WO2021193064A1 - アルミニウム合金部材及びその製造方法 - Google Patents

アルミニウム合金部材及びその製造方法 Download PDF

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WO2021193064A1
WO2021193064A1 PCT/JP2021/009517 JP2021009517W WO2021193064A1 WO 2021193064 A1 WO2021193064 A1 WO 2021193064A1 JP 2021009517 W JP2021009517 W JP 2021009517W WO 2021193064 A1 WO2021193064 A1 WO 2021193064A1
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Prior art keywords
aluminum alloy
mass
alloy member
base material
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English (en)
French (fr)
Japanese (ja)
Inventor
飯塚　章
直人 古村
耕一 中野
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Nippon Light Metal Co Ltd
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Nippon Light Metal Co Ltd
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Priority to KR1020227036968A priority Critical patent/KR20220158055A/ko
Priority to EP21774412.7A priority patent/EP4130315A4/en
Priority to CN202180024400.4A priority patent/CN115315544A/zh
Priority to US17/913,035 priority patent/US20230175159A1/en
Priority to JP2022509562A priority patent/JPWO2021193064A1/ja
Publication of WO2021193064A1 publication Critical patent/WO2021193064A1/ja
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    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D11/00—Electrolytic coating by surface reaction, i.e. forming conversion layers
    • C25D11/02—Anodisation
    • C25D11/04—Anodisation of aluminium or alloys based thereon
    • C25D11/18—After-treatment, e.g. pore-sealing
    • C25D11/20—Electrolytic after-treatment
    • C25D11/22—Electrolytic after-treatment for colouring layers
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D11/00—Electrolytic coating by surface reaction, i.e. forming conversion layers
    • C25D11/02—Anodisation
    • C25D11/04—Anodisation of aluminium or alloys based thereon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/16—Both compacting and sintering in successive or repeated steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
    • 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
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • 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
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • C22C1/0416—Aluminium-based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • 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
    • C22C32/001—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 with only oxides
    • C22C32/0015—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 with only oxides with only single oxides as main non-metallic constituents
    • C22C32/0036—Matrix based on Al, Mg, Be or alloys thereof
    • 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
    • C22C32/0047—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 with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0078—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 with carbides, nitrides, borides or silicides as the main non-metallic constituents only silicides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B22F2003/241—Chemical after-treatment on the surface
    • B22F2003/242—Coating
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/05—Light metals
    • B22F2301/052—Aluminium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D11/00—Electrolytic coating by surface reaction, i.e. forming conversion layers
    • C25D11/02—Anodisation
    • C25D11/04—Anodisation of aluminium or alloys based thereon
    • C25D11/06—Anodisation of aluminium or alloys based thereon characterised by the electrolytes used
    • C25D11/08—Anodisation of aluminium or alloys based thereon characterised by the electrolytes used containing inorganic acids

Definitions

  • the present invention relates to an aluminum alloy member whose surface is required to be blackened or darkened, and a method for manufacturing the same.
  • the surface of the optical member, the electronic circuit member, and the aluminum alloy used for the inspection device of these members is blackened with an organic dye after anodizing treatment such as alumite sulfate treatment in order to suppress light reflection. It is common to be done.
  • Patent Document 1 Japanese Unexamined Patent Publication No. 2010-237282
  • a support frame for a pellicle which is formed of an aluminum material made of aluminum or an aluminum alloy, has an optical thin film body, and is used as a pellicle.
  • a method for manufacturing a support frame for a pellicle, which comprises the above, is disclosed.
  • the aluminum material is anodized with an alkaline aqueous solution containing tartaric acid without using sulfuric acid, which is the largest causative substance of haze, to provide corrosion resistance and It is said that it is possible to obtain a support frame for pellicle that has excellent durability and reduces the occurrence of haze as much as possible.
  • the pellicle frame is formed in a frame shape, and is composed of a sintered body having a Young's modulus of 150 GPa or more and a Vickers hardness of 800 or more, and has a frame shape.
