on the pre-aged plate at 25 ℃ for 14 days (natural aging process);
step 104, bending the plate according to a model of a required component, wherein the deformation amount is 10%;
and 105, performing simulated baking finish heat preservation treatment at 160 ℃/40min on the plate member which is in a natural aging state and is processed and formed in a blast drying oven, and obtaining the alloy plate member with high strength and corrosion resistance.
Example 10
The embodiment provides a processing method of an Al-Zn-Mg- (Cu) alloy material, which comprises the following steps:
101, performing two-stage solution treatment on a 7075 aluminum alloy section with the thickness of 2.4mm, wherein the temperature of the first-stage solution treatment is 450 ℃, and the time of the solution treatment is 5 hours; the temperature of the second-stage solution treatment is 480 ℃, and the time of the solution treatment is 0.5 h; then directly quenching with water to obtain a quenched alloy;
102, carrying out isothermal heat preservation preaging treatment on the quenched alloy at 100 ℃, wherein the treatment time is 30 min;
103, carrying out isothermal treatment on the pre-aged section for 14 days at 15 ℃ (natural aging process);
104, according to a model of a required component, stretching the section, wherein the deformation is 5%;
and 105, performing simulated baking finish heat preservation treatment at 190 ℃/10min on the naturally aged and processed and molded section bar component in a forced air drying oven to obtain the Al-Zn-Mg- (Cu) alloy section bar component with high strength and corrosion resistance.
From the above examples 1 to 10, it can be seen from tables 1 and 7 that the 7075/7050 aluminum alloy sheet after solution quenching, pretreatment at 90-120 ℃ for 10-40min, and natural aging for 14 days has a significant increase in simulated paint baking, and has a higher microhardness after simulated baking. As can be seen from Table 2, the tensile strength and yield strength of the alloy are respectively improved by about 26MPa and 130MPa after simulated baking of the 7075 aluminum alloy plate which is subjected to isothermal treatment at 0 ℃ for 14 days by using the treatment method disclosed by the invention; after simulated baking of the 7075 aluminum alloy plate subjected to natural aging for 14 days at 25 ℃, the tensile strength and the yield strength of the alloy are respectively improved by about 17MPa and 121 MPa; after the 7075 aluminum alloy plate which is subjected to isothermal treatment at 37 ℃ for 14 days is subjected to simulated baking, the tensile strength of the alloy is reduced by about 9MPa, and the yield strength is improved by about 101 MPa. Although the 7075 aluminum alloy plate subjected to the isothermal treatment at 37 ℃ for 14 days in example 2 has relatively good performance after being baked, the 7075 aluminum alloy plate subjected to the isothermal treatment at 37 ℃ for 14 days has high strength, and is not beneficial to subsequent forming processing. In example 2, the 7075 alloy plate which is subjected to isothermal treatment at 0 ℃ and 25 ℃ for 14 days has larger increment of simulated baking finish, and the strength of the two plates in a baking state is similar, but the strength of the two plates after the two plates are subjected to isothermal treatment at 14 days is lower than that of the 7075 alloy plate which is subjected to isothermal treatment at 37 ℃ for 14 days, so that the deformation resistance in the forming and manufacturing process is relatively lower. The data in Table 3 show that the conductivity of the Al-Zn-Mg- (Cu) alloy in the simulated baking varnish state is larger than that in the T6 state, which indicates that the plate in the simulated baking varnish state has better corrosion resistance. As can be seen from Table 4, after the 7075 aluminum alloy plate is pre-aged at 100 ℃/30min and then subjected to natural aging treatment at room temperature for 14 days, the plastic strain ratio r value and the work hardening index n value of the 7075 aluminum alloy plate are relatively close to those of 6016-T4P and 6111-T4, while the 7050 aluminum alloy has higher self-alloying level than that of the 7075 aluminum alloy, so that the plastic strain ratio r value and the work hardening index n value of the 7050 aluminum alloy plate after the room-temperature isothermal treatment (natural aging) for 14 days are lower than those of the 7075 aluminum alloy plate in the same treatment state, and the 6016-T4P and 6111-T4 aluminum alloy plates have certain forming and processing capabilities. Therefore, the 100 ℃/30min → 0 ℃ aging/room temperature natural aging 14 days → 180 ℃/30min baking process can obviously improve the forming performance of the aging precipitation strengthening type Al-Zn-Mg- (Cu) alloy after natural aging and can obtain high baking hardening increment. The preparation method of the Al-Zn-Mg- (Cu) alloy plate member provided by the embodiment of the invention ensures that the high-strength Al-Zn-Mg- (Cu) alloy has excellent forming capability and is beneficial to forming and manufacturing in different modes, and high strength and good corrosion resistance are obtained by combining with subsequent baking treatment, so that the preparation method can be matched and applied to the industrial production flow of the existing vehicle member, and the high-efficiency and high-quality manufacturing of the high-strength Al-Zn-Mg- (Cu) alloy plate member is realized.
