3000 series aluminum alloy and preparation method thereof

Abstract

The invention discloses a 3000 series aluminum alloy and a preparation method thereof, and belongs to the technical field of alloy processing. The 3000 series aluminum alloy has a fine grain structure and a recrystallized grain structure, and the recrystallized grain structure is a P structure and an R-cubeND structure; the recrystallization grain size of the 3000 series aluminum alloy is 50-110 [mu] m, and the length-diameter ratio of the 3000 series aluminum alloy is 0.6-0.8. The invention further discloses a preparation method of the 3000-series aluminum alloy, which comprises the following steps of: performing preheating treatment and cold rolling on an aluminum alloy plate to obtain a pretreated plate; sequentially cutting, cleaning and packaging the pretreated plate, and then carrying out ultrahigh-pressure heat treatment and cooling to obtain the high-strength heat-insulation plate. According to the method, the problem that a 3000-series aluminum alloy fine grain structure and a strong P and R-cubeND texture cannot cooperatively exist can be solved, and a new method is provided for macroscopic texture regulation and control of the aluminum alloy subjected to heat treatment.

Description

Technical Field

[0001] The invention belongs to the technical field of alloy processing, and specifically relates to a 3000 series aluminum alloy and a preparation method thereof. Background Art

[0002] As one of the most widely used non-ferrous metal materials in industrial production, aluminum alloy has excellent corrosion resistance, high specific strength, good formability, low density and excellent thermal and electrical conductivity. Therefore, it is widely used in many engineering fields such as aerospace, construction, automobile industry, transportation industry, electronics industry, chemical industry and food industry.

[0003] 3000 series aluminum alloy is Al-Mn alloy, which is the most widely used rust-proof aluminum. It has low strength and cannot be strengthened by heat treatment. 3000 series aluminum alloy will experience co-precipitation during heat treatment, and the greater the deformation, the greater the impact of co-precipitation, resulting in coarse recrystallized grains (about 200μm). In order to obtain fine recrystallized grain structure, it is necessary to weaken the co-precipitation effect, but this will make the recrystallization texture appear as random texture. It is difficult to obtain fine grain structure of 3000 series aluminum alloy with P and R-cube by current existing technology. ND Texture microstructure. How to obtain fine grain structure in coordination with P and R-cube ND Textured aluminum alloy, further regulating its macro texture to improve the strength performance of 3000 series aluminum alloy after heat treatment is one of the technical difficulties that needs to be solved urgently. Summary of the invention

[0004] The problem to be solved by the present invention is to provide a 3000 series aluminum alloy and a preparation method thereof, so as to solve the problem of fine grain structure of 3000 series aluminum alloy and strong P and R-cube ND It solves the problem of the inability of textures to exist synergistically and provides a new method for controlling the macro texture of aluminum alloys after heat treatment.

[0005] The technical solution adopted to solve the technical problem is to provide a 3000 series aluminum alloy, the 3000 series aluminum alloy has a fine grain structure and a recrystallized grain structure, and the recrystallized texture is a P texture and an R-cube ND Texture: The recrystallized grain size of 3000 series aluminum alloy is 50-110 μm, and the aspect ratio is 0.6-0.8.

[0006] Preferably, the recrystallized grain size of the 3000 series aluminum alloy is 54 μm, and the aspect ratio is 0.73.

[0007] The present invention also provides a method for preparing the above 3000 series aluminum alloy, comprising the following steps:

[0008] (1) preheating and cold rolling the aluminum alloy sheet to obtain a pretreated sheet;

[0009] (2) The pre-treated plate is cut, cleaned and packaged in sequence, and then subjected to ultra-high pressure heat treatment, and then cooled to obtain the product.

[0010] Preferably, the aluminum alloy sheet is CC AA 3003 aluminum alloy.

[0011] Preferably, the preheat treatment comprises the following steps: keeping the 3003 aluminum alloy plate with a thickness of 2 to 3 mm at 450 to 460° C. for 2.5 to 3.5 hours, taking it out and air-cooling it to room temperature.

[0012] More preferably, the preheat treatment comprises the following steps: keeping the 3003 aluminum alloy plate with a thickness of 2.55 mm at 454° C. for 3 hours, taking it out and air-cooling it to room temperature.