  • the corner portion is secured to have a width equal to or larger than the width of the straight portion, and at least one of the corner portions is a pellicle frame wider than the width of the straight portion, and the pellicle frame is made of ceramics, cemented carbide or cermet. It is disclosed to do.
  • the pellicle frame described in Patent Document 2 uses a sintered body having a high Young's modulus and Vickers hardness, the pellicle frame is deformed by the film tension generated when the pellicle film is stretched on the pellicle frame. Can be suppressed. Moreover, since the width of at least one corner portion is wider than the width of the straight portion, the strength of the corner portion can be increased, and the deformation and damage of the pellicle frame can be further suppressed.
  • the support frame for a pellicle described in Patent Document 1 has excellent stability that does not form a reaction product (haze) such as ammonium sulfate even when energy is input from a high-power short-wavelength exposure light source.
  • a reaction product such as ammonium sulfate
  • no consideration is given to color loss when the product is kept in a high temperature environment. Further, it has not been studied to suppress the misalignment caused by the large coefficient of linear expansion of the aluminum material.
  • Patent Document 2 has high mechanical properties at room temperature, thermal expansion and blackening of the surface in a high temperature environment have not been studied.
  • ceramics having poor workability, cemented carbide having a large specific gravity, and cermet are used, and it is difficult to widely use them as optical members.
  • an object of the present invention is a lightweight aluminum alloy member that can be manufactured at a relatively low cost, has high dimensional accuracy in a high temperature environment, and is blackened even in a high temperature environment. It is an object of the present invention to provide an aluminum alloy member having excellent heat resistance and an efficient manufacturing method thereof, in which the surface of the aluminum alloy is not easily faded.
  • the present inventors have obtained an extruded material of aluminum alloy powder having a specific composition having a low linear expansion coefficient. It has been found that it is effective to form an electrolytically colored layer in which a metal or a metal salt is precipitated in the pores of the anodized film, and the present invention has been reached.
  • the present invention It consists of an extruded aluminum powder alloy with a Si content of 20-40% by mass.
  • an aluminum alloy member which is characterized by the above.
  • Si has the effect of lowering the coefficient of linear expansion and improving Young's modulus and wear resistance by crystallizing as a Si phase in the Al matrix.
  • a high Young's modulus, excellent wear resistance and a low coefficient of linear expansion are realized by setting the Si content to 20% by mass or more, and processing is performed by setting the Si content to 40% by mass or less. It suppresses the decrease in strength and toughness due to the decrease in properties and the coarsening of the Si phase.
  • the more preferable Si content is 24 to 28% by mass.
  • the surface of the aluminum alloy member of the present invention is blackened by an electrolytic colored layer in which a metal or a metal salt is precipitated in the pores of the anodized film, and the surface is blackened as compared with the case where the aluminum alloy member is blackened with an organic dye. Fading in a high temperature environment is suppressed extremely effectively. That is, in the aluminum alloy member of the present invention, both the reduction of the coefficient of linear expansion and the suppression of fading in a high temperature environment are realized.
  • the aluminum alloy member of the present invention has a smaller specific gravity than the cemented carbide or cermet, and the optical member can be made lighter.
  • it is easy to handle because it has excellent toughness as compared with ceramics and cemented carbide. Further, since it has good workability, it is possible to reduce the manufacturing cost and to impart high dimensional accuracy to the optical member.
  • the aluminum powder alloy contains Si: 20 to 40% by mass, Mg: 0.2 to 1.2% by mass, Cu: 2% by mass or less, Fe: 2% by mass or less, Cr. : It is preferably 0.4% by mass or less, and the balance is composed of Al and unavoidable impurities.
  • the aluminum alloy member is provided with excellent mechanical properties, corrosion resistance and heat resistance by strengthening precipitation by adding Mg and Cu, improving Young's modulus and corrosion resistance by adding Fe, and refining crystal grains by adding Cr. be able to.
