CN117324891A - Short-process hot forging forming process of pre-reinforced aluminum alloy - Google Patents
Short-process hot forging forming process of pre-reinforced aluminum alloy Download PDFInfo
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- 238000005728 strengthening Methods 0.000 claims abstract description 20
- 238000001816 cooling Methods 0.000 claims abstract description 14
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- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
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Abstract
The invention discloses a pre-reinforced aluminum alloy short-process hot forging forming process, which comprises the steps of preparing an aluminum alloy bar: forming a cast aluminum alloy into a billet; carrying out solution treatment and pre-strengthening treatment on the blank to obtain an aluminum alloy bar; heating the aluminum alloy bar to the temperature near the phase transition point, and preserving heat for a certain time; transferring the heated and insulated aluminum alloy blank into a forging die to be forged and formed to obtain a forging piece; and cooling the forging, trimming, and then machining to obtain the required aluminum alloy part. The beneficial effects of the invention are as follows: adopts the technological route of preparing aluminum alloy bar, heat preservation treatment before forging and forging deformation. The original three times of heating are reduced to one time of heating, the processing time of the aluminum alloy is greatly shortened, and the production period and the production cost are reduced; meanwhile, the types and the amounts of the precipitated phases of the aluminum alloy are regulated and controlled through different heat treatments and deformation in forging forming stages for different series of aluminum alloy materials, so that good formability is obtained.
Description
Technical Field
The invention relates to the technical field of aluminum alloy forging forming, in particular to a short-flow hot forging forming process of a pre-reinforced aluminum alloy.
Background
The aluminum alloy is widely applied to the fields of aerospace, navigation ships, vehicle traffic and the like due to light material, high strength and good processability. With the vigorous development of manufacturing industry and continuous progress of technology, the rapid development of forging industry is promoted, and with the application of lightweight technology, the inevitable trend of energy conservation and emission reduction of automobiles is more complied with, and the application of light metals such as aluminum and alloys thereof in the forging industry is also more extensive. Compared with castings and other workpieces, a better microstructure can be obtained, so that more uniform and reliable mechanical properties are obtained, and the strength, the safety and the plasticity are higher. As a result, there is an increasing demand for aluminum alloy forgings, especially for safety critical lightweight structures.
For heat-treatable reinforced aluminum alloys, there are work hardening and recovery, recrystallization and softening processes during the forming process, and in order to ensure the performance requirements of the alloy after forming, an artificial aging process is usually required; the conventional aluminum alloy forging process mainly comprises the following steps: firstly, preheating a blank before forging, then placing the heated blank into a die for forging and forming, and then carrying out solution treatment, quenching treatment and aging treatment on a forged piece so as to obtain higher mechanical properties. In order to ensure that the aluminum alloy blank is in a unidirectional state as much as possible so as to improve the plasticity of the aluminum alloy forging process and reduce the deformation resistance, multiple tests are required in the forging process to ensure that the aluminum alloy piece is in a proper forging temperature. The deformation resistance can be reduced and the plasticity can be improved by heating before forging, and the strength of the forging is improved by heat treatment after forging so as to meet the performance requirement of the product. Therefore, the traditional aluminum alloy forging process improves the actual production period (such as artificial aging of 7-series aluminum alloy for 24 hours) and the production cost, and generates excessive energy consumption.
Publication number WO2008059242 proposes a hot forming and cold die quenching process which mainly heats the blank to a solid Solution (SHT) temperature; then forming by using a cold die, and after forming, preserving the temperature of the workpiece in the die for 5-6S so as to rapidly quench; followed by an artificial ageing process. The method has high formability, rapid processing, and effective mechanical properties and forming accuracy. However, in order to obtain good formability, this process must be formed at a high holding temperature to increase the solid solubility. In addition, a subsequent artificial aging process is required to achieve the strength requirement, thus resulting in prolonged forming process, low efficiency and increased production costs.
The invention patent with publication number of CN112264498A proposes an aluminum alloy pre-strengthening hot stamping forming method, which can effectively improve the hot stamping production efficiency and ensure the product performance. However, the heat preservation time of different plate thicknesses is not reasonably described, so that a large amount of practice is required in actual production, and the heat preservation time has certain limitation.