[0013] Preferably, the cold rolling comprises the following steps: cold rolling the preheated aluminum alloy sheet to a deformation amount of 85-95%, and after each rolling pass during the cold rolling process, turning the aluminum alloy sheet forward and backward or up and down, with a rolling speed of 0.3-0.5 m / s.

[0014] More preferably, the cold rolling comprises the following steps: cold rolling the preheated aluminum alloy sheet to a deformation amount of 90%, and after each rolling pass during the cold rolling process, flipping the aluminum alloy sheet forward and backward or up and down, with a rolling speed of 0.4 m / s.

[0015] More preferably, the deformation amount of each rolling pass is 8 to 12%.

[0016] More preferably, the amount of rolling deformation per pass is 10%.

[0017] Preferably, the packaging includes the following steps: stacking the cleaned pretreated plate and boron nitride flakes into a boron nitride tube, placing the assembled boron nitride tube into a graphite crucible, sealing both ends with graphite sheets and placing phyllite blocks, and adding conductive steel caps at both ends of the phyllite block to complete the packaging.

[0018] More preferably, the boron nitride sheet, boron nitride tube, graphite crucible, graphite sheet, pyrophyllite block and conductive steel cap are dried for 8 to 15 hours before use.

[0019] Preferably, the pressure of the ultrahigh pressure heat treatment is 2 to 6 GPa, the temperature is 480 to 490° C., the pressure holding time is 1 to 1.5 hours, and the treatment is then water-cooled to room temperature.

[0020] More preferably, the pressure of the ultrahigh pressure heat treatment is 6 GPa, the temperature is 482° C., the pressure holding time is 1 hour, and the treatment is then water-cooled to room temperature.

[0021] More preferably, the heating rate of the ultrahigh pressure heat treatment is 6°C / min.

[0022] The present invention has the following beneficial effects:

[0023] (1) The present invention solves the problem that the traditional 3000 series aluminum alloy microstructure cannot achieve fine grain structure and strong P and R-cube ND The problem of texture synergy; the present invention obtains a P and R-cube with fine grain structure and strong synergy ND The texture microstructure of aluminum alloy provides a new method for controlling the macro texture of aluminum alloy after heat treatment.

[0024] (2) The combined effects of ultrahigh pressure and high temperature in the preparation method of the 3000 series aluminum alloy of the present invention can significantly change the microstructure and texture of the aluminum alloy, promote the redistribution of elements in the alloy and the occurrence of phase change processes, thereby obtaining an aluminum alloy material with a specific texture and grain size. BRIEF DESCRIPTION OF THE DRAWINGS

[0025] Figure 1 This is a schematic diagram of the pre-processed plate packaging;

[0026] Figure 2 TEM image of the 3000 series aluminum alloy prepared in Comparative Example 1;

[0027] Figure 3 This is an EDS surface scan of the 3000 series aluminum alloy prepared in Comparative Example 1; wherein (a) is Al element; (b) is Mn element; (c) is Si element; (d) is Fe element;

[0028] Figure 4 for Figure 2 Elemental analysis diagrams of precipitates No. 1, 2, 3 and 4 in the figure; wherein, (a) is the elemental analysis diagram of precipitate No. 1; (b) is the elemental analysis diagram of precipitate No. 2; (c) is the elemental analysis diagram of precipitate No. 3; (d) is the elemental analysis diagram of precipitate No. 4;

[0029] Figure 5 TEM images of 3000 series aluminum alloys prepared in Examples 1 to 3; wherein (a) is the TEM image of Example 3; (b) is the TEM image of Example 2; (c) is the TEM image of Example 1;

[0030] Figure 6 The metallographic images of the 3000 series aluminum alloys prepared in Examples 1 to 3 and Comparative Example 1; wherein (a) is the metallographic image of the 3000 series aluminum alloy of Comparative Example 1; (b) is the metallographic image of the 3000 series aluminum alloy of Example 3; (c) is the metallographic image of the 3000 series aluminum alloy of Example 2; (d) is the metallographic image of the 3000 series aluminum alloy of Example 1;

