CN115418534B - 8090 aluminum lithium alloy fine-grain plate and preparation method thereof - Google Patents
8090 aluminum lithium alloy fine-grain plate and preparation method thereof Download PDFInfo
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- 229910001148 Al-Li alloy Inorganic materials 0.000 title claims abstract description 68
- JFBZPFYRPYOZCQ-UHFFFAOYSA-N [Li].[Al] Chemical compound [Li].[Al] JFBZPFYRPYOZCQ-UHFFFAOYSA-N 0.000 title claims abstract description 68
- 239000001989 lithium alloy Substances 0.000 title claims abstract description 68
- 238000002360 preparation method Methods 0.000 title claims abstract description 20
- 238000010438 heat treatment Methods 0.000 claims abstract description 152
- 238000005096 rolling process Methods 0.000 claims abstract description 87
- 238000005097 cold rolling Methods 0.000 claims abstract description 21
- 238000005098 hot rolling Methods 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 10
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- 238000005266 casting Methods 0.000 claims description 35
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- 229910045601 alloy Inorganic materials 0.000 claims description 14
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- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 3
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- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C21D8/0231—Warm rolling
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- C21—METALLURGY OF IRON
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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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
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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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
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Abstract
The invention belongs to the technical field of aluminum lithium alloy processing, and particularly relates to an 8090 aluminum lithium alloy fine-grain plate and a preparation method thereof. The invention improves the comprehensive performance of the aluminum-lithium alloy by combining hot rolling, heat treatment and cold rolling, can effectively solve the problems of coarse plate grains and uneven structure and mechanical property after rolling in the 8090 aluminum-lithium alloy production process, and further improves the industrial application value thereof. The 8090 aluminum lithium alloy fine-grain plate is prepared from an aluminum lithium alloy cast ingot, and the aluminum lithium alloy cast ingot comprises the following components in percentage by mass: cu:1.0 to 1.6%, li: 2.2-2.7%, mg: 0.6-1.3%, zr: 0.04-0.16%, and the balance of Al and unavoidable impurity elements. The aluminum lithium alloy plate provided by the invention has the advantages that the crystal grains are greatly refined, and the original fibrous structure is improved, so that the problem of nonuniform structure and mechanical property after rolling is solved, and the industrial application level of the 8090 aluminum lithium alloy is further improved.
Description
Technical Field
The invention belongs to the technical field of aluminum lithium alloy processing, and particularly relates to an 8090 aluminum lithium alloy fine-grain plate and a preparation method thereof.
Background
The 8090 aluminum-lithium alloy has the characteristics of low density, high specific stiffness, high specific strength, high elastic modulus and the like, can reduce the weight by 10-20% when being used for replacing common aluminum alloy, is suitable for the field of military industry, the field of 3C digital codes and the like, is commonly used for manufacturing fine structural members, and has good application prospect. The mechanical property, corrosion resistance, fracture mode and the like of the 8090 aluminum-lithium alloy have great relation with the structure of the aluminum-lithium alloy. To obtain higher strength and higher plasticity, the preparation should be performed mainly by the structure of uncrystallized crystal grains or fine recrystallized crystal grains, however, coarse rolling crystal grains appearing in the preparation process easily cause the material performance to show obvious directivity, and the local performance of the plate is uneven. It can be seen that it is very necessary to control the grain structure of the aluminum lithium alloy.
In order to obtain a fine grain structure, a reasonable thermomechanical treatment must be performed before the parts are manufactured from the 8090 aluminum lithium alloy. Although the traditional thermomechanical treatment can produce a plate with higher surface quality by a simple preheating and rolling mode, and meets the requirement of longitudinal mechanical property, the traditional preheating and rolling method can not crush the rolled fibrous tissue and promote effective recrystallization, and finally the rolled tissue presents a fibrous shape, so that the tissue and mechanical property of the aluminum-lithium alloy plate presents obvious orientation.
Based on the method, the rolling method in the preparation process of the 8090 aluminum lithium alloy is optimized, so that the crystallization mode and the crystal grain shape are changed, the comprehensive mechanical property, the corrosion resistance and the fracture property of the aluminum lithium alloy are improved, the application of the aluminum lithium alloy is effectively expanded, and the light weight level of raw materials in the fields of precision electronic parts and the like is improved.
Disclosure of Invention
The invention aims to overcome the defects in the prior art, and provides an 8090 aluminum lithium alloy fine-grain plate and a preparation method thereof, which can improve the comprehensive performance of aluminum lithium alloy in a hot rolling and cold rolling combined mode, effectively solve the problems of coarse plate grains and uneven structure and mechanical property after rolling in the production process of the 8090 aluminum lithium alloy, and further improve the industrial application value thereof.
The invention also provides application of the 8090 aluminum lithium alloy fine-grain plate.