The invention patent with publication number of CN112496218A proposes a technological method of pre-forging after solution treatment and then final forging after aging treatment, which can reduce the production period and improve the production efficiency. But is practically applied to isothermal forging and 6-series aluminum alloys, and has no universality.
In the invention patent with publication number of CN109182822A, a die forging method of high-performance 7-series aluminum alloy is proposed, a layer of titanium oxide is coated on the surface of carboxylated graphene by using an alcohol-thermal method, and a nano reinforcing phase is uniformly dispersed in a matrix by using cavitation and acoustic streaming effects of high-energy ultrasonic when the reinforcing phase is added to the matrix. The process has the advantages of complex preparation, long production period and certain limitation.
Disclosure of Invention
In view of the foregoing, it is necessary to provide a short-flow hot forging process for pre-reinforced aluminum alloy, which is used for solving the technical problems of long production period and large energy consumption caused by repeated heating in the conventional aluminum alloy die forging process.
In order to achieve the above purpose, the invention provides a short-flow hot forging forming process of a pre-reinforced aluminum alloy, which comprises the following steps:
s1, preparing an aluminum alloy bar: forming a cast aluminum alloy into a billet; then carrying out solution treatment and pre-strengthening treatment on the blank to obtain an aluminum alloy bar;
s2, heating the aluminum alloy bar to the temperature near the phase transition point, and preserving heat for a certain time;
s3, transferring the heated and insulated aluminum alloy blank into a forging die to be forged and formed to obtain a forging;
and S4, cooling the forging, trimming, and then machining to obtain the required aluminum alloy part.
In some embodiments, in the step S1, the specific method for forming the cast aluminum alloy into the blank is as follows: melting aluminum alloy by using melting furnace equipment, and controlling the melting furnace equipment to be constant temperature; pouring the smelted metal into a forming die to finish forming work, and applying ultrasonic waves and electromagnetic waves to molten aluminum during pouring to obtain a blank.
In some embodiments, in the step S1, the specific steps of performing solution treatment and pre-strengthening treatment on the blank include:
s11, carrying out solid solution treatment on the blank to enable the blank to be processed into a W state;
s12, artificially aging the W-state blank.
In some embodiments, in the step S11, the temperature of the blank subjected to the solution treatment is determined according to the model of the blank, specifically:
when the billet is a 7xxx aluminum alloy, the temperature of the solution treatment is from 460 ℃ to 499 ℃;
when the blank is a 6xxx aluminum alloy, the temperature of the solution treatment is 516 ℃ to 579 ℃;
when the billet is a 2xxx aluminum alloy, the temperature of the solution treatment is from 460 ℃ to 550 ℃.
In some embodiments, in the step S11, the time for performing the solution treatment on the blank is determined by the following formula:
t＝(t 0 +t 1 E)H+t c
wherein t is the time of solid solution treatment of the blank, t 0 For heat penetration time t 1 The nominal solid solution time is given, and H is the maximum thickness of the blank; t is t c Is the basic heat preservation time; e is a relevant strengthening coefficient; i is the metallurgical quality coefficient of the cast ingot; a is an alloying coefficient; w is the mechanical property direction coefficient; v is a variety coefficient, G is a grain size coefficient, D is a state coefficient, N is an aging class coefficient, lambda is a deformation coefficient, K is a deformation complementCompensation coefficient.
In some embodiments, in the step S12, the method for determining the temperature for artificially aging the W-state blank is: firstly, determining the temperature corresponding to the exothermic peak position precipitated in the GP zone of the blank according to the model of the blank, wherein the temperature is the temperature for artificially aging the W-state blank, and the specific temperature is as follows:
when the blank is a 7xxx aluminum alloy, the temperature of the artificial aging is 70-120 ℃;
when the blank is a 6xxx aluminum alloy, the temperature of the artificial aging is 110-160 ℃;
when the billet is a 2xxx aluminum alloy, the temperature of the artificial ageing is 60 to 180 ℃.
In some embodiments, in the step S2, the aluminum alloy bar is heated to a temperature near the transformation point, and is kept for a certain period of time, wherein:
the heat preservation temperature is determined according to the model of the blank, and specifically comprises the following steps:
when the blank is 7xxx aluminum alloy, the heat preservation temperature is 160-230 ℃;
when the blank is a 6xxx aluminum alloy, the heat preservation temperature is 160-230 ℃;
when the blank is a 2xxx aluminum alloy, the heat preservation temperature is 220-350 ℃;
the heat preservation time is determined according to the diameter of the blank (namely the maximum thickness of the blank), and the determination method is the same as a solid solution heating time formula.
