CN117701847A - 6000 series aluminum alloy plate manufacturing method and aluminum alloy plate - Google Patents
6000 series aluminum alloy plate manufacturing method and aluminum alloy plate Download PDFInfo
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- CN117701847A CN117701847A CN202211084044.8A CN202211084044A CN117701847A CN 117701847 A CN117701847 A CN 117701847A CN 202211084044 A CN202211084044 A CN 202211084044A CN 117701847 A CN117701847 A CN 117701847A
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- 238000000034 method Methods 0.000 claims abstract description 47
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- 238000005097 cold rolling Methods 0.000 claims abstract description 29
- 238000001816 cooling Methods 0.000 claims abstract description 12
- 230000032683 aging Effects 0.000 claims abstract description 11
- 238000000265 homogenisation Methods 0.000 claims abstract description 10
- 238000000137 annealing Methods 0.000 claims description 31
- 238000001953 recrystallisation Methods 0.000 claims description 19
- 230000009467 reduction Effects 0.000 claims description 11
- 238000005098 hot rolling Methods 0.000 claims description 7
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 7
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Classifications
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- 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
-
- 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
-
- 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
- C21D8/0226—Hot rolling
-
- 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
- C21D8/0236—Cold rolling
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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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
- 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
- C22F1/043—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 silicon as the next major constituent
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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
- 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
- C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
-
- 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
- B21B2003/001—Aluminium or its alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- Chemical & Material Sciences (AREA)
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- Mechanical Engineering (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Metal Rolling (AREA)
Abstract
The invention discloses a manufacturing method of 6000 series aluminum alloy plates with high forming performance, high flanging performance and low rib defects, which comprises the following steps: (1) Homogenizing the cast ingot at 530-580 ℃; (2) Directly carrying out hot rough rolling, hot finish rolling and hot finish rolling coiling on the ingot subjected to homogenization treatment, controlling the initial rolling temperature of the hot finish rolling to be 400-480 ℃ and controlling the hot finish rolling coiling temperature to be more than 250 ℃; (3) cold rolling: controlling the total deformation of the cold rolling to be 50-85 percent, and obtaining Mg in the cold-rolled sheet 2 The average size of the Si precipitated phase is 1.3-1.7 mu m, mg 2 Si precipitated phase surface density not less than 55000 pieces/mm 2 The method comprises the steps of carrying out a first treatment on the surface of the (4) solution treatment; (5) The pre-ageing treatment is carried out,and then air cooling is carried out to obtain 6000 series aluminum alloy plates. Correspondingly, the invention also discloses the 6000 series aluminum alloy plate prepared by the method.
Description
Technical Field
The invention relates to an aluminum alloy plate and a manufacturing method thereof, in particular to a 6000 series aluminum alloy plate and a manufacturing method thereof.
Background
The 6000 series aluminum alloy has the advantages of high strength, good corrosion resistance, good surface quality after baking, improved strength after baking and the like, and is increasingly applied to manufacturing of automobile body outer covering parts.
As a vehicle body panel, the surface quality of 6000 series aluminum alloy automobile panels is as important as the mechanical properties thereof, and whether the appearance of the automobile after painting is ideal or not is related, and Luo Pingwen defect is one of factors influencing the surface quality of the aluminum alloy automobile panels.
In addition, in the flanging process of the aluminum alloy plate, the interface between the coarse intermetallic compound and the aluminum plate matrix often causes serious stress concentration to induce the initiation of microcracks, so that the flanging performance of the alloy plate can be reduced, and the improvement of the flanging performance of the aluminum alloy plate is also of great significance.
Chinese patent publication No. CN101935785B, entitled "an aluminum alloy for high formability automotive body panels", discloses an aluminum alloy for 6000 series automotive body panels having excellent formability obtained by adjusting the contents and proportions of the main elements Si, mg, cu. The excellent formability described in this patent focuses only on yield strength, plasticity and work hardening rate, and does not focus on r-value, burring performance and rib performance which are closely related to the formation of automobile body panels.
Chinese patent document with publication No. CN105074028B, publication No. 2017, 6 and 6, entitled "aluminum alloy sheet excellent in characteristics after room temperature aging" discloses an aluminum alloy sheet excellent in properties after room temperature aging by adding an appropriate amount of Sn element to the chemical composition, and a method for manufacturing the sheet thereof, the material prepared therefrom having excellent formability. This patent achieves good technical results by adding the alloying element Sn, but it does not pay attention to how to improve the flanging performance of the sheet.
Therefore, in the prior art, 6000 series aluminum alloy plates have the problems of poor flanging performance, obvious Luo Pingwen defects on the surface after stamping and the like, and the large-scale popularization and application of 6000 series automobile plates are affected.
Based on this, it is desired to obtain a manufacturing method that imparts high formability, high flanging performance, and low rib defect to 6000 series aluminum alloy sheet.