Based on the above purpose, the invention adopts the following technical scheme:
the 8090 aluminum lithium alloy fine-grain plate is prepared from the following components in percentage by mass by adopting an aluminum lithium alloy cast ingot: cu:1.0 to 1.6%, li: 2.2-2.7%, mg: 0.6-1.3%, zr: 0.04-0.16%, and the balance of Al and unavoidable impurity elements; the content of each impurity element is Cr: less than or equal to 0.1, mn: less than or equal to 0.2 percent, zn: less than or equal to 0.25 percent, si: less than or equal to 0.2 percent, fe: less than or equal to 0.3 percent, ti: less than or equal to 0.1 percent.
The preparation method of the 8090 aluminum lithium alloy fine-grain plate comprises the following steps:
(1) Vacuum casting and forging: proportioning according to the mass percentage of each component in the alloy, vacuumizing to below 10Pa in a heating furnace, performing vacuum casting to obtain an ingot, and forging;
(2) And (3) hot rolling: heating the forged cast ingot to 400-450 ℃, preserving heat for 8-14 h, and then carrying out hot rolling at the temperature to obtain a plate, wherein the rolling time is controlled within 30 min;
(3) Primary solution heat treatment: heating the rolled plate to 500-540 ℃, preserving heat for 2-4 hours, and performing water cooling quenching;
(4) Isothermal rolling: heating the plate subjected to primary solid solution to 150-250 ℃, preserving heat for 6-8 hours, and then carrying out isothermal rolling at the temperature, wherein the rolling time is controlled within 30 min;
(5) Overaging heat treatment: directly heating the sheet material subjected to isothermal rolling to 300-400 ℃, and carrying out heat preservation for 36-48 hours for overaging heat treatment;
(6) Cold rolling and annealing: cold rolling the plate subjected to overaging heat treatment at room temperature for 30 min; after cold rolling, heating the plate to 450-500 ℃, and preserving heat for 12-24 hours for recrystallization annealing;
(7) And (3) secondary solution heat treatment: heating the plate subjected to recrystallization annealing to 500-540 ℃, preserving heat for 3-5 hours for solution heat treatment, and then performing water cooling quenching;
(8) And (3) secondary aging heat treatment: and heating the plate subjected to the secondary solution heat treatment to 150-170 ℃, preserving heat for 15-30 hours, performing aging heat treatment, and then air-cooling to room temperature to obtain a final product.
Specifically, in the step (1), the casting process is as follows: and (3) after the alloy raw materials are proportioned, placing the alloy raw materials into a heating furnace, vacuumizing to less than 10Pa, heating to 200 ℃, then charging 1000Pa of argon gas to increase partial pressure in the furnace, heating to a smelting temperature of not more than 850 ℃ to start refining, standing after refining, and casting to obtain an ingot.
Specifically, in the step (1), the forging process is as follows: heating the ingot along with the furnace, heating to 400-450 ℃, preserving heat for 10-16 h after the furnace temperature is stable, forging at the temperature, controlling the forging time within 40min, and performing air cooling to room temperature after forging, wherein the upsetting deformation is 30-50% during forging.
Specifically, in the step (2), the single-pass deformation amount of hot rolling is controlled to be 15-30%, the total deformation amount is controlled to be 70-80%, and the plate with the size of 60 multiplied by 600 multiplied by 2100mm is obtained.
Specifically, in the step (3), the quenching transfer time is controlled within 15 s.
Specifically, in the step (4), the single-pass deformation amount of isothermal rolling is controlled to be 10-20%, the total deformation amount is controlled to be 50-70%, and the plate with the size of 30 multiplied by 600 multiplied by 4200mm is obtained.
Specifically, in the step (6), the single-pass deformation amount of cold rolling is controlled to be 5-10%, the total deformation amount is controlled to be 10-20%, and the plate with the size of 25 multiplied by 600 multiplied by 5000mm is obtained.
Specifically, in the step (7), the quenching transfer time is controlled within 15 s.
Specifically, in the step (7), the plate subjected to the secondary solution heat treatment is prestretched, and the deformation amount is 1-3%.
The 8090 aluminum lithium alloy fine crystal plate is prepared by forging, rolling, solid solution, aging treatment and other technological methods.
The invention also provides application of the 8090 aluminum lithium alloy fine-grain plate in preparing parts of precise instruments.
Further, the parts of the precision instrument are specifically structural parts of semiconductor packaging equipment.
Compared with the prior art, the invention has the following beneficial effects:
1. according to the preparation method of the 8090 aluminum lithium alloy fine-grain plate, on the basis of the traditional preparation of the 8090 aluminum lithium alloy plate, larger deformation storage energy is provided through large deformation rolling, the atomic diffusion rate is improved, and energy is provided for precipitation of a strengthening phase in subsequent aging.
2. The invention can ensure the consistency of the deformation degree of the plate on one hand and can provide enough nucleation work for recrystallization annealing on the other hand by combining the hot rolling and the cold rolling so as to promote the generation of a recrystallization structure.