In some embodiments, in the step S3, the heated and heat-preserved aluminum alloy blank is transferred to a forging die to be forged and formed to obtain a forging, which specifically includes the following steps:
s31, transferring the heated and insulated aluminum alloy blank into a forging die;
s32, controlling the overall temperature in the forging die through a temperature control module of the forging die, so that the overall temperature in the forging die is kept near the phase transition point temperature of the aluminum alloy blank;
s33, arranging cooling devices at the positions with larger wall thickness and severe deformation of the aluminum alloy blank in the forging die, and preventing the temperatures at the positions with larger wall thickness and severe deformation from exceeding the phase transition point temperature and the overburning temperature of the aluminum alloy blank;
s34, setting a temperature compensating device at the final flow molding position of the aluminum alloy blank in the forging die, and preventing the temperature of the final flow molding position from being lower than the phase change point temperature of the aluminum alloy blank.
In some embodiments, in the step S33, the cooling temperature set by the cooling device is:
wherein DeltaT 1 The temperature of the cooling device is set, and eta is the heat conversion coefficient of the work; w (W) 1 The deformation work is performed on the aluminum alloy blank in a unit area where the wall thickness is large and the deformation is severe; ρ is the density of the material; c is the specific heat capacity of the material.
In some embodiments, in the step S34, the temperature raising temperature set by the temperature compensating device is:
wherein DeltaT 2 The heating temperature is set for the temperature supplementing device, and eta is the heat and power conversion coefficient; w (W) 2 Deformation work per unit area at the final flowing filling position of the aluminum alloy blank; ρ is the density of the material; c is the specific heat capacity of the material.
Compared with the prior art, the technical scheme provided by the invention has the beneficial effects that: adopts the technological route of preparing aluminum alloy bar, heat preservation treatment before forging and forging deformation. The original three times of heating are reduced to one time of heating, the processing time of the aluminum alloy is greatly shortened, and the production period and the production cost are greatly reduced on the premise of fully meeting the performance requirements of the product; meanwhile, the types and the quantity of the precipitated phases of the aluminum alloy are regulated and controlled through different heat treatments and deformation in forging forming stages for different series of aluminum alloy materials, so that good formability is obtained, and rapid hot forming is realized.
Drawings
FIG. 1 is a schematic flow diagram of one embodiment of a short-flow hot forging process for pre-strengthened aluminum alloys provided by the present invention;
FIG. 2 is a schematic flow chart of the steps in FIG. 1;
FIG. 3 is a schematic flow chart of the steps in FIG. 1;
FIG. 4 is a flow chart of conventional aluminum alloy forging forming and a flow chart comparison of the aluminum alloy short-flow hot forging forming process provided by the invention;
FIG. 5 is a schematic diagram showing the variation of the processing temperature in the conventional aluminum alloy forging forming process flow;
FIG. 6 is a schematic diagram showing the change of the processing temperature of the aluminum alloy short-flow hot forging process provided by the invention;
FIG. 7 is a schematic view showing microstructure changes in the processing course of the aluminum alloy short-flow hot forging forming process provided by the invention;
FIG. 8 is a pictorial view of an aluminum alloy member utilizing the aluminum alloy short-flow hot forging process of the present invention;
FIG. 9 is a schematic view of the aluminum alloy member of FIG. 8 in a sampling position.
Detailed Description
Preferred embodiments of the present invention will now be described in detail with reference to the accompanying drawings, which form a part hereof, and together with the description serve to explain the principles of the invention, and are not intended to limit the scope of the invention.