Disclosure of Invention
The invention aims to provide a manufacturing method of 6000 series aluminum alloy plates with high forming performance, high flanging performance and low rib defects, which adopts reasonable process design, and can obtain alloy plates with certain second phase quantity and proportion and grain size through soaking, hot rolling, coiling, optional intermediate annealing and cold rolling processes, further excite a recrystallization nucleation (PSN) effect in the subsequent solid solution pre-aging treatment process, weaken the recrystallization texture content, especially the content of cube texture components and Gaussian texture components, further remarkably improve the forming performance and flanging performance of the finally obtained aluminum alloy plates and improve the rib defects of the aluminum alloy plates.
In order to achieve the above object, the present invention provides a method for manufacturing 6000 series aluminum alloy sheet having high formability, high flanging performance and low rib defect, comprising the steps of:
(1) Homogenizing the cast ingot at 530-580 ℃;
(2) Directly carrying out hot rough rolling, hot finish rolling and hot finish rolling coiling on the ingot subjected to homogenization treatment, controlling the initial rolling temperature of the hot finish rolling to be 400-480 ℃ and controlling the hot finish rolling coiling temperature to be more than 250 ℃;
(3) Cold rolling: controlling cold rolling total variationThe shape quantity is 50-85%, and the obtained Mg in the cold-rolled sheet 2 The average size of the Si precipitated phase is 1.3-1.7 mu m, mg 2 Si precipitated phase surface density not less than 55000 pieces/mm 2 ；
(4) Solution treatment;
(5) Pre-ageing treatment, and air cooling to obtain 6000 series aluminum alloy plate.
The inventors have found through extensive research that the second phase particles have a great influence on the recrystallization texture of 6000 series aluminum alloys, and when coarse second phase particles are precipitated in the alloy, the coarse second phase can excite recrystallization nucleation (PSN, particle Stimulated Nucleation), thereby promoting recrystallization, leading the recrystallized texture components to be mainly random textures, reducing the texture strength, and reducing the aggregation degree of the typical recrystallization texture neutral texture components and gaussian texture components, and reducing the rib defect degree. Furthermore, the inventors have found through studies that the grain size decreases with an increase in cold rolling reduction.
Based on the method, in order to overcome the technical problems of insufficient forming performance, poor flanging performance and easiness in occurrence of Luo Pingwen defect of the traditional 6000 series aluminum alloy plate, the manufacturing method disclosed by the invention can regulate and control coarse Mg in the 6000 series aluminum alloy plate by regulating and controlling soaking, hot rolling, coiling and optional intermediate annealing process parameters in the processing process on the premise of ensuring the process rationality 2 Si phase size and quantity, and fully exert coarse Mg 2 The particles induce a recrystallization nucleation (PSN, particle Stimulated Nucleation) effect in the Si phase during subsequent solid solution, thereby adjusting texture; secondly, the structure and the grain size can be further regulated and controlled by regulating and controlling the cold rolling reduction rate and the grain size in the subsequent cold rolling process so as to achieve the purposes of weakening and regulating and controlling the recrystallization structure type, proportion and space distribution and refining the grain size, thereby obtaining the 6000 series aluminum alloy plate with high forming property, high flanging property and low rib defect for the automobile body.
Specifically, unbalanced eutectic compatibility in an as-cast 6000 series aluminum alloy tends to cause uneven composition or structure, and causes the problems of poor plasticity in subsequent thermal deformation, and the like, which are certainThe forming processability of 6000 series aluminum alloy is restricted to a certain extent. Therefore, the technical proposal controls the soaking temperature in the homogenization process to exceed 530 ℃ so as to ensure that most of too coarse Mg 2 Si dissolves and at the same time aims to improve the hot workability of 6000 series aluminium alloys and to eliminate the effect of non-equilibrium eutectic phases in the alloy.
In addition, according to the research of the inventor, in the technical scheme, if the initial rolling temperature of the hot finish rolling is controlled to be 400-480 ℃, the size of the second phase in the cold-rolled sheet can be controlled to be 1.3-1.7 mu m, and the surface density of the second phase is more than 55000 pieces/mm; if the hot finish rolling start temperature is too high, the size of the precipitated second phase is too large and the number of the precipitated second phase is small; if the hot finish rolling start temperature is too low, the size of the precipitated second phase is too small.
In addition, according to the research of the inventor, in the technical scheme, if the cold rolling reduction is lower than 50%, coarse grains in the finished plate can be caused, on one hand, the outer plate surface of the alloy plate is subjected to flanging to generate defects such as microcracks or continuous necking, the flanging performance is reduced, and on the other hand, the plate is subjected to stamping forming to form an orange peel-shaped rough surface, and the surface quality is reduced; if the cold rolling reduction is higher than 85%, the local deformation region around the coarse second phase particles is too large, and this region becomes a microcrack initiation region during the forming process, which is disadvantageous for the forming performance. Therefore, the cold rolling reduction rate is controlled to be 50-85 percent.