3. According to the invention, by increasing the overaging temperature or prolonging the overaging time, a coarser second phase is generated, and the quantity and the size meet the nucleation requirement; a large amount of second phase particles are separated out through overaging treatment, and a high dislocation density area is formed around the second phase particles, so that the driving force of recrystallization is improved; a region with large orientation gradient is formed around the second phase particles, and nucleation positions are provided for recrystallization nucleation; the uniformity of the size of the structural grains of the 8090 aluminum-lithium alloy is effectively improved through multistage rolling and overaging, and the mechanical property is improved.
4. The overaged sheet material is subjected to cold rolling deformation to form strong deformation areas around large-size second phase particles, and the strong deformation areas become nucleation sites for recrystallization in the subsequent recrystallization annealing process, so that the recrystallization process is promoted.
5. The preparation method can greatly refine grains and improve the original fibrous structure on the basis of the traditional 8090 aluminum lithium alloy plate preparation, thereby solving the problem of uneven structure and mechanical property after rolling and further improving the industrial application level of the 8090 aluminum lithium alloy.
Drawings
FIG. 1 is a photograph of an 8090 aluminum lithium alloy sheet in example 1 of the present invention;
FIG. 2 is a photograph of a microstructure of an ingot according to example 1 of the present invention;
FIG. 3 is a photograph of a microstructure of an 8090 aluminum lithium alloy sheet material in example 1 and comparative example 1 of the present invention, wherein the left drawing is example 1, and the right drawing is comparative example 1;
FIG. 4 is a graph showing the mechanical properties of 8090 aluminum lithium alloy sheets in example 1 and comparative example 1 of the present invention;
FIG. 5 is a photograph of a microstructure of an 8090 aluminum lithium alloy sheet material in example 2 and comparative example 2 of the present invention, wherein the left drawing is example 2, and the right drawing is comparative example 2;
FIG. 6 is a graph showing the mechanical properties of 8090 aluminum lithium alloy sheets in example 2 and comparative example 2 of the present invention;
FIG. 7 is a photograph of a microstructure of an 8090 aluminum lithium alloy sheet material in example 3 and comparative example 3 of the present invention, wherein the left drawing is example 3, and the right drawing is comparative example 3;
FIG. 8 is a graph showing the mechanical properties of 8090 aluminum lithium alloy sheets in example 3 and comparative example 3 of the present invention;
fig. 9 is a photograph of structural components of a semiconductor package apparatus prepared using the 8090 aluminum lithium alloy sheet material described in example 1.
Detailed Description
The present invention will be described in further detail below in order to make the objects, technical solutions and effects of the present invention more clear and distinct. It should be understood that the specific embodiments described herein are for purposes of illustration only and are not intended to limit the scope of the invention. The raw materials used in the following examples are all common commercial products.
Example 1
The 8090 aluminum lithium alloy fine-grain plate is prepared by forging an aluminum lithium alloy cast ingot, rolling, solid solution, aging treatment and other technological methods, wherein the 8090 aluminum lithium alloy cast ingot consists of the following components in percentage by mass: cu:1.2%, li:2.2%, mg:1.2%, zr:0.16%, the balance of Al and unavoidable impurity elements, wherein the content of each impurity element is Cr: less than or equal to 0.1 percent, mn: less than or equal to 0.2 percent, zn: less than or equal to 0.25 percent, si: less than or equal to 0.2 percent, fe: less than or equal to 0.3 percent, ti: less than or equal to 0.1 percent.