Example 1
Referring to fig. 1, the invention provides a pre-reinforced aluminum alloy short-flow hot forging forming process, which is suitable for 7075 aluminum alloy simple pieces which can be formed by only one die forging, and comprises the following steps:
s1, preparing an aluminum alloy bar: forming a cast aluminum alloy into a billet; then carrying out solution treatment and pre-strengthening treatment on the blank to obtain an aluminum alloy bar;
in the step S1, the specific method for manufacturing the cast aluminum alloy into the blank comprises the following steps: melting aluminum alloy by using melting furnace equipment, and controlling the melting furnace equipment to be constant temperature; pouring the smelted metal into a finished productAnd (3) finishing forming work in the die, and applying ultrasonic waves and electromagnetic waves to the aluminum liquid during pouring to obtain a blank. In the embodiment, melting materials by using melting furnace equipment, and controlling the temperature of the melting equipment to be 760 ℃; the frequency of the ultrasonic wave applied to the aluminum liquid is 45-60 kHz; coupling parameters of electromagnetic waves applied to molten aluminum: the magnetic induction intensity is 2.5T, and the current density is 40A/mm 2 ；
Referring to fig. 2, in the step S1, the specific steps of performing solution treatment and pre-strengthening treatment on the blank include:
s11, carrying out solid solution treatment on the blank to enable the blank to be processed into a W state;
the temperature for carrying out solution treatment on the blank is determined according to the model of the blank, and specifically comprises the following steps:
when the billet is a 7xxx aluminum alloy, the temperature of the solution treatment is from 460 ℃ to 499 ℃;
when the blank is a 6xxx aluminum alloy, the temperature of the solution treatment is 516 ℃ to 579 ℃;
when the billet is a 2xxx aluminum alloy, the temperature of the solution treatment is from 460 ℃ to 550 ℃.
The time for solution treatment of the blank is determined by the following formula:
t＝(t 0 +t 1 E)H+t c
wherein t is the time of carrying out solid solution treatment on the blank, and the heat penetration speed of the air furnace is 1.5min/mm; t is t 0 For heat penetration time t 1 For the nominal solid solution time, 1min/mm is usually taken; h is the maximum thickness of the blank; t is t c For basic heat preservation time, usually 25min; e is a relevant strengthening coefficient; i is the metallurgical quality coefficient of the cast ingot, when the metallurgical quality of the cast ingot reaches the following 4 standards, namely (1) the hydrogen content of the aluminum alloy cast ingot reaches less than 0.15mL per 100 gAl; (2) the cast ingot is checked by an oxide film to reach the 1-level standard; (3) checking the cast ingot to be 1 grade in low power; (4) homogenizing, wherein I is 1. When the metallurgical quality of the cast ingot does not reach the 4 standards, 1.2 is taken as I; a is an alloying coefficient, and when the sum of the reinforcing elements (1) is less than 3%, A is 3.0; (2) when the sum of the strengthening elements is 3% -6%, A is 3.3; (2) when the sum of the reinforcing elements is 6.1% -9%, A is 3.6; (2) when the sum of 0 strengthening elements is more than 9%, A is 4; w is a mechanical property direction coefficient, and the mechanical property direction coefficient is divided into 3 types (2)1 is 1.0 in the longitudinal direction through experiments; (2) 2 is 2.0 in the transverse direction; (2) 6 the axial direction is 3.0; therefore, when the requirements of mechanical property anisotropism are different, the solid solution heat preservation time should be different; v is a variety coefficient, (2)4 casting is 4; (2) 5, taking 2.8 parts of forgings, die forgings and hot-rolled thick plates; (3) taking 1.6 parts of cold-rolled sheet; (4) taking a coated aluminum plate and an extruded material as 1.4, wherein G is a grain size coefficient, (2)7 is 1 for a product with no requirement on grain size; (2) 8, taking 0.7 of a product requiring fine crystals; (3) taking 0.3 as a product with the coarse crystal ring smaller than 5mm, wherein D is a state coefficient, and taking 1.1 as the material (1) is an annealing material; (2) when the material is a thermal deformation material, D is 1.0; (3) when the material is cold deformation material, D is 0.9, N is an aging class coefficient, (1) when artificial aging is adopted, N is 1; (2) when natural aging is adopted, N is 0.9, lambda is a deformation coefficient, the deformation coefficient is almost inversely proportional to the solid solution heat preservation time, but when the deformation coefficient lambda is larger than 10, product grains are fully crushed to form a complete deformation structure, when the deformation coefficient is larger than 10, K is a deformation compensation coefficient, and when the deformation modes are casting, thermal deformation and cold deformation, K is 1,1.2,1.5 respectively. When the deformation coefficient is smaller than 10, the deformation compensation coefficient is added with 0.1 every 1 reduction. Thus, the solid solution time according to the above formula was 66 minutes for a cast bar having a diameter of 8mm by a length of 15 mm.