Although the Al-Zn-Mg- (Cu) alloys used in the embodiments of the present invention are typical grades of high strength aluminum alloys, such as 7075, 7050, the method of the present invention can be used for Al-Zn-Mg- (Cu) based alloy materials including but not limited to 7005, 7009, 7012, 7014, 7020, 7021, 7023, 7029, 7030, 7035, 7042, 7N01, 7075, 7050, 7150, 7178, 7449, 7081, 7278A, 7040, 7085, and the like. In addition, the process parameters are not limited to a plurality of specific processes selected in the embodiment, and the same effect can be achieved within the process parameter range.
The above description is only for the purpose of illustrating the preferred embodiments of the present invention and is not to be construed as limiting the invention, and any modifications, equivalents, improvements and the like that fall within the spirit and principle of the present invention are intended to be included therein.
Claims (9)
1. A processing method of an Al-Zn-Mg/Al-Zn-Mg-Cu alloy material is characterized by comprising the following steps:
step 1, carrying out high-temperature solid solution and quenching treatment on Al-Zn-Mg/Al-Zn-Mg-Cu alloy to obtain quenched alloy;
step 2, carrying out isothermal treatment on the quenched alloy at 70-140 ℃ for a preset time, and then carrying out air cooling or water cooling to room temperature;
step 3, carrying out isothermal treatment on the alloy at room temperature at-10-40 ℃ for a preset time to obtain a naturally aged alloy;
and 5, carrying out isothermal treatment on the treated alloy at the temperature of 160-190 ℃ for a preset time, and then carrying out air cooling to room temperature to obtain the Al-Zn-Mg/Al-Zn-Mg-Cu alloy material with high strength and corrosion resistance.
2. The processing method of an Al-Zn-Mg/Al-Zn-Mg-Cu-based alloy material according to claim 1, characterized by further comprising, between step 3 and step 5:
and 4, processing the alloy after natural aging into a member with a required shape to obtain the alloy with a specific shape.
3. The processing method of an Al-Zn-Mg/Al-Zn-Mg-Cu-based alloy material according to any one of claims 1 or 2, characterized in that the high-temperature solution treatment is performed by heating in a salt bath furnace, an air furnace or an aluminum alloy air cushion furnace; the quenching treatment adopts water quenching or gas quenching, and the cooling rate is 1-5 ℃/s.
4. The method for processing an Al-Zn-Mg/Al-Zn-Mg-Cu alloy material according to claim 3, wherein the high-temperature solution treatment in the step 1 is a primary solution treatment process, and the solution treatment schedule is as follows: the solution treatment temperature is 430-490 ℃, and the solution treatment time is 0.5-5 h.
5. The method for processing an Al-Zn-Mg/Al-Zn-Mg-Cu alloy material according to claim 3, wherein the high-temperature solution treatment in the step 1 is a two-stage solution treatment process, and the solution treatment schedule is as follows: the temperature of the first-stage solution treatment is 380-450 ℃, and the time of the solution treatment is 1-5 h; the temperature of the second stage solution treatment is 430-480 ℃, and the time of the solution treatment is 0.5-5 h.
6. The method of processing an Al-Zn-Mg/Al-Zn-Mg-Cu based alloy material according to claim 2, wherein said step 4 of processing a member into a desired shape with a deformation processing amount of 1 to 15%.
7. The method for processing an Al-Zn-Mg/Al-Zn-Mg-Cu based alloy material according to claim 6, wherein said processing in step 4 includes pre-stretching, punching, bending and bulging.
8. The method for processing an Al-Zn-Mg/Al-Zn-Mg-Cu based alloy material according to claim 1, wherein the Al-Zn-Mg/Al-Zn-Mg-Cu based alloy material is a plate or a pipe having a thickness of 0.5 to 4.0 mm.
9. The method for processing an Al-Zn-Mg/Al-Zn-Mg-Cu alloy material according to claim 1, wherein the predetermined time of the isothermal treatment in the step 2 is 10 to 120 min; the moderate temperature treatment time in the step 3 is 7-20 days; and in the step 5, the isothermal treatment is carried out for 10-50 min.
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