The preparation method of the 8090 aluminum lithium alloy fine-grain plate comprises the following specific steps:
(1) Vacuum casting and forging, and the concrete steps are as follows:
the casting process comprises the following steps: proportioning according to the mass percentage of each component in the alloy, drying, loading into a heating furnace, vacuumizing to below 10Pa, heating to 200 ℃, then charging 1000Pa argon to raise internal pressure in the furnace, heating to 830 ℃, starting refining, standing after refining, and casting to obtain square ingots; the microstructure is shown in figure 2, so that the crystal grains in the ingot tissue are uniformly distributed, obvious shrinkage cavity shrinkage porosity defects are avoided, the hydrogen content is lower than 10ppm, argon is introduced for protection during casting, and the casting quality of the ingot is improved;
the forging process comprises the following steps: heating the ingot along with a furnace, heating to 450 ℃, preserving heat for 12 hours after the furnace temperature is stable, forging at the temperature for about 20 minutes, wherein the forging upsetting reduction is 40%, and air cooling to room temperature after forging;
(2) Primary rolling (hot rolling): heating the forged spindle along with a furnace, heating to 450 ℃, preserving heat for 10 hours after the furnace temperature is stable, then rolling for one time at the temperature, controlling the rolling time to be about 10 minutes, controlling the single-pass deformation of one time rolling to be 25%, controlling the total deformation to be 80%, and obtaining the plate with the specification of 60 multiplied by 600 multiplied by 2100 mm;
(3) Primary solution heat treatment: heating the rolled plate along with a furnace, heating to 520 ℃, preserving heat for 3 hours after the furnace temperature is stable, then performing water cooling quenching to room temperature, and controlling the quenching transfer time within 15 seconds;
(4) Secondary rolling (isothermal rolling): placing the plate subjected to primary solid solution in a heating furnace, heating to 250 ℃, preserving heat for 8 hours after the furnace temperature is stable, then carrying out isothermal rolling at the temperature, controlling the rolling time to be about 10min, controlling the single-pass deformation to be 10%, controlling the total deformation to be 50%, and obtaining the plate with the specification of 30 multiplied by 600 multiplied by 4200 mm;
(5) Overaging heat treatment: directly heating the sheet material subjected to isothermal rolling to an overaging temperature of 300 ℃, and preserving heat for 36 hours after the furnace temperature is stable for overaging heat treatment;
(6) Cold rolling and annealing: cold rolling the plate subjected to overaging heat treatment at room temperature for about 10min, wherein the single-pass deformation is controlled to 7%, and the total deformation is controlled to 16%, so as to obtain the plate with the size of 25 multiplied by 600 multiplied by 5000 mm; heating the cold-rolled sheet to 480 ℃, and preserving heat for 24 hours after the furnace temperature is stable for recrystallization annealing;
(7) And (3) secondary solution heat treatment: heating the plate subjected to recrystallization annealing to 520 ℃, preserving heat for 3 hours after the furnace temperature is stable, carrying out solution heat treatment, and then carrying out water cooling quenching, wherein the quenching transfer time is controlled within 15 seconds; cold deforming the plate subjected to the secondary solution heat treatment by using a pre-stretching machine, wherein the deformation is 3%;
(8) And (3) secondary aging heat treatment: and heating the cold deformed plate to 170 ℃, preserving heat for 30 hours after the furnace temperature is stable, performing aging heat treatment, and then air-cooling to room temperature to obtain the final plate product with the thickness of 25 multiplied by 600 multiplied by 5000 mm.
The heating furnace is a resistance type heating furnace, the heating rate is 5 ℃/min, the temperature control precision is kept at +/-5 ℃, the temperature control can be more accurate within a certain temperature range, and the industrial production cost can be effectively reduced.
In the casting process, when a blank obtained by mixing the ingredients of all the elements of the alloy is placed in a hearth of a heating furnace, a gap of 30-40 cm is reserved between the blanks, an external thermocouple is placed at a contact position between the furnace door and the surface of the blank in the heating process, and the temperature of the furnace display temperature is the same as the temperature of the external thermocouple as a temperature judgment basis.
The primary rolling and the secondary rolling are all reciprocating rolling.
The photograph of the plate obtained in this example is shown in fig. 1, the microstructure photograph of the plate is the left graph in fig. 3, and it can be seen from the microstructure of the left graph in fig. 3 that after aging, cold rolling and heat treatment, the grain structure is obviously refined, and the recrystallization proportion is obviously increased.
Comparative example 1
Comparative example 1 a plate with a certain thickness is directly manufactured by casting, forging and rolling by adopting the same 8090 aluminum lithium alloy element composition in example 1, and the specific preparation method comprises the following steps:
(1) The specific steps of vacuum casting and forging are the same as in example 1;
(2) Rolling: heating the forged spindle along with a furnace, heating to 450 ℃, preserving heat for 12 hours after the furnace temperature is stable, rolling at the temperature, controlling the rolling time to be about 10min, controlling the single-pass rolling deformation to be 25%, and controlling the total deformation to be 90%, thus obtaining the plate with the specification of 25 multiplied by 600 multiplied by 2100 mm. The rolling is reciprocating rolling.
The heating furnace is a resistance type heating furnace, the heating rate is 5 ℃/min, the temperature control precision is kept at +/-5 ℃, the temperature control can be more accurate within a certain temperature range, and the industrial production cost can be effectively reduced.
In the casting process, when the blank obtained by mixing the ingredients of all the elements of the alloy is placed in a hearth of a heating furnace, a gap of 30cm is reserved between the blanks, an external thermocouple is placed at the contact position of the surface of the furnace door and the surface of the blank in the heating process, and the temperature of the furnace display temperature is the same as the temperature of the external thermocouple as a temperature judgment basis.
The microstructure photograph of the sheet obtained in comparative example 1 is the right hand drawing of fig. 3, and it can be seen from the microstructure of the right hand drawing of fig. 3 that the fibrous character of the structure in comparative example 1 is evident, and that the rolled structure exhibits fibrous character without significant recrystallization.
The mechanical property results of the products of the example 1 and the comparative example 1 are shown in the figure 4 according to GB/T228.1-2021 tensile test of metal materials, wherein the tensile strength of the example 1 is 477.6MPa, and the elongation is 6.5%; comparative example 1 had a tensile strength of 482.5MPa and an elongation of 5.1%; the tensile strength of comparative example 1 was not much different from that of example 1, but the elongation in example 1 was improved to a large extent, indicating that the fine grain structure improved the plasticity of the 8090 aluminum lithium alloy sheet to some extent.