In the technical scheme of the invention, the unbalanced eutectic phase in the ingot is dissolved by soaking the ingot at reasonable temperature and for a reasonable time, then the homogenized ingot is directly subjected to hot rough rolling, casting defects are eliminated or reduced, and is processed into an intermediate blank meeting the hot finish rolling condition, and then the hot finish rolling, intermediate annealing and cold rolling processes are controlled to obtain a cold-rolled sheet with a large number of coarse second phases and fine grains, and in the solid solution pre-aging process before subsequent delivery, on one hand, the content of recrystallization texture is weakened by a PSN mechanism excited by the coarse second phases; on the other hand, a finished product state plate with fine grains is obtained by regulating and controlling the cold rolling reduction rate, and then the 6000 aluminum alloy plate with high formability, high flanging property and low rib defect is obtained.
In other words, the manufacturing method provided by the invention is matched with a specific process, so that the number, distribution and grain size of coarse second phases in the aluminum alloy are effectively regulated and controlled, the texture and structure of the final finished product T4P 6000 series aluminum alloy plate are regulated and controlled, and the forming performance, flanging performance and rib defect of the 6000 series aluminum alloy plate are obviously improved.
Further, in the step (2) of the 6000 series aluminum alloy sheet manufacturing method of the present invention, when the hot finish rolling coiling temperature is 250 to 340 ℃, intermediate annealing is performed before cold rolling in the step (3): controlling the temperature of the intermediate annealing to be 350-430 ℃, keeping the temperature for 1-4 hours, and then cooling to room temperature along with a furnace; when the hot finishing rolling coiling temperature is higher than 340 ℃, the step (3) is directly performed without intermediate annealing.
In order to facilitate the subsequent further cold working, an intermediate anneal may be added between the hot and cold rolling steps. In the technical scheme, the deformation resistance and easy realization of deformation can be reduced after the intermediate annealing. As a result of the study of the present inventors, it was found that when the hot finish rolling coiling temperature is 250 to 340 ℃, an intermediate annealing is required to control the second phase so that Mg 2 The average size of the Si precipitated phase is 1.3-1.7 mu m, and the surface density is more than or equal to 55000 pieces/mm 2 . Wherein when the intermediate annealing temperature is above 350 ℃, the second phase precipitation speed is relatively high, and the second phase size is relatively large; when the intermediate annealing temperature is below 350 ℃, the second phase precipitation speed is relatively slow, and the second phase particle size is relatively small, so that the occurrence of a PSN mechanism is not facilitated; however, when the intermediate annealing temperature is higher than 430 ℃, the size of the precipitated second phase particles is too large, and the second phase particles become initiation points of microcracks in the processing process, so that the subsequent plate forming is not facilitated, and meanwhile, the formation of subsequent PSN textures is not facilitated due to the small number of the second phase particles at high temperature.
In another embodiment, if the hot finishing rolling temperature is higher than 340 ℃, the intermediate annealing is not performed at this time, and Mg having an average size of 1.3 to 1.7 μm can be obtained 2 Si precipitated phase surface density not less than 55000 pieces/mm 2 Is a second phase of (c).
Further, in the step (2), when the intermediate annealing is performed, the temperature rise rate of the intermediate annealing is 13 to 17 ℃/h, and the temperature reduction rate of the intermediate annealing is 12 to 15 ℃/h.
Further, in the step (1) of the 6000 series aluminum alloy sheet manufacturing method of the present invention, the heat preservation time of the homogenization treatment is 6 to 16 hours.
Further, in the step (1) of the 6000 series aluminum alloy sheet manufacturing method of the present invention, the homogenization treatment temperature is 550 to 570 ℃.
Further, in the step (2) of the 6000 series aluminum alloy plate manufacturing method, the total deformation of hot rough rolling is controlled to be more than 70%; and/or the total deformation of the hot finish rolling is more than 80%.
Further, in the step (2) of the 6000 series aluminum alloy sheet manufacturing method of the present invention, the initial rolling temperature of the finish hot rolling is 440 to 480 ℃.
Further, in the step (3) of the 6000 series aluminum alloy sheet manufacturing method of the present invention, the total cold rolling deformation amount is controlled to be 60 to 85%.
Further, in the step (4) of the 6000 series aluminum alloy plate manufacturing method, the solid solution treatment temperature is 550-570 ℃, the solid solution temperature rise rate is 15-30 ℃/s, the solid solution treatment heat preservation time is 1-5 min, and the quenching mode is water cooling.