S12, artificially aging the W-state blank.
The method for determining the temperature of artificially aging the W-state blank comprises the following steps: firstly, determining the temperature corresponding to the exothermic peak position precipitated in the GP zone of the blank according to the model of the blank, wherein the temperature is the temperature for artificially aging the W-state blank, and the specific temperature is as follows:
when the blank is a 7xxx aluminum alloy, the temperature of the artificial aging is 70-120 ℃;
when the blank is a 6xxx aluminum alloy, the temperature of the artificial aging is 110-160 ℃;
when the billet is a 2xxx aluminum alloy, the temperature of the artificial ageing is 60 to 180 ℃.
In this example, the time for artificial ageing was 12 hours.
It should be noted that the process of preparing the aluminum alloy bar in the step S1 is actually completed by an aluminum alloy bar supplier, and only the relevant process parameters and the process flow in the step S1 need to be sent to the aluminum alloy bar supplier, so that the aluminum alloy bar meeting the requirements can be purchased.
S2, heating the aluminum alloy bar to the temperature near the phase transition point, and preserving heat for a certain time;
in the step S2, the aluminum alloy bar is heated to the vicinity of the phase transition point temperature, and is preserved for a certain time, wherein:
the heat preservation temperature is determined according to the model of the blank, and specifically comprises the following steps:
when the blank is 7xxx aluminum alloy, the heat preservation temperature is 160-230 ℃;
when the blank is a 6xxx aluminum alloy, the heat preservation temperature is 160-230 ℃;
when the blank is a 2xxx aluminum alloy, the heat preservation temperature is 220-350 ℃;
the heat preservation time is determined according to the diameter of the blank (namely the maximum thickness of the blank), and the determination method is the same as a solid solution heating time formula.
In the embodiment, when the material is 7075 aluminum alloy bar with the diameter of 8mm and the length of 10mm, the heat preservation temperature is 200 ℃ after the processing is finished, and the heat preservation time is 5 minutes;
s3, transferring the heated and insulated aluminum alloy blank into a forging die to be forged and formed to obtain a forging;
referring to fig. 3, in the step S3, the heated and insulated aluminum alloy blank is transferred to a forging die to be forged to obtain a forging, which specifically includes the following steps:
s31, transferring the heated and insulated aluminum alloy blank into a forging die;
s32, controlling the overall temperature in the forging die through a temperature control module of the forging die, so that the overall temperature in the forging die is kept near the phase transition point temperature of the aluminum alloy blank;
s33, arranging cooling devices at the positions with larger wall thickness and severe deformation of the aluminum alloy blank in the forging die, and preventing the temperatures at the positions with larger wall thickness and severe deformation from exceeding the phase transition point temperature and the overburning temperature of the aluminum alloy blank;
wherein, the cooling temperature that the heat sink set for is:
wherein DeltaT 1 The temperature of the cooling device is set, and eta is the heat conversion coefficient of the work; w (W) 1 The deformation work is performed on the aluminum alloy blank in a unit area where the wall thickness is large and the deformation is severe; ρ is the density of the material; c is the specific heat capacity of the material. In the present embodiment, deltaT 1 Is 20 ℃.
S34, setting a temperature compensating device at the final flow molding position of the aluminum alloy blank in the forging die, and preventing the temperature of the final flow molding position from being lower than the phase change point temperature of the aluminum alloy blank.
Wherein, the temperature rise temperature that the temperature compensating device set for is:
wherein DeltaT 2 The heating temperature is set for the temperature supplementing device, and eta is the heat and power conversion coefficient; w (W) 2 Deformation work per unit area at the final flowing filling position of the aluminum alloy blank; ρ is the density of the material; c is the specific heat capacity of the material. In the present embodiment, deltaT 2 Is 20 ℃.
And S4, cooling the forging, trimming, and then machining to obtain the required aluminum alloy part.
Tensile samples are cut on the forged and formed parts, the mechanical properties of the forged and formed parts are tested by unidirectional tensile test, the tensile strength of the forged and formed parts can reach 578MPa, and the yield strength of the forged and formed parts can reach 511MPa (shown in table 1).
