WO2023103787A1 - Aluminum alloy material, preparation method therefor, and application thereof - Google Patents

Aluminum alloy material, preparation method therefor, and application thereof Download PDF

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WO2023103787A1
WO2023103787A1 PCT/CN2022/133871 CN2022133871W WO2023103787A1 WO 2023103787 A1 WO2023103787 A1 WO 2023103787A1 CN 2022133871 W CN2022133871 W CN 2022133871W WO 2023103787 A1 WO2023103787 A1 WO 2023103787A1
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aluminum alloy
alloy material
particles
electron microscope
scanning electron
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PCT/CN2022/133871
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French (fr)
Chinese (zh)
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丁小理
罗杰
刘志成
周武军
李建湘
李信
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广东和胜工业铝材股份有限公司
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Publication of WO2023103787A1 publication Critical patent/WO2023103787A1/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/10—Alloys containing non-metals
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • 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
    • C22F1/057—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 copper as the next major constituent

Definitions

  • the invention belongs to the technical field of aluminum alloys, and in particular relates to an aluminum alloy material and its preparation method and application.
  • Aluminum alloy has many characteristics such as light specific gravity, high specific strength, good heat dissipation, easy processing, excellent anodic oxidation decoration effect, and recyclable reuse, so it is widely used in the manufacture of various commodities.
  • As a commonly used material for 3C structural parts in order to give more room for mobile phone internal structure designers, and due to the lightweight requirements of mobile phones, it is required to further increase the yield strength of materials in order to meet the structural strength test requirements of complete mobile phone parts. At the same time, customers are also very concerned about the appearance of mobile phones.
  • the surface treatment is mostly high-brightness anodizing, which can be dyed in various colors, and the oxide film is transparent and shiny. After oxidation, the finished product needs to be tested for salt spray and acid-base reliability, and there must be no film bursting or cracking.
  • the main strengthening phases Mg 2 Si, free Si, and CuAl 2 in 6-series alloys have a positive effect on the strength when dispersed and precipitated, and when the amount exceeds a certain amount, the color and permeability of the oxide film will be seriously deteriorated;
  • the temperature range between its solvus and solidus is about 20°C.
  • the temperature range between the solvus line and the solidus line is about 10°C, and it is extremely easy to appear over-burned structure or insufficient solid solution during the production process; (3)
  • the hardness of the over-burned product is high, because The flow rate is different from that of aluminum, and it will be elongated, forming strip defects in the extruded material. These impurity phases dissolve and fall off during the oxidation process, leaving pits at the falling position, visually presenting black line-like defects, resulting in anodic effects that cannot meet customer needs.
  • Large particles with insufficient solid solution (larger than 1 ⁇ m) have a large difference in electrochemical performance from the substrate.
  • the 6-series alloy only relies on the control of alloy content, and its yield strength is up to 400MPa. If higher strength is required, and it can meet the needs of 3C products with small stress deformation and bright and transparent anodizing effect under the condition of multi-process and large-scale processing of 3C products, it must be completed through innovation of alloy composition and process conditions.
  • the 7-series alloy can easily achieve a strength of 500MPa, or even more than 600MPA, due to the high composition of the 7-series alloy, anodic oxidation is prone to cracking defects, so it cannot be used on high-brightness anodized mobile phone casings. Therefore, it is necessary to develop aluminum alloy materials with a yield strength of more than 450MPa and suitable for high-brightness anodic oxidation.
  • This type of product can be widely used in 3C products that require high material structural strength, low material residual stress and good surface treatment performance. 5G and future 6G requirements.
  • the present invention aims to solve at least one of the above-mentioned technical problems existing in the prior art. For this reason, the invention provides an aluminum alloy material, the yield strength of the aluminum alloy material is greater than 450MPa and the surface treatment performance is good.
  • the present invention also provides a preparation method of the above-mentioned aluminum alloy material.
  • the present invention also provides the application of the above-mentioned aluminum alloy material.
  • the first aspect of the present invention provides an aluminum alloy material prepared from the following components in mass percentage.
  • Si 0.30% to 0.80%.
  • the balance is Al.
  • the aluminum alloy material contains free Si, the mass percentage of the free Si is 0.06-0.35%, and the calculation method of the free Si is: Si%-Mg% ⁇ 0.578.
  • Si exists in the form of Mg 2 Si and free Si.
  • Si and Mg form Mg 2 Si
  • Mg: Si composition content 24.3 ⁇ 2/28.09, that is, when the Si content is 1%, the Mg required to form Mg 2 Si is 1.73%, therefore, the calculation of free Si
  • the aluminum alloy material of the present invention through the design of the alloy composition, enables the material to have good surface treatment and performance while the yield strength is greater than 450 MPa.
  • the aluminum alloy material of the present invention has small stress deformation after being processed by a numerically controlled lathe. Taking the finished product of the middle frame of a straight mobile phone with a length of 170mm x width 80mm x thickness 7mm as an example, the flatness can be controlled within 0.15.
  • the aluminum alloy material of the present invention has no trailing lines when the aluminum alloy is mechanically polished, the oxide film is transparent, and the high-quality anodic oxidation effect of high brightness can be realized.
  • Si and Mg elements are the main alloy elements forming the strengthening phase, and the strength of the material is controlled by the formed Mg 2 Si, and the maximum solid solubility of Mg 2 Si in the aluminum matrix is 1.85%.
  • the total amount of Mg 2 Si is closer to 1.85%, its solid solution temperature and solidus temperature are very close, which is difficult to control in extrusion industrial production. If the temperature is too low, the solid solution is insufficient, and Mg 2 Si cannot function well. If the temperature is too high and exceeds the solidus temperature of the material, cracking will occur during extrusion.
  • Si is controlled at 0.3-0.8%, and Mg is controlled at 0.35-0.90%, so the total amount of Mg 2 Si can be controlled to be less than 1.494%, which effectively ensures the mass production of the process window.
  • a certain amount of free Si is set in the material, and the total amount of free Si is controlled at 0.09-0.35%, which can be used as the nucleation core of the strengthening precipitation phase during the aging treatment, so that the strengthening precipitation phase is finely dispersed and evenly distributed. If the total amount of free Si exceeds 0.35%, the elongation of the extruded profile will be seriously reduced, resulting in cracking in subsequent cold working and low elongation of the final product.
  • the Cu content is controlled at 0.90-2.2%, and an appropriate amount of Cu is added to form a CuAl 2 phase, so as to significantly improve the age hardening performance of the material.
  • the solid solubility of Fe in aluminum alloy is low, and Fe is an impurity element of the raw material, which inevitably exists.
  • the large granular and long Fe phase affects the anodic oxidation effect.
  • an appropriate amount of Mn is added to effectively promote the transformation of the needle-shaped Fe-containing phase into the spherical Fe-phase.
  • the Fe control is ⁇ 0.09%, and the Mn content is controlled at 0.05%-0.15%.
  • the spheroidization rate of Fe phase is improved.
  • B as an impurity element in the raw material aluminum ingot, inevitably exists.
  • an appropriate amount of Ti-B refiner is added during the alloy casting process.
  • the B content exceeds a certain range, it is very easy to form TiB particle agglomeration, as a hard phase, it is easy to embed into the softer aluminum alloy matrix during subsequent mechanical polishing of the aluminum alloy profile, resulting in the appearance of lines.
  • Ti is controlled at 0.0020-0.0150%, and B is controlled at ⁇ 0.0050%.
  • the content of boron element is ⁇ 0.0050%
  • the content of iron element is ⁇ 0.09%
  • the content of a single impurity element is ⁇ 0.03%
  • the total content of impurity elements is ⁇ 0.15%.
  • Mg 2 Si particles are precipitated at the nanoscale to the greatest extent. Under the 100 times field of view of the scanning electron microscope, no white Mg 2 Si particles with a length exceeding 5 ⁇ m appear; and no more than 5 Mg 2 Si particles with a length of 2-5 ⁇ m.
  • Mg 2 Si belongs to strengthening phase particles, and its constituent elements are Mg and Si.
  • the number exceeding 2 ⁇ m is no more than 5.
  • the length of the Fe phase particles is ⁇ 7 ⁇ m, and the number of Fe phase particles exceeding 3 ⁇ m is no more than 10.
  • Fe phase particles belong to insoluble impurity particles.
  • the length of the TiB phase particles is ⁇ 3 ⁇ m, and the number of particles exceeding 2 ⁇ m under the 100x field of view of the scanning electron microscope is no more than 2.
  • the main component of TiB phase particles is TiB.
  • the yield strength of the aluminum alloy material is ⁇ 450 MPa.
  • a second aspect of the present invention provides a method for preparing the above-mentioned aluminum alloy material, including the following steps.
  • the melting temperature of the aluminum ingot is 740°C-780°C.
  • step S2 after adding a refining agent for refining, argon gas is introduced to refine the aluminum alloy liquid, the slag is removed, and the aluminum alloy liquid II is obtained.
  • step S3 the online grain refinement can be realized by adding a conventional grain refiner.
  • step S4 after the aluminum alloy liquid III is filtered, the aluminum alloy liquid IV is obtained by degassing through the double box of the launder, 80ppi ceramic filter plate + a tubular filter above RC level , and then cast and homogenize the aluminum alloy liquid IV.
  • the casting temperature is 700°C to 730°C.
  • the homogenization treatment method is as follows: first heat the material to 480°C-500°C, keep it warm for 2h-6h, continue to raise the temperature to 550°C-575°C, and keep it warm for 12h-24h.
  • the method further includes, after step S4, performing a molding treatment on the material.
  • the method of forming treatment is.