Example 2
The 8090 aluminum lithium alloy fine-grain plate is prepared by forging an aluminum lithium alloy cast ingot, rolling, solid solution, aging treatment and other technological methods, wherein the 8090 aluminum lithium alloy cast ingot consists of the following components in percentage by mass: cu:1.4%, li:2.4%, mg:1.0%, zr:0.12%, and the balance of Al and unavoidable impurity elements, wherein the content of each impurity element is Cr: less than or equal to 0.1 percent, mn: less than or equal to 0.2 percent, zn: less than or equal to 0.25 percent, si: less than or equal to 0.2 percent, fe: less than or equal to 0.3 percent, ti: less than or equal to 0.1 percent.
The preparation method of the 8090 aluminum lithium alloy fine-grain plate comprises the following specific steps:
(1) Vacuum casting and forging, and the concrete steps are as follows:
the casting process comprises the following steps: proportioning according to the mass percentage of each component in the alloy, drying, loading into a heating furnace, vacuumizing to below 10Pa, heating to 200 ℃, then charging 1000Pa argon to improve pressure in the furnace, heating to 850 ℃ for refining, standing after refining, and casting to obtain square ingots; the crystal grains in the ingot tissue are uniformly distributed, obvious shrinkage cavity shrinkage porosity defects are avoided, the hydrogen content is lower than 10ppm, argon is introduced for protection during casting, and the casting quality of the ingot is improved;
the forging process comprises the following steps: heating the ingot along with a furnace, heating to 430 ℃, preserving heat for 12 hours after the furnace temperature is stable, forging at the temperature, controlling the forging time to be about 20min, controlling the upsetting reduction in forging to be 35%, and cooling to room temperature after forging;
(2) Primary rolling (hot rolling): heating the forged spindle along with a furnace, heating to 430 ℃, preserving heat for 10 hours after the furnace temperature is stable, then rolling for one time at the temperature, controlling the rolling time to be about 10 minutes, controlling the single-pass deformation of one time rolling to be 25%, and controlling the total deformation to be 80%, thus obtaining a plate with the specification of 60 multiplied by 600 multiplied by 2100 mm;
(3) Primary solution heat treatment: heating the rolled plate along with a furnace, heating to 510 ℃, preserving heat for 4 hours after the furnace temperature is stable, then performing water cooling quenching to room temperature, and controlling the quenching transfer time within 15 seconds;
(4) Secondary rolling (isothermal rolling): placing the plate subjected to primary solid solution in a heating furnace, heating to 250 ℃, preserving heat for 8 hours after the furnace temperature is stable, then carrying out isothermal rolling at the temperature, controlling the rolling time to be about 10min, controlling the single-pass deformation to be 10%, controlling the total deformation to be 50%, and obtaining the plate with the specification of 30 multiplied by 600 multiplied by 4200 mm;
(5) Overaging heat treatment: directly heating the sheet material subjected to isothermal rolling to an overaging temperature of 300 ℃, and preserving heat for 36 hours after the furnace temperature is stable for overaging heat treatment;
(6) Cold rolling and annealing: cold rolling the plate subjected to overaging heat treatment at room temperature, wherein the rolling time is controlled to be about 10min, the single-pass deformation is controlled to be 6%, and the total deformation is controlled to be 15%, so that the plate with the specification of 25 multiplied by 600 multiplied by 5000mm is obtained; heating the cold-rolled sheet to 470 ℃, and preserving heat for 24 hours after the furnace temperature is stable for recrystallization annealing;
(7) And (3) secondary solution heat treatment: heating the plate subjected to recrystallization annealing to 510 ℃, preserving heat for 4 hours after the furnace temperature is stable, carrying out solution heat treatment, and then carrying out water cooling quenching, wherein the quenching transfer time is controlled within 15 seconds; cold deforming the plate subjected to the secondary solution heat treatment by using a pre-stretching machine, wherein the deformation is 3%;
(8) And (3) secondary aging heat treatment: and heating the cold deformed plate to 170 ℃, preserving heat for 30 hours after the furnace temperature is stable, performing aging heat treatment, and then air-cooling to room temperature to obtain the plate with the final specification of 25 multiplied by 600 multiplied by 5000 mm.
The heating furnace is a resistance type heating furnace, the heating rate is 5 ℃/min, the temperature control precision is kept at +/-5 ℃, the temperature control can be more accurate within a certain temperature range, and the industrial production cost can be effectively reduced.
In the casting process, when a blank obtained by mixing the ingredients of all the elements of the alloy is placed in a hearth of a heating furnace, a gap of 30-40 cm is reserved between the blanks, an external thermocouple is placed at a contact position between the furnace door and the surface of the blank in the heating process, and the temperature of the furnace display temperature is the same as the temperature of the external thermocouple as a temperature judgment basis.