[0031] Figure 7 The recrystallized grain size diagram of the 3000 series aluminum alloys prepared in Examples 1 to 3 and Comparative Example 1;

[0032] Figure 8 ODF analysis diagrams of 3000 series aluminum alloys prepared in Examples 1 to 3 and Comparative Example 1; wherein (a) is Comparative Example 1; (b) is Example 3; (c) is Example 2; and (d) is Example 1. DETAILED DESCRIPTION

[0033] In order to make the purpose, technical scheme and advantages of the present invention more clearly understood, the present invention is further described in detail below in conjunction with embodiments. It should be understood that the specific embodiments described herein are only used to explain the present invention and are not used to limit the present invention, that is, the embodiments described are only part of the embodiments of the present invention, rather than all of the embodiments.

[0034] Therefore, the following detailed description of the embodiments of the present invention is not intended to limit the scope of the invention claimed for protection, but merely represents selected embodiments of the present invention. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without making creative work are within the scope of protection of the present invention.

[0035] The features and performance of the present invention are further described in detail below in conjunction with embodiments.

[0036] Example 1

[0037] A 3000 series aluminum alloy, the 3000 series aluminum alloy has a fine grain structure and a recrystallized grain structure, and the recrystallized texture is a P texture and an R-cube ND Texture: The recrystallized grain size of 3000 series aluminum alloy is 54μm and the aspect ratio is 0.73.

[0038] This embodiment also provides a method for preparing the above 3000 series aluminum alloy, comprising the following steps:

[0039] (1) A CC AA 3003 aluminum alloy plate with a thickness of 2.55 mm is used as a raw material and is placed at 454°C for 3 hours, and then air-cooled to room temperature; the preheated aluminum alloy plate is then cold-rolled to a deformation of 90%. After each cold rolling process, the aluminum alloy plate is turned forward and backward or up and down and then rolled for the next pass. The deformation of each pass is 10%, and the rolling speed is 0.4 m / s, thereby obtaining a pretreated plate;

[0040] (2) Cut the pretreated plate into a circular thin plate with a diameter of 10 mm and clean it. After cleaning, stack it with a cubic boron nitride sheet with a diameter of 10 mm and put it into a cubic boron nitride tube with an inner diameter of 10 mm and an outer diameter of 12 mm. Put the assembled cubic boron nitride tube into a graphite crucible with an inner diameter of 12 mm and an outer diameter of 14 mm, seal both ends with graphite sheets and put into a pyrophyllite block, and add conductive steel caps at both ends of the pyrophyllite block to complete the packaging; wherein, the cubic boron nitride sheet, cubic boron nitride tube, graphite crucible, graphite sheet, pyrophyllite block and conductive steel cap need to be placed in a dryer and dried for 12 hours before use;

[0041] (3) The pretreated plate packaged in step (2) is subjected to ultrahigh pressure treatment, firstly the pressure is increased to 6 GPa, then the temperature is increased to 482°C at a heating rate of 6°C / min and kept at this temperature for 1 hour, then cooled to room temperature with water, and then the pressure is released and taken out.

[0042] Packaging structure such as Figure 1 shown.

[0043] Example 2

[0044] A 3000 series aluminum alloy, the 3000 series aluminum alloy has a fine grain structure and a recrystallized grain structure, and the recrystallized texture is a P texture and an R-cube ND Texture: The recrystallized grain size of 3000 series aluminum alloy is 63~88μm, and the aspect ratio is 0.71.

[0045] A method for preparing a 3000 series aluminum alloy comprises the following steps:

[0046] (1) A CC AA 3003 aluminum alloy plate with a thickness of 2.55 mm is used as a raw material and is placed at 454°C for 3 hours, and then air-cooled to room temperature; the preheated aluminum alloy plate is then cold-rolled to a deformation of 90%. After each cold rolling process, the aluminum alloy plate is turned forward and backward or up and down and then rolled for the next pass. The deformation of each pass is 10%, and the rolling speed is 0.4 m / s, thereby obtaining a pretreated plate;