Further, in the step (5) of the 6000 series aluminum alloy sheet manufacturing method of the present invention, the pre-aging treatment is performed within 3 minutes.
Further, in the step (5) of the 6000 series aluminum alloy plate manufacturing method, the pre-aging treatment is that the temperature is slowly reduced to the room temperature from 80-100 ℃ at the cooling rate of 1-4 ℃/h.
Accordingly, another object of the present invention is to provide a 6000 series aluminum alloy sheet having high formability, high flanging performance and low rib defect, which is easy to produce and low in production cost, and which has relatively high formability, high flanging performance and low Luo Pingwen defect, so that it can be effectively applied to the vehicle manufacturing industry, and meets the requirement of light weight of vehicles.
In order to achieve the above object, the present invention provides a 6000 series aluminum alloy sheet having high formability, high flanging performance and low rib defect, which is manufactured by the manufacturing method of 6000 series aluminum alloy sheet.
Further, the 6000 series aluminum alloy plate provided by the invention has the average grain size of 20-32 mu m, the recrystallization texture density of 6.5-10.0, the content of cubic texture components is less than or equal to 8%, and the content of Gaussian texture components is less than or equal to 7%.
Further, the 6000 series aluminum alloy plate disclosed by the invention has the following properties: the tensile strength is more than or equal to 210MPa, the yield strength is more than or equal to 104MPa, and the elongation is more than or equal to 24%; the plastic strain ratio r is more than or equal to 0.68, the plane anisotropy index Deltar is less than or equal to 0.10, the flanging grade (flanging factor is 0.6) is rated as 1, and the Luo Pingwen grade is rated as 1.
Compared with the prior art, the 6000 series aluminum alloy plate manufacturing method has the following advantages:
(1) According to the manufacturing method of the 6000 series aluminum alloy plate, a large amount of larger second phases can be obtained through homogenization, hot rolling, coiling, optional intermediate annealing and cold rolling processes, so that PSN mechanism recrystallization nucleation is induced in the subsequent solution treatment and pre-ageing processes, the density of recrystallization textures, especially the content of soft texture cube textures and hard texture Gaussian textures, is reduced, the forming performance of the plate is improved, and rib defect of the plate is reduced.
(2) According to the manufacturing method of the 6000 series aluminum alloy plate, the crystal grains of the aluminum alloy plate can be fine by regulating and controlling the cold rolling process in the processing process, so that the flanging performance of the aluminum alloy plate is improved.
(3) The manufacturing method of 6000 series aluminum alloy plates is simple and convenient in process, can realize process optimization by adjusting parameters on the basis of the existing aluminum alloy heat treatment production line, is quite wide in applicability and can meet the industrial production requirements.
(4) The manufacturing method can quantify the organization and texture of 6000 aluminum alloy plates, and the 6000 aluminum alloy plates have the defects of high forming performance, high flanging performance and low Luo Pingwen, can be effectively applied to the vehicle manufacturing industry, meets the requirement of light weight of vehicles, and has very wide application prospect.
Drawings
FIG. 1 schematically shows a process flow diagram of the 6000 series aluminum alloy sheet manufacturing method according to the present invention.
Detailed Description
The 6000 series aluminum alloy sheet and the manufacturing method thereof according to the present invention will be further explained and illustrated with reference to specific examples and drawings, however, the explanation and illustration do not unduly limit the technical scheme of the present invention.
Examples 1 to 8 and comparative examples 1 to 4
Table 1 shows the chemical compositions of 6000 series aluminum alloy sheets of examples 1 to 8 and aluminum alloy sheets of comparative examples 1 to 4.
Table 1 (wt.%), balance Al and other unavoidable impurities
Since the composition ratio of the aluminum alloy sheet is not limited by the present invention, the effects of table 1 are only used for the manufacturing method of the present invention, and are not limited by the manufacturing method and the aluminum alloy sheet.
FIG. 1 schematically shows a process flow diagram of the 6000 series aluminum alloy sheet manufacturing method according to the present invention.