The primary rolling and the secondary rolling are all reciprocating rolling.
The microstructure photograph of the sheet material obtained in this example is the left diagram in fig. 5, and it can be seen from the microstructure of the left diagram in fig. 5 that the grain structure also shows a tendency to be refined after aging, cold rolling and recrystallization treatment.
Comparative example 2
Comparative example 2 a plate with a certain thickness is directly manufactured by casting, forging and rolling by adopting the same 8090 aluminum lithium alloy element composition in example 2, and the specific preparation method comprises the following steps:
(1) The specific steps of vacuum casting and forging are the same as in example 2;
(2) Rolling: heating the forged spindle along with a furnace, heating to 430 ℃, preserving heat for 10 hours after the furnace temperature is stable, rolling at the temperature, controlling the rolling time to be about 10 minutes, controlling the single-pass rolling deformation to be 25%, and controlling the total deformation to be 90%, thus obtaining the plate with the specification of 25 multiplied by 600 multiplied by 5000 mm. The rolling is reciprocating rolling.
The heating furnace is a resistance type heating furnace, the heating rate is 5 ℃/min, the temperature control precision is kept at +/-5 ℃, the temperature control can be more accurate within a certain temperature range, and the industrial production cost can be effectively reduced.
In the casting process, when a blank obtained by mixing the ingredients of all the elements of the alloy is placed in a hearth of a heating furnace, a gap of 30-40 cm is reserved between the blanks, an external thermocouple is placed at a contact position between the furnace door and the surface of the blank in the heating process, and the temperature of the furnace display temperature is the same as the temperature of the external thermocouple as a temperature judgment basis.
The microstructure photograph of the sheet obtained in comparative example 2 is shown in the right hand side of fig. 5, and it can be seen from the microstructure of the right hand side of fig. 5 that the crystal grains in comparative example 2 are still fibrous.
The mechanical property test results of the products of the example 2 and the comparative example 2, which are measured according to GB/T228.1-2021 Metal Material tensile test, are shown in the accompanying figure 6, wherein the tensile strength of the example 2 is 473.2MPa, and the elongation is 7.2%; comparative example 2 has a tensile strength of 496.2MPa and an elongation of 5.8%; the elongation in example 2 was also improved to some extent as compared with example 2, indicating that the fine grain structure improved to some extent in the plasticity of the 8090 aluminum lithium alloy sheet.
Example 3
The 8090 aluminum lithium alloy fine-grain plate is prepared by forging an aluminum lithium alloy cast ingot, rolling, solid solution, aging treatment and other technological methods, wherein the 8090 aluminum lithium alloy cast ingot consists of the following components in percentage by mass: cu:1.6%, li:2.6%, mg:0.8%, zr:0.12%, and the balance of Al and unavoidable impurity elements, wherein the content of each impurity element is Cr: less than or equal to 0.1 percent, mn: less than or equal to 0.2 percent, zn: less than or equal to 0.25 percent, si: less than or equal to 0.2 percent, fe: less than or equal to 0.3 percent, ti: less than or equal to 0.1 percent.
The preparation method of the 8090 aluminum lithium alloy fine-grain plate comprises the following specific steps:
(1) Vacuum casting and forging, and the concrete steps are as follows:
the casting process comprises the following steps: proportioning according to the mass percentage of each component in the alloy, drying, loading into a heating furnace, vacuumizing to below 10Pa, heating to 200 ℃, then charging 1000Pa argon to improve pressure in the furnace, heating to 850 ℃ to smelt and start refining, standing after refining, and casting to obtain square cast ingots; the crystal grains in the ingot tissue are uniformly distributed, obvious shrinkage cavity shrinkage porosity defects are avoided, the hydrogen content is lower than 10ppm, argon is introduced for protection during casting, and the casting quality of the ingot is improved;
the forging process comprises the following steps: heating the ingot along with a furnace, heating to 420 ℃, preserving heat for 12 hours after the furnace temperature is stable, forging at the temperature, controlling the forging time to be about 20min, controlling the upsetting reduction in forging to be 40%, and cooling to room temperature after forging;
(2) Primary rolling (hot rolling): heating the forged spindle along with a furnace, heating to 420 ℃, preserving heat for 10 hours after the furnace temperature is stable, then carrying out primary rolling at the temperature, controlling the rolling time to be about 10 minutes, controlling the single-pass deformation of the primary rolling to be 25%, controlling the total deformation to be 80%, and obtaining the sheet material with the specification of 60 multiplied by 600 multiplied by 2100 mm;
(3) Primary solution heat treatment: heating the rolled plate along with a furnace, heating to 500 ℃, preserving heat for 4 hours after the furnace temperature is stable, then performing water cooling quenching to room temperature, and controlling the quenching transfer time within 15 seconds;