Example 2
Example 2 provides a short-flow hot forging forming process of a pre-reinforced aluminum alloy, which is suitable for 7075 aluminum alloy complex parts which need to be subjected to die forging for multiple times, and the specific method is similar to example 1, and the different process conditions are as follows: and in the forging forming process, multiple die forging is carried out, and in the multiple die forging process, the temperature of the workpiece is kept by utilizing a temperature control device when the forging is transferred between dies.
Tensile samples are cut on the forged and formed parts, the mechanical properties of the forged and formed parts are tested by unidirectional tensile test, the tensile strength of the forged and formed parts can reach 553MPa, and the yield strength of the forged and formed parts can reach 501MPa (shown in table 1).
Example 3
Embodiment 3 provides a short-flow hot forging forming process of a pre-reinforced aluminum alloy, which is suitable for a 6082 aluminum alloy simple piece which can be formed by only one die forging, and the specific method is similar to embodiment 1, and the different process conditions are as follows: the solid solution heat preservation temperature is 516-579 ℃, the heat preservation time is 60 minutes, the pre-aging temperature is 160 ℃, and the heat preservation time is 4 hours.
And cutting a tensile sample from the forged part, and testing the mechanical property of the forged part after shaping by unidirectional tensile test, wherein the tensile strength of the forged part can reach 296MPa and the yield strength of the forged part can reach 255MPa (shown in table 1) by taking the average value of a plurality of tensile samples.
Example 4
Embodiment 4 provides a short-flow hot forging forming process of a pre-reinforced aluminum alloy, which is suitable for 6082 aluminum alloy complex parts which need to be subjected to die forging for multiple times, and the specific method is similar to embodiment 3, and the different process conditions are as follows: and in the forging forming process, multiple die forging is carried out, and in the multiple die forging process, the temperature of the workpiece is kept by utilizing a temperature control device when the forging is transferred between dies.
Tensile samples are cut on the forged and formed parts, the mechanical properties of the forged and formed parts are tested by unidirectional tensile test, the tensile strength of the forged and formed parts can reach 287MPa, and the yield strength of the forged and formed parts can reach 247MPa (shown in table 1).
Example 5
Embodiment 5 provides a short-flow hot forging forming process of a pre-reinforced aluminum alloy, which is suitable for 2024 aluminum alloy simple pieces which can be formed by only one die forging, and the specific method is the same as that of embodiment one, and different process conditions are as follows: the solid solution heat preservation temperature is 460-550 ℃, the heat preservation is carried out for 60 minutes, the pre-aging temperature is 75 ℃, and the heat preservation is carried out for 12 hours.
Tensile samples are cut on the forged and formed parts, the mechanical properties of the forged and formed parts are tested by unidirectional tensile test, the tensile strength of the forged and formed parts can reach 450MPa, and the yield strength of the forged and formed parts can reach 355MPa (shown in table 1).
Example 6
Embodiment 6 provides a short-flow hot forging forming process of a pre-reinforced aluminum alloy, which is suitable for 2024 aluminum alloy complex parts which are required to be subjected to die forging for multiple times, and the specific method is the same as that in embodiment 5, and the different process conditions are as follows: and in the forging forming process, multiple die forging is carried out, and in the multiple die forging process, the temperature of the workpiece is kept by utilizing a temperature control device when the forging is transferred between dies.
Tensile samples are cut on the forged and formed parts, the mechanical properties of the forged and formed parts are tested by unidirectional tensile test, the tensile strength of the forged and formed parts can reach 445MPa, and the yield strength of the forged and formed parts can reach 350MPa (shown in table 1).
Table 1: mechanical properties of forgings of different embodiments
The beneficial effects of the invention are as follows:
the traditional die forging process route of the aluminum alloy is heating and heat preservation, forging deformation, cooling, solid solution treatment and aging treatment (as shown in fig. 4 and 5), and the process route adopted by the invention is that the aluminum alloy bar is prepared, heat preservation treatment before forging and forging deformation. The original three times of heating are reduced to one time of heating (as shown in fig. 6 and 7), the processing time is reduced to a few minutes from the original twenty-four hours, and the production period and the production cost are greatly reduced on the premise of fully meeting the performance requirements of the product.