[0047] (2) Cut the pretreated plate into a circular thin plate with a diameter of 10 mm and clean it. After cleaning, stack it with a cubic boron nitride sheet with a diameter of 10 mm and put it into a cubic boron nitride tube with an inner diameter of 10 mm and an outer diameter of 12 mm. Put the assembled cubic boron nitride tube into a graphite crucible with an inner diameter of 12 mm and an outer diameter of 14 mm, seal both ends with graphite sheets and put into a pyrophyllite block, and add conductive steel caps at both ends of the pyrophyllite block to complete the packaging; wherein, the cubic boron nitride sheet, cubic boron nitride tube, graphite crucible, graphite sheet, pyrophyllite block and conductive steel cap need to be placed in a dryer and dried for 12 hours before use;

[0048] (3) The pretreated plate packaged in step (2) is subjected to ultrahigh pressure treatment, firstly the pressure is increased to 4 GPa, then the temperature is increased to 482°C at a heating rate of 6°C / min and kept at this temperature for 1 hour, then cooled to room temperature with water, and then the pressure is released and taken out.

[0049] Example 3

[0050] A 3000 series aluminum alloy, the 3000 series aluminum alloy has a fine grain structure and a recrystallized grain structure, and the recrystallized texture is a P texture and an R-cube ND Texture: The recrystallized grain size of 3000 series aluminum alloy is 67~102μm, and the aspect ratio is 0.65.

[0051] A method for preparing a 3000 series aluminum alloy comprises the following steps:

[0052] (1) A CC AA 3003 aluminum alloy plate with a thickness of 2.55 mm is used as a raw material and is placed at 454°C for 3 hours, and then air-cooled to room temperature; the preheated aluminum alloy plate is then cold-rolled to a deformation of 90%. After each cold rolling process, the aluminum alloy plate is turned forward and backward or up and down and then rolled for the next pass. The deformation of each pass is 10%, and the rolling speed is 0.4 m / s, thereby obtaining a pretreated plate;

[0053] (2) Cut the pretreated plate into a circular thin plate with a diameter of 10 mm and clean it. After cleaning, stack it with a cubic boron nitride sheet with a diameter of 10 mm and put it into a cubic boron nitride tube with an inner diameter of 10 mm and an outer diameter of 12 mm. Put the assembled cubic boron nitride tube into a graphite crucible with an inner diameter of 12 mm and an outer diameter of 14 mm, seal both ends with graphite sheets and put into a pyrophyllite block, and add conductive steel caps at both ends of the pyrophyllite block to complete the packaging; wherein, the cubic boron nitride sheet, cubic boron nitride tube, graphite crucible, graphite sheet, pyrophyllite block and conductive steel cap need to be placed in a dryer and dried for 12 hours before use;

[0054] (3) The pretreated plate packaged in step (2) is subjected to ultrahigh pressure treatment, firstly the pressure is increased to 2 GPa, then the temperature is increased to 482°C at a heating rate of 6°C / min and kept at this temperature for 1 hour, then cooled to room temperature with water, and then the pressure is released and taken out.

[0055] Comparative Example 1

[0056] A method for preparing a 3000 series aluminum alloy comprises the following steps:

[0057] (1) A CC AA 3003 aluminum alloy plate with a thickness of 2.55 mm is used as a raw material and is placed at 454°C for 3 hours, and then air-cooled to room temperature; the preheated aluminum alloy plate is then cold-rolled to a deformation of 90%. After each cold rolling process, the aluminum alloy plate is turned forward and backward or up and down and then rolled for the next pass. The deformation of each pass is 10%, and the rolling speed is 0.4 m / s, thereby obtaining a pretreated plate;

[0058] (2) The pretreated plate was placed in a muffle furnace for atmospheric pressure heat treatment at a temperature of 482°C, a heating rate of 6°C / min, a holding time of 1h, and then water-cooled.