(4) Secondary rolling (isothermal rolling): placing the plate subjected to primary solid solution in a heating furnace, heating to 250 ℃, preserving heat for 8 hours after the furnace temperature is stable, then carrying out isothermal rolling at the temperature, controlling the rolling time to be about 10min, controlling the single-pass deformation to be 10%, controlling the total deformation to be 50%, and obtaining the plate with the specification of 30 multiplied by 600 multiplied by 4200 mm;
(5) Overaging heat treatment: heating the sheet material subjected to isothermal rolling to an overaging temperature of 300 ℃, and preserving heat for 36 hours after the furnace temperature is stable to carry out overaging heat treatment;
(6) Cold rolling and annealing: cold rolling the plate subjected to overaging heat treatment at room temperature for about 10min, wherein the single-pass deformation is controlled to 7%, and the total deformation is controlled to 16%, so as to obtain the plate with the size of 25 multiplied by 600 multiplied by 5000 mm; heating the cold-rolled sheet to 450 ℃, and preserving heat for 24 hours after the furnace temperature is stable for recrystallization annealing;
(7) And (3) secondary solution heat treatment: heating the plate subjected to recrystallization annealing to 500 ℃, preserving heat for 4 hours after the furnace temperature is stable, carrying out solution heat treatment, and then carrying out water cooling quenching, wherein the quenching transfer time is controlled within 15 seconds; cold deforming the plate subjected to the secondary solution heat treatment by using a pre-stretching machine, wherein the deformation is 3%;
(8) And (3) secondary aging heat treatment: and heating the cold deformed plate to 170 ℃, preserving heat for 30 hours after the furnace temperature is stable, performing aging heat treatment, and then air-cooling to room temperature to obtain the plate with the final size of 25 multiplied by 600 multiplied by 5000 mm.
The heating furnace is a resistance type heating furnace, the heating rate is 5 ℃/min, the temperature control precision is kept at +/-5 ℃, the temperature control can be more accurate within a certain temperature range, and the industrial production cost can be effectively reduced.
In the casting process, when a blank obtained by mixing the ingredients of all the elements of the alloy is placed in a hearth of a heating furnace, a gap of 30-40 cm is reserved between the blanks, an external thermocouple is placed at a contact position between the furnace door and the surface of the blank in the heating process, and the temperature of the furnace display temperature is the same as the temperature of the external thermocouple as a temperature judgment basis.
The primary rolling and the secondary rolling are all reciprocating rolling.
The microstructure photograph of the sheet material obtained in this example is the left graph in fig. 7, and it can be seen from the microstructure of the left graph in fig. 7 that the grain structure is significantly refined and the recrystallization rate is significantly increased after aging and cold rolling treatment.
Comparative example 3
Comparative example 3 a plate with a certain thickness is directly manufactured by casting, forging and rolling by adopting the same 8090 aluminum lithium alloy element composition in example 3, and the specific preparation method comprises the following steps:
(1) The specific steps of vacuum casting and forging are the same as in example 3;
(2) Rolling: heating the forged spindle along with a furnace, heating to 420 ℃, preserving heat for 12 hours after the furnace temperature is stable, rolling at the temperature, controlling the rolling time to be about 10min, controlling the single-pass rolling deformation to be 25%, and controlling the total deformation to be 90%, thus obtaining the plate with the specification of 25 multiplied by 600 multiplied by 5000 mm. The rolling is reciprocating rolling.
The heating furnace is a resistance type heating furnace, the heating rate is 5 ℃/min, the temperature control precision is kept at +/-5 ℃, the temperature control can be more accurate within a certain temperature range, and the industrial production cost can be effectively reduced.
In the casting process, when the blank obtained by mixing the ingredients of all the elements of the alloy is placed in a hearth of a heating furnace, a gap of 30cm is reserved between the blanks, an external thermocouple is placed at the contact position of the surface of the furnace door and the surface of the blank in the heating process, and the temperature of the furnace display temperature is the same as the temperature of the external thermocouple as a temperature judgment basis.
The secondary rolling is reciprocating rolling.
The microstructure photograph of the sheet obtained in comparative example 3 is the right hand drawing of fig. 7, and it can be seen from the microstructure of the right hand drawing of fig. 7 that the fibrous structure characteristic of comparative example 3 is still evident, and no significant recrystallization occurs at this time, and the grain characteristics are predominantly fibers after rolling.
The mechanical property test results of the products of the example 3 and the comparative example 3, which are measured according to GB/T228.1-2021 tensile test of metal materials, are shown in the accompanying figure 8, wherein the tensile strength of the example 3 is 476.8MPa, and the elongation is 7.0%; comparative example 3 had a tensile strength of 483.8MPa and an elongation of 5.1%; the elongation improvement effect in example 3 was also more remarkable as compared with example 3.