  • the temperature of the cast rod on the machine is controlled at 520°C to 560°C, the extrusion ratio is greater than 20, and the cast rod is extruded.
  • the temperature at the extrusion outlet is controlled at 530°C to 570°C, and quenched and cooled by passing through water within 60s to obtain an extruded profile.
  • the deformation of the cold deformation processing area is controlled at 4% to 15%.
  • the calculation method of the deformation of the cold processing area is: (cross-sectional area before cold processing-cross-sectional area after cold processing)/cross-sectional area before cold processing.
  • Aluminum alloy can improve product strength through cold work hardening.
  • a certain amount of cold working is applied to improve the strength and ensure the anodic oxidation effect.
  • the cold deformation processing in the preparation method includes but is not limited to drawing, rolling, forging and other modes of deformation processing at normal temperature.
  • the cold deformation processing in the preparation method includes but is not limited to drawing, rolling, forging and other modes of deformation processing at normal temperature.
  • Fig. 1 is the scanning electron microscope detection result of the microscopic morphology of the aluminum alloy material prepared in Example 1.
  • Fig. 2 is the scanning electron microscope detection result of the microscopic morphology of the aluminum alloy material prepared in Comparative Example 1.
  • an aluminum alloy material is prepared from the following components.
  • Si 0.65%, Mg: 0.7%, Cu: 1.8%, Mn: 0.12%, Ti: 0.012%, B: 0.004%, Fe: 0.08%, and the balance is Al.
  • the content of a single impurity element is ⁇ 0.03%, and the total content of impurity elements is ⁇ 0.15%.
  • the specific preparation method is as follows.
  • W -713-3 Refining Agent or Pyrique's PROMAG Ri refining agent can be used, which belongs to sodium salt and potassium salt refining agent.
  • the aluminum alloy liquid III is degassed through the double box of the launder, and the 80ppi ceramic filter plate + the tubular filter above the RC level is obtained to obtain the aluminum alloy liquid IV.
  • the aluminum alloy liquid IV was cast at 710° C. to obtain aluminum alloy cast rods.
  • the aluminum alloy casting rod was homogenized, and the specific process was: heating up to 480° C. for 6 hours and then continuing to heat up to 570° C. for 16 hours to obtain the aluminum alloy casting rod A.
  • the aluminum alloy cast rod A is heated, and the temperature is kept at 530-570° C. for 1 hour.
  • the temperature of the cast rod is controlled at 540-550°C, the extrusion ratio is 40, and the cast rod is extruded.
  • the extrusion outlet temperature is controlled at 550-570°C, and quenched and cooled through water within 60 seconds to obtain an extruded profile.
  • the heating of the cast rod is a process of gradually increasing the temperature.
  • the length of the material extruded by each cast rod is about 50m. Because of the frictional heating, the temperature of the head and tail actually has a process of change, so the above The temperature is set as a temperature interval.
  • the deformation of the cold deformation processing area is controlled at 13% to 15%.
  • Example 2 an aluminum alloy material is prepared, the difference from Example 1 is that the magnesium content is 0.86%.
  • Example 2 an aluminum alloy material is prepared, the difference from Example 1 is that the silicon content is 0.74%.
  • Example 1 an aluminum alloy material is prepared, the difference from Example 1 is that the content of copper is 0.9%.
  • an aluminum alloy material is prepared, which differs from the embodiment 1 in that the content of manganese is 0.05%.
  • an aluminum alloy material is prepared, which differs from that in Embodiment 1 in that the content of boron is 0.001%.
  • an aluminum alloy material is prepared from the following components.
  • Si 0.65%, Mg: 0.7%, Cu: 1.8%, Mn: 0.12%, Ti: 0.012%, B: 0.004%, Fe: 0.08%, and the balance is Al.
  • the content of a single impurity element is ⁇ 0.03%, and the total content of impurity elements is ⁇ 0.15%.
  • the specific preparation method is as follows.
  • the aluminum alloy liquid III is degassed through the double box of the launder, and the 80ppi ceramic filter plate + the tubular filter above the RC level is obtained to obtain the aluminum alloy liquid IV.
  • the aluminum alloy liquid IV was cast at 710° C. to obtain aluminum alloy cast rods.
  • the aluminum alloy casting rod was homogenized, and the specific process was: heating up to 480° C. for 6 hours and then continuing to heat up to 570° C. for 16 hours to obtain the aluminum alloy casting rod A.
  • the aluminum alloy cast rod A is heated, and the temperature is kept at 530-570° C. for 1 hour.
  • the temperature of the cast rod on the machine is controlled at 520-530°C, the extrusion ratio is 40, and the cast rod is extruded.
  • the extrusion outlet temperature is controlled at 540-560°C, and quenched and cooled through water within 60 seconds to obtain an extruded profile.
  • the deformation of the cold deformation processing area is controlled at 13% to 15%.
  • This example prepares an aluminum alloy material.
  • the difference from Example 1 is that during the preparation process, during the preheating treatment of the profile, the extruded material is preheated and heated to 160° C. for 2 hours.
  • This example prepares an aluminum alloy material, and the difference from Example 1 lies in that during the preparation process, the profile is cold deformed, and the deformation of the cold deformed area is controlled at 4% to 5.5%.
  • an aluminum alloy material is prepared.
  • the difference from Example 1 is that the aluminum alloy material is prepared from the following components.
  • Si 0.3%, Mg: 0.35%, Cu: 2.2%, Mn: 0.12%, Ti: 0.012%, B: 0.004%, Fe: 0.08%, and the balance is Al.
  • the content of a single impurity element is ⁇ 0.03%, and the total content of impurity elements is ⁇ 0.15%.
  • Example 2 an aluminum alloy material is prepared, the difference from Example 1 is that the silicon content is 0.25%.
  • Example 2 an aluminum alloy material is prepared, the difference from Example 1 is that the content of Mg is 0.30%.
  • the content of free Si exceeds the range of 0.09-0.35% limited by the present invention.
  • Example 1 an aluminum alloy material is prepared, the difference from Example 1 is that the content of copper is 0.8%.
  • Example 2 an aluminum alloy material is prepared, the difference from Example 1 is that the content of boron is 0.0.006%.
  • Example 2 an aluminum alloy material is prepared, one of the differences from Example 1 is that the content of titanium is 0.02%.
  • the second difference is that among the Al-Ti-B refiners, 90% of TiB 2 single particle diameters are less than 3 ⁇ m, and some of them are agglomerated.
  • Example 2 an aluminum alloy material is prepared.
  • the difference from Example 1 is that the aluminum alloy cast rod is directly heated to 570° C. for 16 hours during homogenization treatment.
  • Example 2 an aluminum alloy material is prepared.
  • the temperature of the casting rod on the machine is controlled at 500-520° C., and the extrusion ratio is 40, and the casting rod is extruded.
  • the extrusion outlet temperature is controlled at 520-540°C, and quenched and cooled through water within 60 seconds to obtain an extruded profile.
  • Example 1 an aluminum alloy material is prepared, and the difference from Example 1 is that during the cold deformation process of the profile, the deformation amount of the cold deformation processing area is controlled at 16%-17%.
  • Example 2 an aluminum alloy material is prepared.
  • the difference from Example 1 is that during the artificial aging treatment of the profile, the cold-processed aluminum alloy profile is heated to 180° C. for 2 hours.
  • Example 1 an aluminum alloy material is prepared, and the difference from Example 1 is that no preheating treatment is performed during the profile extrusion process.
  • the aluminum alloy materials prepared in the examples and the comparative examples were polished, and it was observed whether there was a trailing line defect.
  • the aluminum alloy materials prepared in the examples and the comparative examples were machined with a numerical control machine tool. Specifically, the materials were processed into a straight mobile phone middle frame with a length of 170mm x width 80mm x thickness 7mm, and the flatness was tested.
  • the anodic oxidation surface treatment was carried out on the middle frame of the straight mobile phone, and the appearance and performance of the oxide film were observed.
  • the aluminum alloy material prepared in Comparative Example 2 cracked at the edge during the cold working process.
  • the microstructure and morphology of the aluminum alloy materials prepared in the examples and comparative examples were observed with a scanning electron microscope. The specific situation is.
  • Example 1 The maximum length of Mg 2 Si particles is 2 ⁇ m, and under the 100 times field of view of the scanning electron microscope, there are 0 particles exceeding 2 ⁇ m.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • the morphology of the particles prepared in Example 1 is shown in Figure 1.
  • Example 2 The maximum length of Mg 2 Si particles is 3 ⁇ m, and under the 100 times field of view of the scanning electron microscope, no more than 2 particles exceed 2 ⁇ m.
  • the maximum length of Fe phase particles is 4 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Example 3 The maximum length of Mg 2 Si particles is 1.8 ⁇ m, and the number of particles exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Example 4 The maximum length of Mg 2 Si particles is 2 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 2 ⁇ m is 0.
  • the maximum length of Fe phase particles is 4 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Example 5 The maximum length of Mg 2 Si particles is 2 ⁇ m, and the number of particles exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • the maximum length of Fe phase particles is 6 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m does not exceed 7.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Example 6 The maximum length of Mg 2 Si particles is 2 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 2 ⁇ m is 0.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the TiB phase, Ti particles and B particles could not be found.
  • Example 7 The maximum length of Mg 2 Si particles is 3 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the maximum number of particles exceeding 2 ⁇ m is 3.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Example 8 The maximum length of MgSi particles is 2 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 2 ⁇ m is 0.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Example 9 The maximum length of Mg 2 Si particles is 2 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 2 ⁇ m is 0.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Example 10 Mg 2 Si particles cannot be observed under a scanning electron microscope with a field of view of 100 times.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Comparative Example 1 No Mg 2 Si particles could be observed under the 100 ⁇ field of view of the scanning electron microscope.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • the morphology of the particles prepared in Comparative Example 1 is shown in FIG. 2 .