As shown in FIG. 1, 6000 series aluminum alloy sheets of examples 1-8 according to the present invention were prepared by the following steps:
(1) Smelting and casting: preparing materials according to chemical compositions shown in table 1, and casting to prepare an aluminum alloy ingot after melting in a smelting furnace;
(2) Homogenizing: heating the aluminum alloy ingot in a homogenizing heat treatment furnace along with the furnace, heating to 530-580 ℃ at a heating rate of 20-50 ℃/h, and preferably controlling the temperature to 550-570 ℃ for homogenizing heat treatment; and preferably controlling the heat preservation time of the homogenization treatment to be 6-16 hours, and further preferably controlling the heat preservation time to be 8-12 hours;
(3) Hot rough rolling: performing hot rough rolling on the cast ingot, and controlling the total deformation of the hot rough rolling to be more than 70%;
(4) And (3) hot finish rolling: performing hot finish rolling on the hot rough rolled plate, wherein the initial rolling temperature of the hot finish rolling is controlled to be 400-480 ℃, and preferably can be controlled to be 440-480 ℃; controlling the coiling temperature of the hot finish rolling to be more than 250 ℃ and controlling the total deformation of the hot finish rolling to be more than 80%;
(5) Intermediate annealing: when the coiling temperature of the hot finish rolling is 250-340 ℃, performing intermediate annealing, controlling the temperature of the intermediate annealing to be 350-430 ℃, keeping the temperature for 1-4 hours, and controlling the temperature rising rate of the intermediate annealing to be 13-17 ℃/h and the temperature reducing rate of the intermediate annealing to be 12-15 ℃/h; when the coiling temperature of the hot final rolling is higher than 340 ℃, directly entering cold rolling without intermediate annealing;
(6) Cold rolling: controlling the total deformation of the cold rolling to be 50-85%, preferably controlling the total deformation of the cold rolling to be 60-85%;
(7) Solution treatment: controlling the solid solution treatment temperature to be 550-570 ℃, controlling the solid solution temperature rising rate to be 15-30 ℃/s, controlling the solid solution treatment time to be 1-5 min, and then adopting water cooling.
(8) Pre-ageing: immediately carrying out pre-ageing treatment within 3min, and slowly cooling the aluminum alloy plate from 80-100 ℃ to room temperature at a cooling rate of 1-4 ℃/h to obtain the T4P-state aluminum alloy plate.
It should be noted that the manufacturing steps of comparative examples 1-4 were similar to the present examples, but the process parameters did not conform to the design scope of the present invention.
Table 2-1 and Table 2-2 show specific process parameters of the 6000 series aluminum alloy sheets of examples 1-8 and the aluminum alloy sheets of comparative examples 1-4 in the above process steps.
Table 2-1.
Table 2-2.
In the present invention, the second phase (Mg 2 Si precipitated phase) is sampled on the cold rolled sheet instead of the final finished sheet. This is because: since the recrystallization process occurs during the solution treatment of the cold-rolled sheet, it is necessary to observe the second phase of the cold-rolled sheet by observing the influence of the second relative recrystallization process and the texture thereof.
In the invention, square blocks of 12mm (rolling direction) multiplied by 10mm (transverse direction) are cut from cold-rolled sheet samples corresponding to each example and comparative example, the longitudinal sections of the sheets are ground, and coarse grinding is carried out by sequentially using water-grinding sand paper of 320 meshes, 800 meshes and 1500 meshes; then using 800-mesh metallographic sand paper to make fine grinding, finally polishing longitudinal section of plate material by using polishing cloth, then using Sirion 200 field emission scanning electron microscope to make second phase (i.e. Mg) 2 Si precipitated phase) size and distribution were observed and analyzed, and the results of the relevant observation and analysis are shown in table 3 below.
Table 3 shows the Mg in the cold rolled sheet of examples 1-8 and comparative examples 1-4 2 Average size and area density of Si precipitate phase.
Table 3.
The invention also carries out sampling detection on the grain sizes of the finished T4P-state aluminum alloy plates of each example and comparative example. The specific method comprises the following steps:
rectangular samples of 15mm (rolled direction) ×10mm (transverse direction) were cut from the final T4P-state aluminum alloy sheet material corresponding to each example and comparative example, and the statistical plane was a longitudinal section. The sample is polished by a water mill with water abrasive paper with granularity of 320, 800, 1000 and 1500 and metallographic abrasive paper with granularity of 800 and 1000, and then diamond grinding paste with granularity of 0.5 mu m is smeared on the woolen cloth for mechanical polishing. And (3) performing anode coating on the polished sample by using a direct current power supply. Then, a metallographic photograph is taken under a condition of a magnification of 100 times by using a metallographic microscope, the grain size of the aluminum alloy plate is detected by adopting an intercept method through imageJ software, and the detection results are shown in table 4.
In addition, in order to describe the structure and the relationship between texture and properties, the present invention also samples the final 6000 series aluminum alloy sheets of examples 1 to 8 and the aluminum alloy sheets of comparative examples 1 to 4, respectively, to test the macroscopic texture. The preparation and detection means of XRD macroscopic texture detection samples are as follows:
a square of 15mm (rolled direction). Times.10 mm (transverse direction) was cut from a 1mm thick sample of finished T4P-state aluminum alloy sheet material corresponding to each of examples 1-8 and comparative examples 1-4, and the test surface was a sheet plane. The sample is polished by water abrasive paper and metallographic abrasive paper, the test surface is polished to be close to the thickness center of the plate, then is soaked in 30 percent NaOH aqueous solution for 8 to 15 minutes, and is taken out and then is placed in 10 percent HNO 3 Soaking in the aqueous solution for 5s, taking out the sample, washing with water and drying. Macroscopic texture testing was performed on a Bruker D8 Discover X-ray diffractometer under 40kV tube voltage, 40mA tube current, cuK alpha radiation, ni filtering. Respectively measuring three incomplete pole figures (alpha=0-75 degrees; beta=0-360 degrees) of the {111}, {200}, and {220}, of pure aluminum powder and each sample according to a Shulz reflection method, and corresponding backing with peak centers deviated from delta theta= ±1.4 degrees; back correction and defocus correction were performed with Mtex-4.1.4, and an Orientation Distribution Function (ODF) was calculated. The results of the measurements are shown in Table 4.