[0059] Experimental example

[0060] 1. Metallographic structure observation of the 3000 series aluminum alloys obtained in the above Examples 1 to 3 and Comparative Example 1

[0061] The 3000 series aluminum alloy obtained in Examples 1 to 3 and Comparative Example 1 was cut into appropriate sizes on the rolling direction-normal surface using electric spark wire cutting, and metallographic specimens were prepared using cold mounting technology. The metallographic specimens were first coarsely ground with sandpaper, and then mechanically polished on a polishing machine using a diamond grinding paste with a particle size of 2.5 μm. The mechanically polished specimens were electrolytically polished and subsequently anodic coated on an Electromet 4 electrolytic polishing and etching instrument. The solution components and ratios used in the electrolytic polishing and anodic coating processes are shown in Tables 2 and 3, respectively. The metallographic structure of the coated metallographic specimens was observed using an Axiovert 200MAT metallographic microscope under polarized light.

[0062] Table 2 Electrolytic polishing liquid composition and process parameters

[0063]

[0064] Table 3 Anode coating liquid composition and process parameters

[0065]

[0066] 2. Characterization and analysis of the 3000 series aluminum alloys obtained in Examples 1 to 3 and Comparative Example 1

[0067] The precipitates of the sample were observed using a transmission electron microscope of model Talos-F200X with an acceleration voltage of 200kV. The observation surface of the TEM sample is the rolling-transverse plane. First, a 10mm×10mm square block is cut on the rolling-transverse plane of the sample using electric spark wire cutting. The sample is evenly polished from both sides with sandpaper to obtain a thin slice close to the middle layer with a thickness of about 50μm. A circular disc with a diameter of 3mm is punched out with a puncher and double-sprayed on a Struers TenuPol-5 electrolytic double-spray instrument. The solutions and test parameters used for double spraying are shown in Table 4. The sample obtained after double spraying was thinned at a small angle using an ion thinning instrument (Ganta 691) to remove the oxides produced during double spraying. The acceleration voltage is 200kV. The EDS energy spectrum analysis system on the Talos-F200X transmission electron microscope is used for point analysis and surface scanning of elements. EDS analysis can obtain the elemental composition of the precipitates and the content of each element. The results are shown in Figures 2 to 5 shown.

[0068] Table 4 Double spray liquid composition and process parameters

[0069]

[0070] Combination Figures 2 to 5 It can be seen that the morphology of the precipitated phase and EDS analysis of the CC 3003 aluminum alloy sheet with 90% deformation annealed at 482℃ for 1h under different pressures. Figure 2 It can be seen that the precipitation phase of the plate annealed at normal pressure contains large-sized precipitation phase (1-3 μm) and fine precipitation phase (50-150 nm). The large-sized precipitation phase includes the initial precipitation phase before heat treatment and the secondary precipitation phase precipitated during heat treatment. Figure 3 The elemental analysis surface scans of Al, Mn, Si and Fe in 2 are given. It can be seen that the distribution of Mn and Fe is almost the same, and the number density of Mn and Fe is very high in the large precipitation phase area (Mn-rich area), but the number density is very low in the fine precipitation phase area (Mn-poor area). Different from this, the distribution of Si is relatively discrete and uniform. Figure 4 Given from Figure 2 The elemental analysis diagram of four representative precipitates selected from the above graphs shows that the four precipitates belong to Al6(Mn,Fe) phase and α-Al(Mn,Fe)Si phase. It is worth noting that when the pressure increases from normal pressure to 2 GPa, the fine precipitate phase disappears, such as Figure 5 (a), the same phenomenon also occurs in the plates annealed at 4 GPa and 6 GPa ( Figure 5(b) and (c)). In addition, with the increase of pressure, the number of large-sized precipitates increases and the particle size decreases; when the pressure increases to 6 GPa, the number of precipitates after annealing is large, and the particle size is 0.5-1.5 μm ( Figure 5 (c)).