  • Comparative Example 2 No Mg 2 Si particles could be observed under the 100 ⁇ field of view of the scanning electron microscope.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Comparative example 3 the maximum length of Mg 2 Si particles is 2 ⁇ m, and under the 100 times field of view of the scanning electron microscope, there are 0 particles exceeding 2 ⁇ m.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of the TiB phase and Ti particles does not exceed 1 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Comparative example 4 the maximum length of Mg 2 Si particles is 2 ⁇ m, and the number of particles exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of TiB phase and Ti particles is 4 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Comparative example 5 the maximum length of Mg 2 Si particles is 2 ⁇ m, and the number of particles exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of TiB phase and Ti particles is 5 ⁇ m, and the number of them exceeds 2 ⁇ m under the 100 times field of view of the scanning electron microscope.
  • Comparative example 6 the maximum length of Mg 2 Si particles is 2 ⁇ m, and under the 100 times field of view of the scanning electron microscope, there are 0 particles exceeding 2 ⁇ m.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of TiB phase and Ti particles is 1 ⁇ m, and the number of them exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • Comparative example 7 the maximum length of Mg 2 Si particles is 7 ⁇ m, and under the 100 times field of view of the scanning electron microscope, there are 20 particles exceeding 2 ⁇ m.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of TiB phase and Ti particles is 1 ⁇ m, and the number of them exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • Comparative Example 8 The maximum length of MgSi particles is 2 ⁇ m, and the number of particles exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of TiB phase and Ti particles is 1 ⁇ m, and the number of them exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • Comparative Example 9 The maximum length of Mg 2 Si particles is 2 ⁇ m, and the number of particles exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of TiB phase and Ti particles is 1 ⁇ m, and the number of them exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • Comparative Example 10 The maximum length of Mg 2 Si particles is 2 ⁇ m, and the number of particles exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.
  • the maximum length of Fe phase particles is 5 ⁇ m, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 ⁇ m shall not exceed 3.
  • the maximum length of TiB phase and Ti particles is 1 ⁇ m, and the number of them exceeding 2 ⁇ m is 0 under the 100 times field of view of the scanning electron microscope.

Abstract

The present invention provides an aluminum alloy material, a preparation method therefor, and an application thereof. According to the aluminum alloy material of the present invention, by means of alloy component design, the material can have good surface treatment performance while the yield strength is greater than 450 MPa. The aluminum alloy material of the present invention is small in stress deformation after being machined by a numerical control lathe. Taking a finished product of a middle frame of a bar phone having the length of 170 mm, the width of 80 mm, and the thickness of 7 mm as an example, the flatness can be controlled within 0.15. According to the aluminum alloy material of the present invention, the aluminum alloy is mechanically polished without trailing lines, and an oxidation film is transparent, such that high brightness can be achieved, and the anodic oxidation effect is good. The present invention further provides a preparation method for the aluminum alloy material and an application thereof in preparation of a 3C product housing.

Description

一种铝合金材料及其制备方法和应用A kind of aluminum alloy material and its preparation method and application 技术领域technical field
 本发明属于铝合金技术领域，具体涉及一种铝合金材料及其制备方法和应用。The invention belongs to the technical field of aluminum alloys, and in particular relates to an aluminum alloy material and its preparation method and application.
背景技术Background technique
 铝合金具有比重轻、比强度高、散热性能好、易加工、阳极氧化装饰效果优良，且可回收再利用等诸多特点而被广泛应用于各类商品的制造。作为3C结构件的常用材料，为了给手机内部结构设计者更多的发挥空间，同时由于手机的轻量化需求，要求进一步提升材料的屈服强度以期满足手机完整件的结构强度测试要求。同时，客户对手机的外观也非常关注，其表面处理多采用高亮阳极氧化处理，可以染上各种颜色，且氧化膜通透有光泽。氧化后成品需要进行盐雾及酸碱可靠性测试，不能有爆膜、开裂的情况。Aluminum alloy has many characteristics such as light specific gravity, high specific strength, good heat dissipation, easy processing, excellent anodic oxidation decoration effect, and recyclable reuse, so it is widely used in the manufacture of various commodities. As a commonly used material for 3C structural parts, in order to give more room for mobile phone internal structure designers, and due to the lightweight requirements of mobile phones, it is required to further increase the yield strength of materials in order to meet the structural strength test requirements of complete mobile phone parts. At the same time, customers are also very concerned about the appearance of mobile phones. The surface treatment is mostly high-brightness anodizing, which can be dyed in various colors, and the oxide film is transparent and shiny. After oxidation, the finished product needs to be tested for salt spray and acid-base reliability, and there must be no film bursting or cracking.
技术问题technical problem
在满足高亮阳极氧化外观基准的情况下，目前商用手机6系铝合金最高屈服强度约400MPa，普遍在370MPa左右，如果只采用简单的添加强化相含量、强化元素含量的方法试图进行强度提高，效果难以达成。主要因素有：(1)合金元素与氧化膜色泽通透性强相关：合金元素总量越高，氧化膜色泽通透性越差。如6系合金中的主要强化相Mg 2Si、游离Si、CuAl 2 ，在弥散析出时对强度起正面作用，而当超过一定量时，氧化膜色泽及通透性会严重恶化；(2)合金元素越高，生产的工艺窗口越窄(固溶温度和固相线温度区间越窄)，在平衡相图中，Mg 2Si最大固溶度1.85％，实际生产情况偏离平衡相图，Mg 2Si最大固溶度更低。比如在平衡相图中，Mg 2Si为1.6％时，其固溶线和固相线间温度区间约为20℃。Mg 2Si为1.7时，其固溶线和固相线间温度区间约为10℃，在生产过程中极其容易出现过烧组织或固溶不充分；(3)过烧产物硬度高，因其流动速度与铝有差异，会被拉长，在挤压材中形成条形缺陷。这些杂质相在氧化处理过程中溶解脱落，脱落位置留下凹坑，视觉上呈现黑色线条状缺陷，导致阳极效果不能满足客户需求。(4)固溶不充分的大颗粒物(大1μm))，与基体的电化学性能存在较大差异，阳极氧化表面处理时，作为阳极，会掉落形成孔洞或掺杂在氧化膜中，导致氧化膜视觉上的发麻效果，阳极效果不能满足客户需求。因此，在手机高亮阳极氧化要求的前提下，6系合金仅依赖合金含量的管控，其屈服强度最高400MPa。若需要更高的强度，而且能满足3C类产品多工序大加工量情况下的材料应力变形小、阳极氧化效果高亮通透，须通过合金成分及工艺条件创新予以完成。 In the case of meeting the appearance standard of high-brightness anodizing, the highest yield strength of 6-series aluminum alloys for commercial mobile phones is about 400MPa, generally around 370MPa. If only a simple method of adding strengthening phase content and strengthening element content is used to try to improve the strength, The effect is difficult to achieve. The main factors are: (1) Alloying elements are strongly related to the color and permeability of the oxide film: the higher the total amount of alloying elements, the worse the color and permeability of the oxide film. For example, the main strengthening phases Mg 2 Si, free Si, and CuAl 2 in 6-series alloys have a positive effect on the strength when dispersed and precipitated, and when the amount exceeds a certain amount, the color and permeability of the oxide film will be seriously deteriorated; (2) The higher the alloying elements, the narrower the production process window (the narrower the range of solid solution temperature and solidus temperature), in the equilibrium phase diagram, the maximum solid solubility of Mg 2 Si is 1.85%, and the actual production situation deviates from the equilibrium phase diagram, Mg 2 The maximum solid solubility of Si is lower. For example, in the equilibrium phase diagram, when Mg 2 Si is 1.6%, the temperature range between its solvus and solidus is about 20°C. When the Mg 2 Si is 1.7, the temperature range between the solvus line and the solidus line is about 10°C, and it is extremely easy to appear over-burned structure or insufficient solid solution during the production process; (3) The hardness of the over-burned product is high, because The flow rate is different from that of aluminum, and it will be elongated, forming strip defects in the extruded material. These impurity phases dissolve and fall off during the oxidation process, leaving pits at the falling position, visually presenting black line-like defects, resulting in anodic effects that cannot meet customer needs. (4) Large particles with insufficient solid solution (larger than 1 μm) have a large difference in electrochemical performance from the substrate. During anodic oxidation surface treatment, as an anode, they will fall to form holes or be doped in the oxide film, resulting in The visual numbness and anode effect of the oxide film cannot meet customer needs. Therefore, under the premise of high-brightness anodizing requirements for mobile phones, the 6-series alloy only relies on the control of alloy content, and its yield strength is up to 400MPa. If higher strength is required, and it can meet the needs of 3C products with small stress deformation and bright and transparent anodizing effect under the condition of multi-process and large-scale processing of 3C products, it must be completed through innovation of alloy composition and process conditions.
虽然7系合金可以轻松把强度做到500MPa，甚至600MPA以上，但由于7系合金成分高，阳极氧化容易出现爆膜开裂缺陷，因此未能使用在高亮阳极氧化的手机外壳上。因此，需要开发屈服强度达450MPa以上，能够适合高亮阳极氧化的铝合金材料，该类产品可广泛应用于要求高材料结构强度、材料残余应力小而且表面处理性能良好的3C产品中，能够适应5G以及未来6G的需求。Although the 7-series alloy can easily achieve a strength of 500MPa, or even more than 600MPA, due to the high composition of the 7-series alloy, anodic oxidation is prone to cracking defects, so it cannot be used on high-brightness anodized mobile phone casings. Therefore, it is necessary to develop aluminum alloy materials with a yield strength of more than 450MPa and suitable for high-brightness anodic oxidation. This type of product can be widely used in 3C products that require high material structural strength, low material residual stress and good surface treatment performance. 5G and future 6G requirements.