In addition, in order to further illustrate the mechanical properties, flanging property and surface quality of the finished 6000 series aluminum alloy plate according to the invention, the invention further samples the obtained finished 6000 series aluminum alloy plates of examples 1-8 and the finished comparative aluminum alloy plates of comparative examples 1-4 again, and tests and evaluates the mechanical properties, flanging property and rib-mark defects of the finished aluminum alloy plates of each example and comparative example.
The related mechanical property detection means are as follows:
the finished T4P-state aluminum alloy plate samples corresponding to each example and comparative example are subjected to room temperature tensile property test after being naturally aged at room temperature for 7 days. Room temperature tensile tests were carried out according to ASTM E8/E8M-16a requirements, room temperature tensile samples being taken from three directions on the finished T4P-state aluminum alloy sheet sample at angles of 0 °, 45 ° and 90 ° with respect to the sheet rolling direction, respectively. Room temperature tensile testing was performed on a MTS810 tensile tester with a controlled draw rate of 2mm/min. Accordingly, the plastic strain ratio r value and the plane anisotropy index Δr value were measured according to the GB/T5027-2007 standard.
The relevant flanging performance evaluation means are as follows:
rectangular samples of 250mm (rolled direction) ×30mm (transverse direction) were cut from the final T4P-state aluminum alloy sheet samples corresponding to each example and comparative example, and the flanging property was evaluated. The flanging performance evaluation was performed according to the requirements of GMW 15421-2018. After the sample is prestretched by 10% along the rolling direction, a rectangular sample with the length of 50mm (rolling direction) multiplied by 30mm (transverse direction) is cut, and then 180-degree bending experiments are carried out by using a pressure head with the radius of 0.6mm, wherein in the experimental process, the distance between supporting rollers is ensured to be 3.0-3.1 mm. The outer surface was rated after bending according to the criteria of the figure: stage 1: the surface is smooth; 2 stages: discontinuous local contraction; 3 stages: microcrack morphology; 4 stages: obvious crack morphology, with grade 1 and grade 2 acceptable and grade 3 and grade 4 unacceptable.
The relevant Luo Pingwen defect evaluation means are as follows:
a rectangular specimen of 250mm (rolled direction). Times.35 mm (transverse direction) was cut out from the final T4P-state aluminum alloy sheet samples corresponding to each of examples 1 to 8 and comparative examples 1 to 4 for Luo Pingwen defect evaluation. Polishing of the Luo Pingwen defect evaluation sample is required to be carried out on a flat workbench surface, firstly, oilpaper is padded below the sample, cleaning is convenient after testing, black ink is uniformly smeared on the surface of the sample, and the volatilization time is waited for 10-15 s. Then polishing the surface of the sample by using a foam cushion with sand paper on the surface, applying slight pressure on the surface of the sample during polishing, polishing for 2-3 times along the rolling direction in one direction generally, and then manually evaluating the level of the rib flat defects: stage 1: the surface is required to have no vertical stripes parallel to the rolling direction; 2 stages: the number of vertical stripes which are allowed to be parallel to the rolling direction on the surface is 1-5; 3 stages: the number of vertical stripes with the surfaces parallel to the rolling direction exceeds 5; 4 stages: the number of vertical stripes with the surface parallel to the rolling direction exceeds 5 cut vertical stripes with a pitch less than 3mm, where grade 1 and grade 2 are acceptable and grade 3 and grade 4 are not acceptable.
Table 4 shows the structure, texture and property measurements of the finished 6000 series aluminum alloy sheets of examples 1-8 and the finished aluminum alloy sheets of comparative examples 1-4.
Table 4.