[0071] At the beginning of the heating process of high pressure heat treatment, the annealing temperature is low, so the diffusion coefficient is very low, which makes the nucleation of the precipitation phase in the Mn-poor area very difficult. As the annealing temperature continues to increase, more and more Mn precipitates from the solid solution, and the diffusion coefficient of Mn in the Al matrix continues to increase, so new precipitation phases continue to precipitate from the matrix, and the precipitation process slowly extends to the Mn-poor area. However, due to the scarcity of Mn elements and insufficient time to grow, the size of the particles in the Mn-poor area is very small. After pressurization, the diffusion coefficient decreases, making it difficult for the fine precipitation phase in the Mn-poor area to nucleate, so the number of fine precipitation phases in the plate annealed under high pressure decreases sharply. With the further increase of pressure, the diffusion coefficient of atoms continues to decrease, and long-range diffusion is hindered, resulting in a decrease in the size of large particle precipitation phases. On the other hand, pressurization before heating is a cold deformation process. As the pressure increases, the degree of deformation becomes greater and greater, resulting in more serious lattice distortion, which provides a driving force for the nucleation of the precipitation phase in the Mn-rich area. At the same time, the cold deformation caused by pressurization also leads to an increase in dislocations in the plate. Dislocations are channels for the precipitation of solute atoms, which also leads to an increase in the nucleation rate of the precipitated phase. In summary, after pressurization, the fine precipitated phase disappears, the number of large-particle precipitated phases increases, but the particle size decreases.

[0072] 3. Metallographic and texture analysis of the 3000 series aluminum alloys obtained in Examples 1 to 3 and Comparative Example 1

[0073] The texture of the cold-rolled and annealed samples was tested by X-ray diffraction using a Rigaku D / Max-2500. During the cold rolling process, the surface of the sample will undergo shear deformation due to the friction between the sample and the roller. Therefore, the sample for the texture test needs to be sanded off 1 / 4 of the layer to ensure the accuracy of the texture. The diffraction source of the X-ray is Cu target Kα radiation, and its characteristic wavelength λ is The test voltage is 40 kV, the working current is 200 mA, and the present invention uses the Schulz backscattering method to measure the pole figures of the three crystal planes (111), (200) and (220), and the maximum tilt angle is 75°. Figures 6 to 8 shown.

[0074] from Figure 6 It can be seen that the pressure during the preparation process has a great influence on the microstructure. Figure 7The changes in the recrystallized grain size along the RD and ND directions of the plate with 90% deformation annealed at 482℃ for 1h under different pressures are given. It can be seen that as the pressure increases from normal pressure to 2GPa, the recrystallized grain size along the RD direction decreases rapidly, while when the pressure increases from 2GPa to 6GPa, the recrystallized grain size along the RD direction decreases slowly; in contrast, when the pressure increases from normal pressure to 2GPa, the recrystallized grain size along the ND direction increases significantly, and then decreases slowly as the pressure increases from 2GPa to 6GPa.

[0075] After high pressure heat treatment, the elongated recrystallized grains disappeared, and the recrystallized grains were approximately equiaxed. As the pressure increased from normal pressure to 6GPa, the aspect ratio increased from 0.18 to 0.73. This can be attributed to the sharp decrease in the number of fine precipitated phases after pressurization, which led to the weakening of the pinning effect, so that the recrystallized grains can grow normally. At the same time, as the pressure increased from 2GPa to 6GPa, the size of the recrystallized grains along the RD and ND directions decreased. During the high pressure heat treatment process, the pressurization before heating is a cold deformation process, and with the increase of pressure, the degree of deformation is greater, which leads to the formation of a large number of dislocations in the plate, providing a position for the recrystallization nucleation in the subsequent annealing process, so the nucleation rate (N) increases. On the other hand, high pressure reduces the atomic diffusion coefficient, interface migration rate and orientation difference between small-angle subgrain boundaries, resulting in a decrease in the growth rate (G) of recrystallized grains.

[0076] Combination Figure 8 It can be seen that the recrystallization textures of CC 3003 aluminum alloy sheets with 90% deformation annealed at 482℃ for 1h under different pressures are mainly P, R-cube ND It can be seen that pressure has a strong effect on the recrystallization texture. As the pressure increases from normal pressure to 2 GPa, the strength of the M texture decreases significantly, and as the pressure further increases, the strength of the M texture remains almost unchanged, while the P texture and R-cube ND The strength of the texture increases significantly with increasing pressure.