技术解决方案technical solution
本发明旨在至少解决现有技术中存在的上述技术问题之一。为此，本发明提供了一种铝合金材料，该铝合金材料屈服强度大于450MPa的同时表面处理性能良好。The present invention aims to solve at least one of the above-mentioned technical problems existing in the prior art. For this reason, the invention provides an aluminum alloy material, the yield strength of the aluminum alloy material is greater than 450MPa and the surface treatment performance is good.
本发明还提供了上述铝合金材料的制备方法。The present invention also provides a preparation method of the above-mentioned aluminum alloy material.
本发明还提供了上述铝合金材料的应用。The present invention also provides the application of the above-mentioned aluminum alloy material.
本发明的第一方面提供了一种铝合金材料，以质量百分比计，由以下组分制备得到。The first aspect of the present invention provides an aluminum alloy material prepared from the following components in mass percentage.
Si：0.30％～0.80％。Si: 0.30% to 0.80%.
Mg：0.35％～0.90％。Mg: 0.35% to 0.90%.
Cu：0.90％～2.20％。Cu: 0.90% to 2.20%.
Mn：0.05％～0.15％。Mn: 0.05% to 0.15%.
Ti：0.002％～0.015％。Ti: 0.002% to 0.015%.
B：≤0.0050％。B: ≤0.0050%.
余量为Al。The balance is Al.
所述铝合金材料中含有游离Si，所述游离Si的质量百分比为0.06～0.35％，所述游离Si的计算方法为：Si％-Mg％×0.578。The aluminum alloy material contains free Si, the mass percentage of the free Si is 0.06-0.35%, and the calculation method of the free Si is: Si%-Mg%×0.578.
本发明的铝合金材料中，Si以Mg 2 Si和游离Si的形式存在。 In the aluminum alloy material of the present invention, Si exists in the form of Mg 2 Si and free Si.
在合金中，Si和Mg形成Mg 2 Si，Mg:Si成分含量＝24.3×2/28.09，即当Si含量为1％时，形成Mg 2Si需要的Mg为1.73％，因此，游离Si的计算方法为：Si的总含量-Mg 2Si中的Si含量＝Si％-Mg％×0.578。 In the alloy, Si and Mg form Mg 2 Si, Mg: Si composition content = 24.3×2/28.09, that is, when the Si content is 1%, the Mg required to form Mg 2 Si is 1.73%, therefore, the calculation of free Si The method is: total content of Si-Si content in Mg 2 Si=Si%-Mg%×0.578.
本发明关于铝合金材料的技术方案中的一个技术方案，至少具有以下有益效果。One of the technical solutions of the present invention on aluminum alloy materials has at least the following beneficial effects.
本发明的铝合金材料，通过合金成分设计，使得材料能够在屈服强度大于450MPa的同时具有良好的表面处理以性能。The aluminum alloy material of the present invention, through the design of the alloy composition, enables the material to have good surface treatment and performance while the yield strength is greater than 450 MPa.
本发明的铝合金材料，数控车床加工后应力变形小。以长170mm×宽80mm×厚7mm的直板手机中框加工完成品为例，平面度可以控制在0.15以内。The aluminum alloy material of the present invention has small stress deformation after being processed by a numerically controlled lathe. Taking the finished product of the middle frame of a straight mobile phone with a length of 170mm x width 80mm x thickness 7mm as an example, the flatness can be controlled within 0.15.
本发明的铝合金材料，铝合金机械抛光无拖尾线条出现，氧化膜通透，可实现高亮阳极氧化效果优质。The aluminum alloy material of the present invention has no trailing lines when the aluminum alloy is mechanically polished, the oxide film is transparent, and the high-quality anodic oxidation effect of high brightness can be realized.
本发明的铝合金材料，合金成分设计中，Si和Mg元素是形成强化相的主要合金元素，通过形成的Mg 2Si控制材料强度，Mg 2Si在铝基体中最大固溶度为1.85％，当Mg 2 Si总量越靠近1.85％时，其固溶温度和固相线温度非常接近，挤压工业生产中很难控制。温度过低，固溶不充分，Mg 2 Si不能很好发挥作用。温度过高，超过材料的固相线温度，则挤压出现开裂。本发明中，将Si控制在0.3～0.8％，Mg控制在0.35～0.90％，则Mg 2Si总量可以控制小于1.494％，有效保证了工艺窗口的量产性。材料中设置一定的游离Si，游离Si总量控制在0.09～0.35％，可以在时效处理过程中作为强化沉淀相的形核核心，使得强化沉淀相细小弥散均匀分布。若游离Si总量超过0.35％，会严重降低挤压型材的延伸率，导致后续冷加工产生开裂以及最终成品延伸率低。 In the aluminum alloy material of the present invention, in the design of the alloy composition, Si and Mg elements are the main alloy elements forming the strengthening phase, and the strength of the material is controlled by the formed Mg 2 Si, and the maximum solid solubility of Mg 2 Si in the aluminum matrix is 1.85%. When the total amount of Mg 2 Si is closer to 1.85%, its solid solution temperature and solidus temperature are very close, which is difficult to control in extrusion industrial production. If the temperature is too low, the solid solution is insufficient, and Mg 2 Si cannot function well. If the temperature is too high and exceeds the solidus temperature of the material, cracking will occur during extrusion. In the present invention, Si is controlled at 0.3-0.8%, and Mg is controlled at 0.35-0.90%, so the total amount of Mg 2 Si can be controlled to be less than 1.494%, which effectively ensures the mass production of the process window. A certain amount of free Si is set in the material, and the total amount of free Si is controlled at 0.09-0.35%, which can be used as the nucleation core of the strengthening precipitation phase during the aging treatment, so that the strengthening precipitation phase is finely dispersed and evenly distributed. If the total amount of free Si exceeds 0.35%, the elongation of the extruded profile will be seriously reduced, resulting in cracking in subsequent cold working and low elongation of the final product.
本发明的铝合金材料，合金成分设计中，将Cu的含量控制在0.90～2.2％，添加适量Cu，形成CuAl 2相，以显著提高材料的时效硬化性能。 In the aluminum alloy material of the present invention, in the alloy composition design, the Cu content is controlled at 0.90-2.2%, and an appropriate amount of Cu is added to form a CuAl 2 phase, so as to significantly improve the age hardening performance of the material.
Fe在铝合金中固溶度低，而Fe是原材料的杂质元素，不可避免存在。而大颗粒状长条状的的Fe相影响阳极氧化效果。本发明中将适量添加Mn，能有效促进针状含Fe相转化为球状Fe相。本文中Fe控制≤0.09％、Mn含量控制0.05％～0.15％。并通过后续高温长时间的均匀化处理(温度550℃～575℃，保温12h～24h)，提高Fe相球化率。The solid solubility of Fe in aluminum alloy is low, and Fe is an impurity element of the raw material, which inevitably exists. The large granular and long Fe phase affects the anodic oxidation effect. In the present invention, an appropriate amount of Mn is added to effectively promote the transformation of the needle-shaped Fe-containing phase into the spherical Fe-phase. In this paper, the Fe control is ≤0.09%, and the Mn content is controlled at 0.05%-0.15%. And through the follow-up high-temperature and long-term homogenization treatment (temperature 550°C-575°C, heat preservation 12h-24h), the spheroidization rate of Fe phase is improved.
本发明的铝合金材料，合金成分设计中，B作为原材料铝锭中的杂质元素，不可避免存在。而为了细化晶粒，合金铸造过程中加入适量Ti-B细化剂。当B含量超过一定范围时，极易形成TiB颗粒团聚，作为硬质相，在后续铝合金型材进行机械抛光时容易嵌入较软的铝合金基体从而导致线条出现。本文中Ti控制0.0020～0.0150％、B控制≤0.0050％。In the aluminum alloy material of the present invention, in the alloy composition design, B, as an impurity element in the raw material aluminum ingot, inevitably exists. In order to refine the grains, an appropriate amount of Ti-B refiner is added during the alloy casting process. When the B content exceeds a certain range, it is very easy to form TiB particle agglomeration, as a hard phase, it is easy to embed into the softer aluminum alloy matrix during subsequent mechanical polishing of the aluminum alloy profile, resulting in the appearance of lines. In this paper, Ti is controlled at 0.0020-0.0150%, and B is controlled at ≤0.0050%.
根据本发明的一些实施方式，所述铝合金材料中，硼元素含量≤0.0050％，铁元素含量≤0.09％，单种杂质元素含量≤0.03％，杂质元素含量合计≤0.15％。According to some embodiments of the present invention, in the aluminum alloy material, the content of boron element is ≤0.0050%, the content of iron element is ≤0.09%, the content of a single impurity element is ≤0.03%, and the total content of impurity elements is ≤0.15%.
根据本发明的一些实施方式，本发明的铝合金材料中，Mg 2Si颗粒最大程度呈纳米级的析出。在扫描电镜100倍视场下，不出现长度超5μm白的Mg 2Si颗粒；且长度为2～5μm的Mg 2Si颗粒不超过5颗。 According to some embodiments of the present invention, in the aluminum alloy material of the present invention, Mg 2 Si particles are precipitated at the nanoscale to the greatest extent. Under the 100 times field of view of the scanning electron microscope, no white Mg 2 Si particles with a length exceeding 5 μm appear; and no more than 5 Mg 2 Si particles with a length of 2-5 μm.