In addition, the types and the amounts of the precipitated phases of the aluminum alloy are regulated and controlled through different heat treatments and deformation in forging forming stages for different series of aluminum alloy materials, so that good formability is obtained, and the required product is manufactured. The internal precipitated phase can be further evolved in a mode of underaging combined with forging deformation, so that the peak aging effect is achieved, the transformation of the precipitated phase is achieved through deformation instead of traditional coarsening, a large number of nano-layer errors are generated in the deformation process, the strength of the formed component is further improved through the reinforcing effect of the nano-layer errors, and the mechanical property of the formed component is superior to that of the T6-state aluminum alloy.
Specifically, the precipitation strengthening phase sequence of the 2000 series aluminum alloy is as follows: SSS→GP region→θ "→θ' →θ (CuAl) 2 ) The precipitation strengthening phase sequence of 6000 series aluminum alloy is as follows: SSS→GP region→β "→β' →β (Mg 2 Si), 7000 series aluminum alloy precipitation strengthening phases are in the order: SSS→GPI region (GPI/GPI) →η' →η (MgZn) 2 ) Wherein SSS is a supersaturated solid solution, θ "and β" are matrix co-ordinates, θ ', β ', η ' are metastable precipitated phases of the matrix semi-co-ordinates, η is equilibrium precipitated phases of non-co-ordinates with the matrix (MgZn 2 ). As the temperature increases, the size of the strengthening phase increases and the non-coherent phase gradually replaces the semi-coherent phase, resulting in a substantial decrease in strength. Therefore, in the solid solution treatment and pre-strengthening treatment stage in the step S1 and in the heating and heat preservation process in the step S2, the type and the number of the precipitated phases can be further controlled by controlling the temperature and the time, so that a large number of phases which are semi-coherent with the matrix are obtained, the precipitation strengthening effect is ensured, and the part with the performance meeting the requirement and good mechanical property is obtained.
The technology of the invention regulates the types and the quantity of the aluminum alloy precipitated phases through the deformation of different heat treatment and processing forming stages, ensures the precipitation strengthening effect, realizes the rapid thermal forming, can reduce the production period and the production cost, reduces the energy consumption and improves the production efficiency. Referring to fig. 8, fig. 9 is a schematic diagram of a sampling position of an aluminum alloy member obtained by the aluminum alloy short-flow hot forging process according to the present invention.
The foregoing is only a preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any changes or substitutions easily contemplated by those skilled in the art within the technical scope of the present invention should be included in the scope of the present invention.
Claims (10)
1. A pre-reinforced aluminum alloy short-flow hot forging forming process is characterized by comprising the following steps:
s1, preparing an aluminum alloy bar: forming a cast aluminum alloy into a billet; then carrying out solution treatment and pre-strengthening treatment on the blank to obtain an aluminum alloy bar;
s2, heating the aluminum alloy bar to the temperature near the phase transition point, and preserving heat for a certain time;
s3, transferring the heated and insulated aluminum alloy blank into a forging die to be forged and formed to obtain a forging;
and S4, cooling the forging, trimming, and then machining to obtain the required aluminum alloy part.
2. The short-flow hot forging process for a pre-strengthened aluminum alloy according to claim 1, wherein in the step S1, the specific method for forming the cast aluminum alloy into the blank is as follows: melting aluminum alloy by using melting furnace equipment, and controlling the melting furnace equipment to be constant temperature; pouring the smelted metal into a forming die to finish forming work, and applying ultrasonic waves and electromagnetic waves to molten aluminum during pouring to obtain a blank.
3. The short-process hot forging process for a pre-strengthened aluminum alloy according to claim 1, wherein in the step S1, the specific steps of solution treatment and pre-strengthening treatment of the blank include:
s11, carrying out solid solution treatment on the blank to enable the blank to be processed into a W state;
s12, artificially aging the W-state blank.
4. The short-process hot forging process for a pre-strengthened aluminum alloy according to claim 3, wherein in the step S11, the temperature of the blank subjected to the solution treatment is determined according to the type of the blank, specifically:
when the billet is a 7xxx aluminum alloy, the temperature of the solution treatment is from 460 ℃ to 499 ℃;
when the blank is a 6xxx aluminum alloy, the temperature of the solution treatment is 516 ℃ to 579 ℃;
when the billet is a 2xxx aluminum alloy, the temperature of the solution treatment is from 460 ℃ to 550 ℃.