[0077] During the annealing process of CC 3003 aluminum alloy, the recrystallization texture M is caused by co-precipitation and is very sensitive to co-precipitation, while high pressure can limit co-precipitation ( Figures 2 to 5 ), so the M texture is significantly weakened after pressurization. The formation of P-oriented grains is more likely to occur near the coarse precipitates distributed along the RD direction. During the high-pressure heat treatment, the plate with large deformation amount undergoes severe plastic deformation during the pressurization process before heating, which reduces the critical particle size of the PSN mechanism. In addition, high pressure can refine the size of the large particle precipitation phase ( Figures 2 to 5), which leads to the prevalence of PSN mechanism, so that the plate finally forms a strong P texture and R-cube ND Texture.

[0078] In summary, the present invention obtains a fine-grained structure with P and R-cube by ultra-high pressure heat treatment of CC AA 3003 aluminum alloy. ND The present invention effectively solves the problem of fine grain structure of 3000 series aluminum alloy and strong P and R-cube ND It solves the problem of the inability of textures to exist synergistically and provides a new method for controlling the macro texture of aluminum alloys after heat treatment.

[0079] The present invention has been described according to the above embodiments. It should be understood that the above embodiments do not limit the present invention in any form. Any technical solutions obtained by equivalent replacement or equivalent transformation shall fall within the scope of the present invention.

Claims

1. A 3000 series aluminum alloy, characterized in that: The 3000 series aluminum alloy has a fine grain structure and a recrystallized grain structure, and the recrystallized texture is a P texture and an R-cube texture. ND Texture; The recrystallized grain size of the 3000 series aluminum alloy is 50 to 110 μm, and the aspect ratio is 0.6 to 0.

8.

2. The 3000 series aluminum alloy according to claim 1, characterized in that: The recrystallized grain size of the 3000 series aluminum alloy is 54 μm, and the aspect ratio is 0.

73.

3. The method for preparing the 3000 series aluminum alloy according to any one of claims 1 to 2, characterized in that: The following steps are involved: (1) preheating and cold rolling the aluminum alloy sheet to obtain a pretreated sheet; (2) The pre-treated plate is cut, cleaned and packaged in sequence, and then subjected to ultra-high pressure heat treatment, and then cooled to obtain the product.

4. The method for preparing the 3000 series aluminum alloy according to claim 3, characterized in that: The preheating treatment comprises the following steps: keeping a 3003 aluminum alloy plate with a thickness of 2 to 3 mm at 450 to 460° C. for 2.5 to 3.5 hours, taking it out and air cooling it to room temperature.

5. The method for preparing the 3000 series aluminum alloy according to claim 3, characterized in that: The cold rolling comprises the following steps: cold rolling the preheated aluminum alloy sheet to a deformation amount of 85-95%, and turning the aluminum alloy sheet forward and backward or up and down after each rolling process during the cold rolling process, with a rolling speed of 0.3-0.5 m / s.

6. The method for preparing the 3000 series aluminum alloy according to claim 5, characterized in that: The cold rolling comprises the following steps: cold rolling the preheated aluminum alloy sheet to a deformation amount of 90%, and turning the aluminum alloy sheet forward and backward or upward and downward after each rolling process during the cold rolling process, with a rolling speed of 0.4 m / s.

7. The method for preparing the 3000 series aluminum alloy according to claim 3, characterized in that: The packaging comprises the following steps: stacking the cleaned pre-treated plate and the boron nitride sheet into a boron nitride tube, placing the assembled boron nitride tube into a graphite crucible, sealing both ends with graphite sheets and placing pyrophyllite blocks, and adding conductive steel caps at both ends of the pyrophyllite block to complete the packaging.

8. The method for preparing the 3000 series aluminum alloy according to claim 7, characterized in that: The boron nitride sheet, boron nitride tube, graphite crucible, graphite sheet, pyrophyllite block and conductive steel cap are dried for 8 to 15 hours before use.

9. The method for preparing the 3000 series aluminum alloy according to claim 3, characterized in that: The ultra-high pressure heat treatment is performed at a pressure of 2 to 6 GPa, a temperature of 480 to 490° C., a pressure holding time of 1 to 1.5 hours, and water cooling to room temperature after pressure holding.

10. The method for preparing the 3000 series aluminum alloy according to claim 9, characterized in that: The ultra-high pressure heat treatment is performed at a pressure of 6 GPa, a temperature of 482° C., a pressure holding time of 1 hour, and water cooling to room temperature after pressure holding.

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