Mg 2Si属于强化相颗粒，组成元素为Mg和Si。 Mg 2 Si belongs to strengthening phase particles, and its constituent elements are Mg and Si.
根据本发明的一些实施方式，本发明的铝合金材料中，扫描电镜100倍视场下，超过2μm的数量不超过5个。According to some embodiments of the present invention, in the aluminum alloy material of the present invention, under a scanning electron microscope with a field of view of 100 times, the number exceeding 2 μm is no more than 5.
根据本发明的一些实施方式，本发明的铝合金材料中，扫描电镜100倍视场下，Fe相颗粒的长度≤7μm，超过3μm数量不超过10个。According to some embodiments of the present invention, in the aluminum alloy material of the present invention, under the 100 times field of view of the scanning electron microscope, the length of the Fe phase particles is ≤7 μm, and the number of Fe phase particles exceeding 3 μm is no more than 10.
Fe相颗粒属于不可溶的杂质颗粒。Fe phase particles belong to insoluble impurity particles.
根据本发明的一些实施方式，本发明的铝合金材料中，扫描电镜100倍视场下，TiB相颗粒的长度≤3μm，扫描电镜100视场下，超过2μm数量不超过2个。According to some embodiments of the present invention, in the aluminum alloy material of the present invention, under the 100x field of view of the scanning electron microscope, the length of the TiB phase particles is ≤ 3 μm, and the number of particles exceeding 2 μm under the 100x field of view of the scanning electron microscope is no more than 2.
TiB相颗粒主要成分为TiB。The main component of TiB phase particles is TiB.
根据本发明的一些实施方式，所述铝合金材料的屈服强度≥450MPa。According to some embodiments of the present invention, the yield strength of the aluminum alloy material is ≥450 MPa.
本发明的第二方面提供了制备上述的铝合金材料的方法，包括以下步骤。A second aspect of the present invention provides a method for preparing the above-mentioned aluminum alloy material, including the following steps.
S1：按照配比进行备料，将铝锭熔化后，加入镁锭和中间合金，得到铝合金液I。S1: prepare materials according to the ratio, melt the aluminum ingots, add magnesium ingots and intermediate alloys, and obtain aluminum alloy liquid I.
S2：加入精炼剂对所述铝合金液I进行精炼，得到铝合金液II。S2: Adding a refining agent to refine the aluminum alloy solution I to obtain the aluminum alloy solution II.
S3：加入晶粒细化剂对所述铝合金液II进行在线晶粒细化处理，得到铝合金液III。S3: Adding a grain refiner to perform on-line grain refinement treatment on the aluminum alloy liquid II to obtain the aluminum alloy liquid III.
S4：将所述铝合金液III过滤后，进行铸造和均匀化处理。S4: After filtering the aluminum alloy liquid III, casting and homogenization treatment are performed.
根据本发明的一些实施方式，步骤S1中，铝锭熔化的温度为740℃～780℃。According to some embodiments of the present invention, in step S1, the melting temperature of the aluminum ingot is 740°C-780°C.
根据本发明的一些实施方式，步骤S2中，加入精炼剂进行精炼后，再通入氩气对铝合金液进行精炼，扒渣、静置，得到铝合金液II。According to some embodiments of the present invention, in step S2, after adding a refining agent for refining, argon gas is introduced to refine the aluminum alloy liquid, the slag is removed, and the aluminum alloy liquid II is obtained.
根据本发明的一些实施方式，步骤S3中，在线晶粒细化，通过添加常规的晶粒细化剂即可实现。According to some embodiments of the present invention, in step S3, the online grain refinement can be realized by adding a conventional grain refiner.
根据本发明的一些实施方式，步骤S4中，将所述铝合金液III过滤后，经过流槽双箱体除气，80ppi陶瓷过滤板+RC级别以上的管式过滤器，得到铝合金液Ⅳ，再对铝合金液Ⅳ进行铸造和均匀化处理。According to some embodiments of the present invention, in step S4, after the aluminum alloy liquid III is filtered, the aluminum alloy liquid IV is obtained by degassing through the double box of the launder, 80ppi ceramic filter plate + a tubular filter above RC level , and then cast and homogenize the aluminum alloy liquid IV.
根据本发明的一些实施方式，铸造的温度为700℃～730℃。According to some embodiments of the present invention, the casting temperature is 700°C to 730°C.
根据本发明的一些实施方式，所述均匀化处理的方法为：先将材料升温至480℃～500℃，保温2h～6h，继续升温至550℃～575℃，保温12h～24h。According to some embodiments of the present invention, the homogenization treatment method is as follows: first heat the material to 480°C-500°C, keep it warm for 2h-6h, continue to raise the temperature to 550°C-575°C, and keep it warm for 12h-24h.
根据本发明的一些实施方式，所述方法还包括在步骤S4之后，对材料进行成型处理。According to some embodiments of the present invention, the method further includes, after step S4, performing a molding treatment on the material.
根据本发明的一些实施方式，成型处理的方法为。According to some embodiments of the present invention, the method of forming treatment is.
(1)将铝合金铸棒加热，加热过程中，530℃～570℃区间保温1h～4h。(1) Heat the aluminum alloy cast rod, and keep warm at 530°C to 570°C for 1h to 4h during the heating process.
(2)铸棒上机温度控制在520℃～560℃，挤压比大于20，铸棒进行挤压成形。(2) The temperature of the cast rod on the machine is controlled at 520°C to 560°C, the extrusion ratio is greater than 20, and the cast rod is extruded.
(3)挤压出口温度控制在530℃～570℃，并在60s内穿水淬火冷却，得到挤压型材。(3) The temperature at the extrusion outlet is controlled at 530°C to 570°C, and quenched and cooled by passing through water within 60s to obtain an extruded profile.
(4)型材的预热处理：将挤压材进行预热处理加热至160℃～190℃保温2h～12h。(4) Preheat treatment of profiles: Preheat the extruded material and heat it to 160°C-190°C for 2h-12h.
(5)型材的冷变形加工，冷变形加工面积变形量控制在4％～15％，冷加工面积变形量的计算方法为：(冷加工前断面面积-冷加工后断面面积)/冷加工前断面面面积。(5) For cold deformation processing of profiles, the deformation of the cold deformation processing area is controlled at 4% to 15%. The calculation method of the deformation of the cold processing area is: (cross-sectional area before cold processing-cross-sectional area after cold processing)/cross-sectional area before cold processing.
(6)人工时效处理：将冷加工后铝合金型材加热至170℃～200℃保温2h～12h，且人工时效温度比预热处理温度高10℃以上。(6) Artificial aging treatment: heat the aluminum alloy profile after cold working to 170°C-200°C for 2h-12h, and the artificial aging temperature is 10°C higher than the preheating temperature.
铝合金可以通过冷作硬化提高产品强度，一般情况下，变形量越大，材料内部储能越高，材料耐腐蚀性下降，阳极发麻发哑，变形量太小，强度提升效果有限。本发明中，施加一定的冷加工量，提升强度并保证阳极氧化效果。Aluminum alloy can improve product strength through cold work hardening. Generally speaking, the greater the deformation, the higher the internal energy storage of the material, the lower the corrosion resistance of the material, the anode is numb and dull, the deformation is too small, and the strength improvement effect is limited. In the present invention, a certain amount of cold working is applied to improve the strength and ensure the anodic oxidation effect.
制备方法中的冷变形加工包括而且不局限于拉拔、轧制、锻压等常温下进行变形加工的模式。The cold deformation processing in the preparation method includes but is not limited to drawing, rolling, forging and other modes of deformation processing at normal temperature.
制备方法中的冷变形加工包括而且不局限于拉拔、轧制、锻压等常温下进行变形加工的模式。The cold deformation processing in the preparation method includes but is not limited to drawing, rolling, forging and other modes of deformation processing at normal temperature.
铝合金在挤压加工以及冷作硬化过程，不可避免产生一定的残余应力。本发明中，通过二级热处理制度，而且第二级人工时效温度比第一级高10℃及以上，使应力去除更为彻底，满足3C类产品的加工需求。In the process of extrusion processing and cold work hardening of aluminum alloy, certain residual stress will inevitably be generated. In the present invention, through the two-stage heat treatment system, and the artificial aging temperature of the second stage is 10°C or more higher than that of the first stage, the stress removal is more thorough, and the processing requirements of 3C products are met.
附图说明Description of drawings
图1是实施例1制备的铝合金材料微观形貌的扫描电镜检测结果。Fig. 1 is the scanning electron microscope detection result of the microscopic morphology of the aluminum alloy material prepared in Example 1.
图2是对比例1制备的铝合金材料微观形貌的扫描电镜检测结果。Fig. 2 is the scanning electron microscope detection result of the microscopic morphology of the aluminum alloy material prepared in Comparative Example 1.
本发明的最佳实施方式BEST MODE FOR CARRYING OUT THE INVENTION
以下是本发明的具体实施例，并结合实施例对本发明的技术方案作进一步的描述，但本发明并不限于这些实施例。The following are specific examples of the present invention, and further describe the technical solutions of the present invention in conjunction with the examples, but the present invention is not limited to these examples.
实施例1。Example 1.
本实施例制备了一种铝合金材料，由以下组分制备得到。In this embodiment, an aluminum alloy material is prepared from the following components.
Si：0.65％，Mg：0.7％，Cu：1.8％，Mn：0.12％，Ti：0.012％，B：0.004％，Fe：0.08％，余量为Al。Si: 0.65%, Mg: 0.7%, Cu: 1.8%, Mn: 0.12%, Ti: 0.012%, B: 0.004%, Fe: 0.08%, and the balance is Al.