5. A short-flow hot forging process for a pre-strengthened aluminum alloy according to claim 3, wherein in step S11, the time for solution-treating the blank is determined by the following formula:
t＝(t 0 +t 1 E)H+t c
wherein t is the time of solid solution treatment of the blank, t 0 For heat penetration time t 1 The nominal solid solution time is given, and H is the maximum thickness of the blank; t is t c Is the basic heat preservation time; e is a relevant strengthening coefficient; i is the metallurgical quality coefficient of the cast ingot; a is an alloying coefficient; w is the mechanical property direction coefficient; v is a variety coefficient, G is a grain size coefficient, D is a state coefficient, N is an aging class coefficient, lambda is a deformation coefficient, and K is a deformation compensation coefficient.
6. The short-process hot forging process for a pre-strengthened aluminum alloy according to claim 3, wherein in the step S12, the determination method of the temperature for artificially aging the W-state blank is as follows: firstly, determining the temperature corresponding to the exothermic peak position precipitated in the GP zone of the blank according to the model of the blank, wherein the temperature is the temperature for artificially aging the W-state blank, and the specific temperature is as follows:
when the blank is a 7xxx aluminum alloy, the temperature of the artificial aging is 70-120 ℃;
when the blank is a 6xxx aluminum alloy, the temperature of the artificial aging is 110-160 ℃;
when the billet is a 2xxx aluminum alloy, the temperature of the artificial ageing is 60 to 180 ℃.
7. The short-process hot forging process for a pre-strengthened aluminum alloy according to claim 5, wherein in the step S2, the aluminum alloy bar is heated to a temperature near a transformation point, and is kept for a certain period of time, wherein:
the heat preservation temperature is determined according to the model of the blank, and specifically comprises the following steps:
when the blank is 7xxx aluminum alloy, the heat preservation temperature is 160-230 ℃;
when the blank is a 6xxx aluminum alloy, the heat preservation temperature is 160-230 ℃;
when the blank is a 2xxx aluminum alloy, the heat preservation temperature is 220-350 ℃;
the heat preservation time is determined according to the diameter of the blank, and the determination method is the same as a solid solution heating time formula.
8. The short-process hot forging forming process of the pre-reinforced aluminum alloy according to claim 1, wherein in the step S3, the heated and heat-preserved aluminum alloy blank is transferred to a forging die for forging forming to obtain a forging, and the method specifically comprises the following steps:
s31, transferring the heated and insulated aluminum alloy blank into a forging die;
s32, controlling the overall temperature in the forging die through a temperature control module of the forging die, so that the overall temperature in the forging die is kept near the phase transition point temperature of the aluminum alloy blank;
s33, arranging cooling devices at the positions with larger wall thickness and severe deformation of the aluminum alloy blank in the forging die, and preventing the temperatures at the positions with larger wall thickness and severe deformation from exceeding the phase transition point temperature and the overburning temperature of the aluminum alloy blank;
s34, setting a temperature compensating device at the final flow molding position of the aluminum alloy blank in the forging die, and preventing the temperature of the final flow molding position from being lower than the phase change point temperature of the aluminum alloy blank.
9. The short-process hot forging process for a pre-strengthened aluminum alloy according to claim 8, wherein in the step S33, the temperature reduction set by the temperature reduction device is as follows:
wherein DeltaT 1 The temperature of the cooling device is set, and eta is the heat conversion coefficient of the work; w (W) 1 The deformation work is performed on the aluminum alloy blank in a unit area where the wall thickness is large and the deformation is severe; ρ is the density of the material; c is the specific heat capacity of the material.
10. The short-process hot forging process for a pre-strengthened aluminum alloy according to claim 8, wherein in the step S34, the temperature raising temperature set by the temperature compensating device is:
wherein DeltaT 2 The heating temperature is set for the temperature supplementing device, and eta is the heat and power conversion coefficient; w (W) 2 Deformation work per unit area at the final flowing filling position of the aluminum alloy blank; ρ is the density of the material; c is the specific heat capacity of the material.
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