After the 8090 aluminum lithium alloy cast ingot of the comparative example is rolled, crystal grains are obviously elongated and fibrous, and the problem of uneven mechanical properties can occur in the use scene with higher requirements on certain mechanical properties.
Therefore, the embodiments 1, 2 and 3 of the invention make improvements on the basis, increase overaging, rolling and recrystallization processes, increase the precipitation quantity of second phase particles and the nuclear energy of recrystallization, increase the proportion of the recrystallization grains, finally lead the grains to be in a better fine crystal shape, effectively solve the problems of poor plasticity and inconsistent performance of the 8090 aluminum lithium alloy sheet, enlarge the application field of the 8090 aluminum lithium alloy and have better application prospect.
Application example 1
The 8090 aluminum lithium alloy fine-grain plate has good strength, high elongation and high elastic modulus, is used for manufacturing fine structural parts in the field of digital products, and has the characteristics of high strength, light weight and difficult deformation in the machining process. As shown in FIG. 9, the structural component of the semiconductor packaging device manufactured by machining the 8090 aluminum lithium alloy fine-grain plate in embodiment 1 has light weight and small deformation, is used for structural members of digital products, can reduce the weight by about 10%, replaces the traditional 6XXX and 7XXX aluminum alloys, can effectively reduce the weight of the products, exerts the maximum weight reduction value, and has good application prospects in the field of precision manufacturing.
While specific embodiments of the invention have been described above, it should be understood that the invention is not limited to the particular embodiments described above. Various changes or modifications may be made by one skilled in the art within the scope of the claims without affecting the spirit of the invention.
Claims (8)
1. The preparation method of the 8090 aluminum lithium alloy fine-grain plate is characterized by comprising the following steps:
(1) Vacuum casting and forging: proportioning according to the mass percentage of each component in the alloy, vacuumizing to below 10Pa, performing vacuum casting to obtain an ingot, and forging;
(2) And (3) hot rolling: heating the forged cast ingot to 400-450 ℃, preserving heat for 8-14 h, hot rolling to obtain a plate, and controlling the rolling time within 30 min;
(3) Primary solution heat treatment: heating the rolled plate to 500-540 ℃, preserving heat for 2-4 hours, and performing water cooling quenching;
(4) Isothermal rolling: heating the plate subjected to primary solid solution to 150-250 ℃, preserving heat for 6-8 hours, and carrying out isothermal rolling for 30min or less;
(5) Overaging heat treatment: directly heating the sheet material subjected to isothermal rolling to 300-400 ℃, and carrying out heat preservation for 36-48 hours for overaging heat treatment;
(6) Cold rolling and annealing: cold rolling the plate subjected to overaging heat treatment at room temperature for 30 min; after cold rolling, heating the plate to 450-500 ℃, and preserving heat for 12-24 hours for annealing;
(7) And (3) secondary solution heat treatment: heating the annealed plate to 500-540 ℃, preserving heat for 3-5 hours, performing solution heat treatment, and then performing water cooling quenching;
(8) And (3) secondary aging heat treatment: heating the plate subjected to the secondary solution heat treatment to 150-170 ℃, preserving heat for 15-30 hours, performing aging heat treatment, and then air-cooling to room temperature to obtain a final product;
the aluminum-lithium alloy in the step (1) comprises the following components in percentage by mass: cu:1.0 to 1.6%, li: 2.2-2.7%, mg: 0.6-1.3%, zr: 0.04-0.16%, and the balance of Al and unavoidable impurity elements.
2. The method of claim 1, wherein in step (1), the casting process comprises: and (3) after the alloy raw materials are proportioned, vacuumizing to less than 10Pa, heating to 200 ℃, then charging 1000Pa of argon, heating to a smelting temperature of not more than 850 ℃ to start refining, standing after refining, and casting to obtain an ingot.
3. The method of claim 1, wherein in step (1), the forging process comprises: heating the ingot to 400-450 ℃, preserving heat for 10-16 h, forging, controlling the forging time within 40min, and performing air cooling to room temperature after forging, wherein the upsetting deformation is 30-50% during forging.
4. The method according to claim 1, wherein in the step (2), the single-pass deformation amount of the hot rolling is controlled to 15-30%, and the total deformation amount is controlled to 70-80%, so that a plate with a size of 60×600×2100mm is obtained.
5. The method according to claim 1, wherein in the step (3), the quenching transfer time is controlled to be within 15 seconds.
6. The method according to claim 1, wherein in the step (4), the single-pass deformation amount of isothermal rolling is controlled to be 10-20%, and the total deformation amount is controlled to be 50-70%, so that a plate with the size of 30×600×4200mm is obtained.
7. The method according to claim 1, wherein in the step (6), the single-pass deformation amount of cold rolling is controlled to be 5-10%, and the total deformation amount is controlled to be 10-20%, so that a plate with a size of 25 x 600 x 5000mm is obtained.
8. The method according to claim 1, wherein in the step (7), the quenching transfer time is controlled to be within 15 seconds.
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