铝合金材料中，单种杂质元素含量≤0.03％，杂质元素含量合计≤0.15％。In the aluminum alloy material, the content of a single impurity element is ≤0.03%, and the total content of impurity elements is ≤0.15%.
具体制备方法为。The specific preparation method is as follows.
(1)合金铸棒的熔炼、铸造及均质处理。(1) Melting, casting and homogenization of alloy cast rods.
按照上述质量百分比进行备料，其中，铝和镁采用铝锭和镁锭，铝锭中的不可避免杂质Fe：0.08％，B：0.0050％。铝钛硼细化剂中，TiB 2单个质点直径小于3μm的在95％，分布大致均匀弥散。 Prepare materials according to the above mass percentages, wherein aluminum and magnesium are made of aluminum ingots and magnesium ingots, and the unavoidable impurities in the aluminum ingots are Fe: 0.08%, and B: 0.0050%. In the Al-Ti-B refiner, 95% of TiB 2 single particle diameters are less than 3 μm, and the distribution is roughly uniform and dispersed.
将铝锭加热到760℃进行熔化，再加入镁锭和中间合金，搅拌熔化，得到铝合金液I。Heat the aluminum ingot to 760°C for melting, then add magnesium ingot and intermediate alloy, stir and melt to obtain aluminum alloy solution I.
向铝合金液中加入精炼剂，再通入氩气对铝合金液进行精炼，扒渣、静置，得到铝合金液II；精炼剂通过市场购买得到，本发明中，使用西盛公司的W-713-3精炼剂或派瑞克的PROMAG  Ri精炼剂均可，属于钠盐、钾盐精炼剂。Add a refining agent to the aluminum alloy liquid, and then introduce argon gas to refine the aluminum alloy liquid, remove the slag, and leave it to stand to obtain the aluminum alloy liquid II; the refining agent is purchased from the market. In the present invention, W -713-3 Refining Agent or Pyrique's PROMAG Ri refining agent can be used, which belongs to sodium salt and potassium salt refining agent.
将铝合金液II放入流槽，再加入晶粒细化剂进行在线晶粒细化处理，得到铝合金液III。Putting the aluminum alloy liquid II into the launder, and then adding a grain refiner to carry out on-line grain refinement treatment, to obtain the aluminum alloy liquid III.
将铝合金液III经过流槽双箱体除气，80ppi陶瓷过滤板+RC级别以上的管式过滤器，得到铝合金液Ⅳ。The aluminum alloy liquid III is degassed through the double box of the launder, and the 80ppi ceramic filter plate + the tubular filter above the RC level is obtained to obtain the aluminum alloy liquid IV.
将铝合金液Ⅳ于710℃条件下进行铸造，得到铝合金铸棒。The aluminum alloy liquid IV was cast at 710° C. to obtain aluminum alloy cast rods.
将铝合金铸棒进行均匀化处理，具体过程为：升温至480℃保温6小时后继续升温至570℃保温16小时，得到铝合金铸棒A。The aluminum alloy casting rod was homogenized, and the specific process was: heating up to 480° C. for 6 hours and then continuing to heat up to 570° C. for 16 hours to obtain the aluminum alloy casting rod A.
(2)型材挤压。(2) Profile extrusion.
将铝合金铸棒A加热，其中530～570℃区间保温1小时。The aluminum alloy cast rod A is heated, and the temperature is kept at 530-570° C. for 1 hour.
铸棒上机温度控制在540～550℃，挤压比40，铸棒进行挤压成形。The temperature of the cast rod is controlled at 540-550°C, the extrusion ratio is 40, and the cast rod is extruded.
挤压出口温度控制在550～570℃，并在60秒内穿水淬火冷却，得到挤压型材。The extrusion outlet temperature is controlled at 550-570°C, and quenched and cooled through water within 60 seconds to obtain an extruded profile.
型材挤压过程中，铸棒加温为一个逐步升温的过程，每一个铸棒挤压的材料长度约50m，因为摩擦升温的原因，实际上头部和尾部温度有一个变化的过程，因此上述温度设置为温度区间。During the profile extrusion process, the heating of the cast rod is a process of gradually increasing the temperature. The length of the material extruded by each cast rod is about 50m. Because of the frictional heating, the temperature of the head and tail actually has a process of change, so the above The temperature is set as a temperature interval.
(3)型材的预热处理：将挤压材进行预热处理加热至190℃保温2h。(3) Preheat treatment of profiles: Preheat the extruded material and heat it to 190°C for 2 hours.
(4)型材的冷变形加工，冷变形加工面积变形量控制在13％～15％。(4) For cold deformation processing of profiles, the deformation of the cold deformation processing area is controlled at 13% to 15%.
(5)人工时效处理：将冷加工后铝合金型材加热至200℃保温2h。(5) Artificial aging treatment: heat the cold-worked aluminum alloy profile to 200°C for 2 hours.
实施例2。Example 2.
本实施例制备了一种铝合金材料，与实施例1的区别是，其中镁的含量为0.86％。In this example, an aluminum alloy material is prepared, the difference from Example 1 is that the magnesium content is 0.86%.
实施例3。Example 3.
本实施例制备了一种铝合金材料，与实施例1的区别是，其中硅的含量为0.74％。In this example, an aluminum alloy material is prepared, the difference from Example 1 is that the silicon content is 0.74%.
实施例4。Example 4.
本实施例制备了一种铝合金材料，与实施例1的区别是，其中铜的含量为0.9％。In this example, an aluminum alloy material is prepared, the difference from Example 1 is that the content of copper is 0.9%.
实施例5。Example 5.
本实施例制备了一种铝合金材料，与实施例1的区别是，其中锰的含量为0.05％。In this embodiment, an aluminum alloy material is prepared, which differs from the embodiment 1 in that the content of manganese is 0.05%.
实施例6。Example 6.
本实施例制备了一种铝合金材料，与实施例1的区别是，其中硼的含量为0.001％。In this embodiment, an aluminum alloy material is prepared, which differs from that in Embodiment 1 in that the content of boron is 0.001%.
实施例7。Example 7.
本实施例制备了一种铝合金材料，由以下组分制备得到。In this embodiment, an aluminum alloy material is prepared from the following components.
Si：0.65％，Mg：0.7％，Cu：1.8％，Mn：0.12％，Ti：0.012％，B：0.004％，Fe：0.08％，余量为Al。Si: 0.65%, Mg: 0.7%, Cu: 1.8%, Mn: 0.12%, Ti: 0.012%, B: 0.004%, Fe: 0.08%, and the balance is Al.
铝合金材料中，单种杂质元素含量≤0.03％，杂质元素含量合计≤0.15％。In the aluminum alloy material, the content of a single impurity element is ≤0.03%, and the total content of impurity elements is ≤0.15%.
具体制备方法为。The specific preparation method is as follows.
(1)合金铸棒的熔炼、铸造及均质处理。(1) Melting, casting and homogenization of alloy cast rods.
按照上述质量百分比进行备料，其中，铝和镁采用铝锭和镁锭，铝锭中的不可避免杂质Fe：0.08％，B：0.0050％。铝钛硼细化剂中，TiB 2 单个质点直径小于3μm的在95％，分布大致均匀弥散。 Prepare materials according to the above mass percentages, wherein aluminum and magnesium are made of aluminum ingots and magnesium ingots, and the unavoidable impurities in the aluminum ingots are Fe: 0.08%, and B: 0.0050%. In the Al-Ti-B refiner, 95% of TiB 2 single particle diameters are less than 3 μm, and the distribution is roughly uniform and dispersed.
将铝锭加热到760℃进行熔化，再加入镁锭和中间合金，搅拌熔化，得到铝合金液I。Heat the aluminum ingot to 760°C for melting, then add magnesium ingot and intermediate alloy, stir and melt to obtain aluminum alloy solution I.
向铝合金液中加入精炼剂，再通入氩气对铝合金液进行精炼，扒渣、静置，得到铝合金液II。Adding a refining agent to the aluminum alloy liquid, and then introducing argon gas to refine the aluminum alloy liquid, removing slag, and standing still to obtain aluminum alloy liquid II.
将铝合金液II放入流槽，再加入晶粒细化剂进行在线晶粒细化处理，得到铝合金液III。Putting the aluminum alloy liquid II into a launder, and then adding a grain refiner to carry out on-line grain refinement treatment, to obtain the aluminum alloy liquid III.
将铝合金液III经过流槽双箱体除气，80ppi陶瓷过滤板+RC级别以上的管式过滤器，得到铝合金液Ⅳ。The aluminum alloy liquid III is degassed through the double box of the launder, and the 80ppi ceramic filter plate + the tubular filter above the RC level is obtained to obtain the aluminum alloy liquid IV.
将铝合金液Ⅳ于710℃条件下进行铸造，得到铝合金铸棒。The aluminum alloy liquid IV was cast at 710° C. to obtain aluminum alloy cast rods.
将铝合金铸棒进行均匀化处理，具体过程为：升温至480℃保温6小时后继续升温至570℃保温16小时，得到铝合金铸棒A。The aluminum alloy casting rod was homogenized, and the specific process was: heating up to 480° C. for 6 hours and then continuing to heat up to 570° C. for 16 hours to obtain the aluminum alloy casting rod A.
(2)型材挤压。(2) Profile extrusion.
将铝合金铸棒A加热，其中530～570℃区间保温1小时。The aluminum alloy cast rod A is heated, and the temperature is kept at 530-570° C. for 1 hour.