As shown in tables 3 and 4, the 6xxx sheets prepared according to the process of examples 1-8 meet the requirements of the present invention with Mg having an average size of 1.3 to 1.7 μm in the cold rolled sheet 2 Si precipitated phase surface density not less than 55000 pieces/mm 2 The method comprises the steps of carrying out a first treatment on the surface of the The average grain size of the finished-state plate is 20-32 mu m, the recrystallization texture density is 6.5-10.0, the content of cubic texture components is less than or equal to 8%, and the content of Gaussian texture components is less than or equal to 7%; the performance of the finished-state plate meets the conditions that the tensile strength is more than or equal to 210Mpa, the yield strength is more than or equal to 104Mpa, the elongation is more than or equal to 24%, the plastic strain ratio r value is more than or equal to 0.68, the delta r is less than or equal to 0.10, the flanging grades (the flanging factor is 0.6) are all rated as 1, and the Luo Pingwen grades are all rated as 1. In the comparative examples, however, the 6xxx series plates prepared by the processes of comparative examples 1 to 4 do not satisfy the process range of the present invention, resulting in the following results:
comparative example 1, in which the finish rolling coiling temperature of the finish rolling was 340 ℃ or lower but no intermediate annealing was performed, too many fine second phases were precipitated and the number of coarse second phases was too low, so that the PSN effect of the coarse second phases excited in the subsequent solid solution process was suppressed, and the recrystallized texture density was too high, and the formability of the final sheet was poor (r value was low, Δr value was high); especially, the content of the soft orientation component with the cube texture and the hard orientation component with the Gaussian texture are higher, and the two texture components are gathered and distributed alternately along the rolling direction, so that grains with the hard orientation with the Gaussian texture are not easy to deform and present ridges when 10% pre-stretching is carried out in the direction perpendicular to the rolling direction, and the grains with the soft orientation with the cube texture are easy to deform and thin and present valleys, thereby having the rib defect of high and low fluctuation along the rolling direction.
In comparative example 2, the intermediate annealing temperature was too high, and the second phase was excessively large, so that the size of the coarse second phase was too large, and the coarse second phase was difficult to sufficiently melt back in the subsequent solid solution process, remained in the final product plate, and resulted in an increase in crack sources in the flanging process, and further resulted in poor flanging performance (flanging grade of 4).
Comparative example 3 has a poor flanging property (a flanging grade of 4) because the cold rolling reduction is too low, resulting in an excessively large grain size in the finished plate, and coarse grains promote the generation and propagation of shear bands during the flanging.
Comparative example 4 has too high deformation texture density in cold rolled sheet due to too high cold rolling reduction, and also has high recrystallization texture density in finished sheet due to genetic effect of texture, especially high content of soft orientation component of cubic texture and hard orientation component of gaussian texture, thereby causing serious Luo Pingwen defect (Luo Pingwen defect rating of 3).
Therefore, the 6000 series aluminum alloy plate manufacturing method with high formability, high flanging property and low rib defect can be seen, on one hand, through reasonably regulating and controlling the soaking, hot rolling, coiling and intermediate annealing technological parameters in the processing process, the coarse Mg in the 6000 series aluminum alloy plate is regulated and controlled 2 The size and the number of the Si precipitated phases fully exert coarse Mg 2 PSN effect of Si phase in the subsequent solid solution process, thereby adjusting texture; on the other hand, the texture and the grain size of the finished-state plate are further regulated and controlled by regulating and controlling the cold rolling reduction rate, and finally the recrystallization texture density and the recrystallization texture density of the finished-state plate are weakenedThe purpose of refining the grain size of the finished plate is to further obtain 6000 series aluminum alloy plates with high formability, high flanging property and low rib defect for automobile bodies.
It should be noted that the combination of the technical features in the present invention is not limited to the combination described in the claims or the combination described in the specific embodiments, and all the technical features described in the present invention may be freely combined or combined in any manner unless contradiction occurs between them.
It should also be noted that the above-recited embodiments are merely specific examples of the present invention. It is apparent that the present invention is not limited to the above embodiments, and similar changes or modifications will be apparent to those skilled in the art from the present disclosure, and it is intended to be within the scope of the present invention.
Claims (14)
1. A6000 series aluminum alloy plate manufacturing method with high forming performance, high flanging performance and low rib defect is characterized by comprising the following steps:
(1) Homogenizing the cast ingot at 530-580 ℃;
(2) Directly carrying out hot rough rolling, hot finish rolling and hot finish rolling coiling on the ingot subjected to homogenization treatment, controlling the initial rolling temperature of the hot finish rolling to be 400-480 ℃ and controlling the hot finish rolling coiling temperature to be more than 250 ℃;
(3) Cold rolling: controlling the total deformation of the cold rolling to be 50-85 percent, and obtaining Mg in the cold-rolled sheet 2 The average size of the Si precipitated phase is 1.3-1.7 mu m, mg 2 Si precipitated phase surface density not less than 55000 pieces/mm 2 ；
(4) Solution treatment;
(5) Pre-ageing treatment, and air cooling to obtain 6000 series aluminum alloy plate.
2. The method of manufacturing 6000 series aluminum alloy sheet as set forth in claim 1, wherein in step (2), when the hot finish rolling coiling temperature is 250 to 340 ℃, intermediate annealing is performed before cold rolling in step (3): controlling the temperature of the intermediate annealing to be 350-430 ℃, keeping the temperature for 1-4 hours, and then cooling to room temperature along with a furnace; when the hot finishing rolling coiling temperature is higher than 340 ℃, the step (3) is directly performed without intermediate annealing.
3. The method of manufacturing a 6000 series aluminum alloy sheet as set forth in claim 1, wherein in the step (2), when the intermediate annealing is performed, a temperature rise rate of the intermediate annealing is 13 to 17 ℃/h and a temperature reduction rate of the intermediate annealing is 12 to 15 ℃/h.
4. The method of producing a 6000 series aluminum alloy sheet as claimed in claim 1, wherein in the step (1), the heat-retaining time of the homogenization treatment is 6 to 16 hours.
5. The method of producing a 6000 series aluminum alloy sheet as claimed in claim 1, wherein in the step (1), the homogenization treatment temperature is 550 to 570 ℃.
6. The method of manufacturing 6000 series aluminum alloy sheet as set forth in claim 1, wherein in step (2), the total deformation amount of hot rough rolling is controlled to be more than 70%; and/or the total deformation of the hot finish rolling is more than 80%.
7. The method of producing 6000 series aluminum alloy sheet as claimed in claim 1, wherein in the step (2), the initial rolling temperature of the finish hot rolling is 440 to 480 ℃.
8. The method of manufacturing 6000 series aluminum alloy sheet as set forth in claim 1, wherein in step (3), the total cold rolling deformation is controlled to 60 to 85%.
9. The method of producing a 6000 series aluminum alloy sheet as claimed in claim 1, wherein in the step (4), the solution treatment temperature is 550 to 570 ℃, the solution temperature rise rate is 15 to 30 ℃/s, the solution treatment holding time is 1 to 5 minutes, and the quenching mode is water cooling.
10. The method for manufacturing 6000 series aluminum alloy sheet as claimed in claim 1, wherein in step (5), the pre-aging treatment is performed within 3 minutes.
11. The method of manufacturing 6000 series aluminum alloy sheet as set forth in claim 1, wherein in the step (5), the pre-aging treatment is a slow cooling from 80 to 100 ℃ to room temperature at a cooling rate of 1 to 4 ℃/h.
12. 6000 series aluminum alloy sheet manufactured by the manufacturing method according to any one of claims 1 to 11.
13. 6000 series aluminium alloy sheet according to claim 12, characterized in that it has an average grain size of 20-32 μm, a recrystallisation texture density of 6.5-10.0, a cubic texture content of 8% or less and a gaussian texture content of 7% or less.
14. 6000 series aluminium alloy sheet according to claim 12, wherein the properties thereof are as follows:
the tensile strength is more than or equal to 210MPa, the yield strength is more than or equal to 104MPa, and the elongation is more than or equal to 24%;
the plastic strain ratio r is more than or equal to 0.68, the plane anisotropy index Deltar is less than or equal to 0.10, the flanging grade is 1, and the Luo Pingwen grade is 1.
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| CN104451208A (en) * | 2014-11-28 | 2015-03-25 | 苏州有色金属研究院有限公司 | Manufacturing method for 6XXX-series aluminum alloy plate for automobile body |
| CN105441740A (en) * | 2016-01-12 | 2016-03-30 | 苏州有色金属研究院有限公司 | Autobody 6XXX series aluminium alloy plate with high edge-curling property and manufacturing method thereof |
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| CN111334728A (en) * | 2018-12-19 | 2020-06-26 | 有研工程技术研究院有限公司 | Method for improving flanging performance of aluminum alloy plate |
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| JP4836486B2 (en) * | 2005-04-26 | 2011-12-14 | 住友軽金属工業株式会社 | Al-Mg-Si alloy sheet having excellent deep drawability and method for producing the same |
| CN104018040B (en) * | 2014-06-23 | 2017-08-08 | 北京科技大学 | A kind of automobile high formability aluminum alloy materials |
| CN104372210B (en) * | 2014-12-01 | 2017-11-17 | 北京科技大学 | A kind of automobile using low cost high formability aluminum alloy materials and preparation method thereof |
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| CN104451208A (en) * | 2014-11-28 | 2015-03-25 | 苏州有色金属研究院有限公司 | Manufacturing method for 6XXX-series aluminum alloy plate for automobile body |
| CN105441740A (en) * | 2016-01-12 | 2016-03-30 | 苏州有色金属研究院有限公司 | Autobody 6XXX series aluminium alloy plate with high edge-curling property and manufacturing method thereof |
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| CN111334728A (en) * | 2018-12-19 | 2020-06-26 | 有研工程技术研究院有限公司 | Method for improving flanging performance of aluminum alloy plate |
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