铸棒上机温度控制在520～530℃，挤压比40，铸棒进行挤压成形。The temperature of the cast rod on the machine is controlled at 520-530°C, the extrusion ratio is 40, and the cast rod is extruded.
挤压出口温度控制在540～560℃，并在60秒内穿水淬火冷却，得到挤压型材。The extrusion outlet temperature is controlled at 540-560°C, and quenched and cooled through water within 60 seconds to obtain an extruded profile.
(3)型材的预热处理：将挤压材进行预热处理加热至190℃保温2h。(3) Preheat treatment of profiles: Preheat the extruded material and heat it to 190°C for 2 hours.
(4)型材的冷变形加工，冷变形加工面积变形量控制在13％～15％。(4) For cold deformation processing of profiles, the deformation of the cold deformation processing area is controlled at 13% to 15%.
(5)人工时效处理：将冷加工后铝合金型材加热至200℃保温2h。(5) Artificial aging treatment: heat the cold-worked aluminum alloy profile to 200°C for 2 hours.
实施例8。Example 8.
本实施例制备了一种铝合金材料，与实施例1的区别在于，制备过程中，型材的预热处理时，将挤压材进行预热处理加热至160℃保温2h。This example prepares an aluminum alloy material. The difference from Example 1 is that during the preparation process, during the preheating treatment of the profile, the extruded material is preheated and heated to 160° C. for 2 hours.
实施例9。Example 9.
本实施例制备了一种铝合金材料，与实施例1的区别在于，制备过程中，型材的冷变形加工，冷变形加工面积变形量控制在4％～5.5％。This example prepares an aluminum alloy material, and the difference from Example 1 lies in that during the preparation process, the profile is cold deformed, and the deformation of the cold deformed area is controlled at 4% to 5.5%.
实施例10。Example 10.
本实施例制备了一种铝合金材料，与实施例1的区别是，铝合金材料由以下组分制备得到。In this example, an aluminum alloy material is prepared. The difference from Example 1 is that the aluminum alloy material is prepared from the following components.
Si：0.3％，Mg：0.35％，Cu：2.2％，Mn：0.12％，Ti：0.012％，B：0.004％，Fe：0.08％，余量为Al。Si: 0.3%, Mg: 0.35%, Cu: 2.2%, Mn: 0.12%, Ti: 0.012%, B: 0.004%, Fe: 0.08%, and the balance is Al.
铝合金材料中，单种杂质元素含量≤0.03％，杂质元素含量合计≤0.15％。In the aluminum alloy material, the content of a single impurity element is ≤0.03%, and the total content of impurity elements is ≤0.15%.
对比例1。Comparative example 1.
本对比例制备了一种铝合金材料，与实施例1的区别是，其中硅的含量为0.25％。游离Si的含量为0.25-0.7×0.578＝-0.1546，该数值为负数，说明此时铝合金材料中不含游离Si。In this comparative example, an aluminum alloy material is prepared, the difference from Example 1 is that the silicon content is 0.25%. The content of free Si is 0.25-0.7×0.578=-0.1546, which is a negative number, indicating that there is no free Si in the aluminum alloy material at this time.
对比例2。Comparative example 2.
本对比例制备了一种铝合金材料，与实施例1的区别是，其中Mg的含量为0.30％。游离Si的含量为0.65-0.3×0.578＝0.4766，本对比例中游离Si的含量超出了本发明限定的0.09～0.35％的范围，型材在冷变形加工时，材料边部开裂。In this comparative example, an aluminum alloy material is prepared, the difference from Example 1 is that the content of Mg is 0.30%. The content of free Si is 0.65-0.3×0.578=0.4766. In this comparative example, the content of free Si exceeds the range of 0.09-0.35% limited by the present invention. When the profile is processed by cold deformation, the edge of the material cracks.
对比例3。Comparative example 3.
本对比例制备了一种铝合金材料，与实施例1的区别是，其中铜的含量为0.8％。In this comparative example, an aluminum alloy material is prepared, the difference from Example 1 is that the content of copper is 0.8%.
对比例4。Comparative example 4.
本对比例制备了一种铝合金材料，与实施例1的区别是，其中硼的含量为0.0.006％。In this comparative example, an aluminum alloy material is prepared, the difference from Example 1 is that the content of boron is 0.0.006%.
对比例5。Comparative example 5.
本对比例制备了一种铝合金材料，与实施例1的区别之一是，其中钛的含量为0.02％。区别之二是，铝钛硼细化剂中，TiB 2 单个质点直径小于3μm的在90％，有部分团聚情况。 In this comparative example, an aluminum alloy material is prepared, one of the differences from Example 1 is that the content of titanium is 0.02%. The second difference is that among the Al-Ti-B refiners, 90% of TiB 2 single particle diameters are less than 3 μm, and some of them are agglomerated.
对比例6。Comparative example 6.
本对比例制备了一种铝合金材料，与实施例1的区别是，将铝合金铸棒进行均匀化处理过程中，直接升温至570℃保温16小时。In this comparative example, an aluminum alloy material is prepared. The difference from Example 1 is that the aluminum alloy cast rod is directly heated to 570° C. for 16 hours during homogenization treatment.
对比例7。Comparative example 7.
本对比例制备了一种铝合金材料，与实施例1的区别是，型材挤压过程中，铸棒上机温度控制在500～520℃，挤压比40，铸棒进行挤压成形。In this comparative example, an aluminum alloy material is prepared. The difference from Example 1 is that during the profile extrusion process, the temperature of the casting rod on the machine is controlled at 500-520° C., and the extrusion ratio is 40, and the casting rod is extruded.
挤压出口温度控制在520～540℃，并在60秒内穿水淬火冷却，得到挤压型材。The extrusion outlet temperature is controlled at 520-540°C, and quenched and cooled through water within 60 seconds to obtain an extruded profile.
对比例8。Comparative example 8.
本对比例制备了一种铝合金材料，与实施例1的区别是，型材冷变形加工过程中，冷变形加工面积变形量控制在16％～17％。In this comparative example, an aluminum alloy material is prepared, and the difference from Example 1 is that during the cold deformation process of the profile, the deformation amount of the cold deformation processing area is controlled at 16%-17%.
对比例9。Comparative example 9.
本对比例制备了一种铝合金材料，与实施例1的区别是，型材人工时效处理过程中，将冷加工后铝合金型材加热至180℃保温2h。In this comparative example, an aluminum alloy material is prepared. The difference from Example 1 is that during the artificial aging treatment of the profile, the cold-processed aluminum alloy profile is heated to 180° C. for 2 hours.
对比例10。Comparative example 10.
本对比例制备了一种铝合金材料，与实施例1的区别是，型材挤压过程中，未进行预热处理。In this comparative example, an aluminum alloy material is prepared, and the difference from Example 1 is that no preheating treatment is performed during the profile extrusion process.
性能测试1。performance test 1.
测试了实施例和对比例制备的铝合金材料的屈服强度。The yield strength of the aluminum alloy materials prepared in the examples and comparative examples was tested.
对实施例和对比例制备的铝合金材料进行了抛光，观察是否有拖尾线条缺陷出现。The aluminum alloy materials prepared in the examples and the comparative examples were polished, and it was observed whether there was a trailing line defect.
用数控机床对实施例和对比例制备的铝合金材料进行机加工，具体将材料加工成长170mm×宽80mm×厚7mm的直板手机中框，测试平面度。The aluminum alloy materials prepared in the examples and the comparative examples were machined with a numerical control machine tool. Specifically, the materials were processed into a straight mobile phone middle frame with a length of 170mm x width 80mm x thickness 7mm, and the flatness was tested.
相同条件下，对直板手机中框进行了阳极氧化表面处理，观察氧化膜的外观性能。Under the same conditions, the anodic oxidation surface treatment was carried out on the middle frame of the straight mobile phone, and the appearance and performance of the oxide film were observed.
结果如表1所示。The results are shown in Table 1.
表1。Table 1.
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其中，对比例2制备的铝合金材料在冷加工过程边部开裂。Among them, the aluminum alloy material prepared in Comparative Example 2 cracked at the edge during the cold working process.
性能测试2。performance test 2.
用扫描电镜观察了实施例和对比例制备的铝合金材料的微观组织形貌。具体情况为。The microstructure and morphology of the aluminum alloy materials prepared in the examples and comparative examples were observed with a scanning electron microscope. The specific situation is.
实施例1：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。实施例1制备的颗粒物形貌如图1所示。 Example 1: The maximum length of Mg 2 Si particles is 2 μm, and under the 100 times field of view of the scanning electron microscope, there are 0 particles exceeding 2 μm. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope. The morphology of the particles prepared in Example 1 is shown in Figure 1.
实施例2：Mg 2Si颗粒的最大长度3μm，其中扫描电镜100倍视场下，超过2μm数量不超过2个。Fe相颗粒最大长度4μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Example 2: The maximum length of Mg 2 Si particles is 3 μm, and under the 100 times field of view of the scanning electron microscope, no more than 2 particles exceed 2 μm. The maximum length of Fe phase particles is 4 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
实施例3：Mg 2Si颗粒的最大长度1.8μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Example 3: The maximum length of Mg 2 Si particles is 1.8 μm, and the number of particles exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
实施例4：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度4μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Example 4: The maximum length of Mg 2 Si particles is 2 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 2 μm is 0. The maximum length of Fe phase particles is 4 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
实施例5：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度6μm，其中扫描电镜100倍视场下，超过3μm数量不超过7个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Example 5: The maximum length of Mg 2 Si particles is 2 μm, and the number of particles exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope. The maximum length of Fe phase particles is 6 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm does not exceed 7. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
实施例6：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。扫描电镜100倍视场下，未能找到TiB相及Ti颗粒、B颗粒。 Example 6: The maximum length of Mg 2 Si particles is 2 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 2 μm is 0. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. Under the 100X field of view of the scanning electron microscope, the TiB phase, Ti particles and B particles could not be found.
实施例7：Mg 2Si颗粒的最大长度3μm，其中扫描电镜100倍视场下，超过2μm数量最多3个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Example 7: The maximum length of Mg 2 Si particles is 3 μm, and under the 100 times field of view of the scanning electron microscope, the maximum number of particles exceeding 2 μm is 3. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
实施例8：MgSi颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。Example 8: The maximum length of MgSi particles is 2 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 2 μm is 0. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
实施例9：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Example 9: The maximum length of Mg 2 Si particles is 2 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 2 μm is 0. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
实施例10：扫描电镜100倍视场下，未能观察到Mg 2Si颗粒。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Example 10: Mg 2 Si particles cannot be observed under a scanning electron microscope with a field of view of 100 times. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
对比例1：扫描电镜100倍视场下，未能观测到Mg 2Si颗粒。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。对比例1制备的颗粒物形貌如图2所示。 Comparative Example 1: No Mg 2 Si particles could be observed under the 100× field of view of the scanning electron microscope. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope. The morphology of the particles prepared in Comparative Example 1 is shown in FIG. 2 .
对比例2：扫描电镜100倍视场下，未能观测到Mg 2Si颗粒。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Comparative Example 2: No Mg 2 Si particles could be observed under the 100× field of view of the scanning electron microscope. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
对比例3：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度不超过1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Comparative example 3: the maximum length of Mg 2 Si particles is 2 μm, and under the 100 times field of view of the scanning electron microscope, there are 0 particles exceeding 2 μm. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of the TiB phase and Ti particles does not exceed 1 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
对比例4：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度4μm，其中扫描电镜100倍视场下，超过2μm数量6个。 Comparative example 4: the maximum length of Mg 2 Si particles is 2 μm, and the number of particles exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of TiB phase and Ti particles is 4 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
对比例5：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度5μm，其中扫描电镜100倍视场下，超过2μm数量6个。 Comparative example 5: the maximum length of Mg 2 Si particles is 2 μm, and the number of particles exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of TiB phase and Ti particles is 5 μm, and the number of them exceeds 2 μm under the 100 times field of view of the scanning electron microscope.
对比例6：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Comparative example 6: the maximum length of Mg 2 Si particles is 2 μm, and under the 100 times field of view of the scanning electron microscope, there are 0 particles exceeding 2 μm. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of TiB phase and Ti particles is 1 μm, and the number of them exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope.
对比例7：Mg 2Si颗粒的最大长度7μm，其中扫描电镜100倍视场下，超过2μm数量20个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Comparative example 7: the maximum length of Mg 2 Si particles is 7 μm, and under the 100 times field of view of the scanning electron microscope, there are 20 particles exceeding 2 μm. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of TiB phase and Ti particles is 1 μm, and the number of them exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope.
对比例8：MgSi颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度1μm，其中扫描电镜100倍视场下，超过2μm数量0个。Comparative Example 8: The maximum length of MgSi particles is 2 μm, and the number of particles exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of TiB phase and Ti particles is 1 μm, and the number of them exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope.
对比例9：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Comparative Example 9: The maximum length of Mg 2 Si particles is 2 μm, and the number of particles exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of TiB phase and Ti particles is 1 μm, and the number of them exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope.
对比例10：Mg 2Si颗粒的最大长度2μm，其中扫描电镜100倍视场下，超过2μm数量0个。Fe相颗粒最大长度5μm，其中扫描电镜100倍视场下，超过3μm数量不超过3个。TiB相及Ti颗粒最大长度1μm，其中扫描电镜100倍视场下，超过2μm数量0个。 Comparative Example 10: The maximum length of Mg 2 Si particles is 2 μm, and the number of particles exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope. The maximum length of Fe phase particles is 5 μm, and under the 100 times field of view of the scanning electron microscope, the number of particles exceeding 3 μm shall not exceed 3. The maximum length of TiB phase and Ti particles is 1 μm, and the number of them exceeding 2 μm is 0 under the 100 times field of view of the scanning electron microscope.
上面结合实施例对本发明作了详细说明，但是本发明不限于上述实施例，在所属技术领域普通技术人员所具备的知识范围内，还可以在不脱离本发明宗旨的前提下作出各种变化。The present invention has been described in detail above in conjunction with the embodiments, but the present invention is not limited to the above embodiments, and various changes can be made within the scope of knowledge of those of ordinary skill in the art without departing from the gist of the present invention.

Claims (10)

  1. 一种铝合金材料，其特征在于，以质量百分比计，由以下组分制备得到：An aluminum alloy material is characterized in that, in terms of mass percentage, it is prepared from the following components:
    Si：0.30％～0.80％，Si: 0.30% to 0.80%,
    Mg：0.35％～0.90％，Mg: 0.35% to 0.90%,
    Cu：0.90％～2.20％，Cu: 0.90%～2.20%,
    Mn：0.05％～0.15％，Mn: 0.05% to 0.15%,
    Ti：0.002％～0.015％，Ti: 0.002% to 0.015%,
    B：≤0.0050％，B: ≤0.0050%,
    余量为Al，The balance is Al,
    所述铝合金材料中含有游离Si，所述游离Si的质量百分比为0.09～0.35％，所述游离Si的计算方法为：Si％-Mg％×0.578。The aluminum alloy material contains free Si, the mass percentage of the free Si is 0.09-0.35%, and the calculation method of the free Si is: Si%-Mg%×0.578.
  2. 根据权利要求1所述的铝合金材料，其特征在于，所述铝合金材料中，硼元素含量≤0.0050％，铁元素含量≤0.09％，单种杂质元素含量≤0.03％，杂质元素含量合计≤0.15％。The aluminum alloy material according to claim 1, characterized in that, in the aluminum alloy material, the content of boron element ≤ 0.0050%, the content of iron element ≤ 0.09%, the content of a single impurity element ≤ 0.03%, and the total content of impurity elements ≤ 0.15%.
  3. 根据权利要求1所述的铝合金材料，其特征在于，所述铝合金材料的屈服强度≥450MPa。The aluminum alloy material according to claim 1, characterized in that, the yield strength of the aluminum alloy material is ≥450 MPa.
  4. 根据权利要求1所述的铝合金材料，其特征在于，所述铝合金材料中含有Mg 2Si颗粒，所述Mg 2Si颗粒的长度≤5μm。 The aluminum alloy material according to claim 1, characterized in that the aluminum alloy material contains Mg 2 Si particles, and the length of the Mg 2 Si particles is ≤5 μm.
  5. 根据权利要求1所述的铝合金材料，其特征在于，所述铝合金材料中，Fe相颗粒的长度≤7μm。The aluminum alloy material according to claim 1, characterized in that, in the aluminum alloy material, the length of the Fe phase particles is ≤7 μm.
  6. 根据权利要求1所述的铝合金材料，其特征在于，所述铝合金材料中，TiB相颗粒的长度≤3μm。The aluminum alloy material according to claim 1, characterized in that, in the aluminum alloy material, the length of the TiB phase particles is ≤3 μm.
  7. 一种制备如权利要求1至6任一项所述的铝合金材料的方法，其特征在于，包括以下步骤：A method for preparing the aluminum alloy material according to any one of claims 1 to 6, characterized in that it comprises the following steps:
    S1：按照配比进行备料，将铝锭熔化后，加入镁锭和中间合金，得到铝合金液I；S1: prepare materials according to the proportion, melt the aluminum ingots, add magnesium ingots and intermediate alloys, and obtain aluminum alloy liquid I;
    S2：加入精炼剂对所述铝合金液I进行精炼，得到铝合金液II；S2: adding a refining agent to refine the aluminum alloy liquid I to obtain aluminum alloy liquid II;
    S3：加入晶粒细化剂对所述铝合金液II进行在线晶粒细化处理，得到铝合金液III；S3: Adding a grain refiner to perform on-line grain refinement treatment on the aluminum alloy liquid II to obtain the aluminum alloy liquid III;
    S4：将所述铝合金液III过滤后，进行铸造和均匀化处理。S4: After filtering the aluminum alloy liquid III, casting and homogenization treatment are performed.
  8. 根据权利要求7所述的方法，其特征在于，所述均匀化处理的方法为：先将材料升温至480℃～500℃，保温2h～6h，继续升温至550℃～575℃，保温12h～24h。The method according to claim 7, characterized in that, the homogenization treatment method is as follows: first heat the material to 480°C-500°C, keep it warm for 2h-6h, continue to heat up to 550°C-575°C, and keep it warm for 12h- 24h.
  9. 根据权利要求7所述的方法，其特征在于，所述方法还包括在步骤S4之后，对材料进行成型处理。The method according to claim 7, further comprising, after step S4, performing a molding treatment on the material.
  10. 一种如权利要求1至6任一项所述的铝合金材料在制备3C产品外壳中的应用。An application of the aluminum alloy material as claimed in any one of claims 1 to 6 in the preparation of a 3C product shell.
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CN110358951A (en) * 2019-08-06 2019-10-22 广东和胜工业铝材股份有限公司 It is a kind of high to lead high strength alumin ium alloy and preparation method thereof
CN111118353A (en) * 2020-01-17 2020-05-08 广东和胜工业铝材股份有限公司 Aluminum alloy and manufacturing method thereof
CN114351019A (en) * 2021-12-06 2022-04-15 广东和胜工业铝材股份有限公司 Aluminum alloy material and preparation method and application thereof

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