  • the metal and the metal salt contain at least one of Ni, Co, Cu, Sn, Mn, Fe, Pb, Ca, Zn and Mg. By including these elements, blackening of the surface can be efficiently and surely achieved.
  • the coefficient of linear expansion is 10 ⁇ 10 -6 to 23 ⁇ 10 -6 / K.
  • the coefficient of linear expansion is close to that of a material made of silicon or the like.
  • the value is set to 23 ⁇ 10 -6 / K or less, it is possible to suppress the displacement due to thermal expansion in a high temperature environment (for example, 200 ° C.).
  • the more preferable range of the coefficient of linear expansion is 13 ⁇ 10 -6 to 20 ⁇ 10 -6 / K
  • the most preferable range of the coefficient of linear expansion is 15 ⁇ 10 -6 to 19 ⁇ 10 -6 / K. ..
  • the difference between the L * value as before heat treatment L * value after the heat treatment of holding for 100 hours in an atmosphere of 200 ° C. is 3 or less, are preferred. If the difference between the L * value before heating L * value after heating is 3 or less, need hardly consider the fading in a high-temperature environment in which the optical member is used.
  • the difference between the L * value before heating L * value after heating is 2 or less, and most preferably 1 or less.
  • the L * value of the aluminum alloy member is more preferably 50 or less, and further preferably 45 or less.
  • the aluminum alloy member of the present invention is an optical member or a member for an optical member inspection device. Since the aluminum alloy member of the present invention is an aluminum alloy member having high dimensional accuracy in a high temperature environment and having a blackened surface that is hard to fade even in a high temperature environment and has excellent heat resistance, it is an optical member or an optical member. It can be suitably used as a member for an inspection device.
  • the optical member inspection device an inspection light source device for a CCD / C-MOS image sensor can be exemplified.
  • the present invention The first step of producing a base material by subjecting aluminum alloy powder having a Si content of 20 to 40% by mass to pressure molding, sintering and extrusion processing.
  • the second step of forming an anodized film on the surface of the base material and The base material is electrolytically colored in an electrolytic solution containing a metal or a metal salt, and the metal or the metal salt is precipitated in the pores of the anodized film to form an electrolytically colored layer on the surface of the base material.
  • Including the third step Also provided is a method for manufacturing an aluminum alloy member.
  • a homogeneous aluminum alloy By extruding a sintered body of aluminum alloy powder, a homogeneous aluminum alloy can be obtained even if the Si content is 20 to 40% by mass. Further, by electrolytically coloring an aluminum alloy material having an anodized film in an electrolytic solution containing a metal or a metal salt, a metal or a metal salt is precipitated in the pores of the anodized film to achieve blackening. Can be done.
  • the present invention is a lightweight aluminum alloy member that can be manufactured at a relatively low cost, has high dimensional accuracy in a high temperature environment, and has excellent heat resistance because the blackened surface does not easily fade even in a high temperature environment. It is possible to provide an aluminum alloy member and an efficient manufacturing method thereof.
  • FIG. 1 shows a schematic cross-sectional view of the aluminum alloy member of the present invention.
  • the aluminum alloy member 1 has an anodic oxide film 4 formed on the surface of the aluminum alloy base material 2, and includes an electrolytic colored layer 6 in which a metal or a metal salt is deposited in the pores of the anodic oxide film 4.
  • the aluminum alloy base material 2 contains Si: 20 to 40% by mass, Mg: 0.2 to 1.2% by mass, Cu: more than 0 and 2% by mass or less, Fe: more than 0 and 2% by mass or less, Cr: more than 0 and 0. .4% by mass or less, and the balance is composed of extruded aluminum alloy powder sintered body composed of Al and unavoidable impurities.
  • Si In addition to contributing to the improvement of Young's modulus by crystallizing Si as the Si phase in the Al matrix phase, it has the effect of improving the wear resistance and lowering the coefficient of thermal expansion.
  • a high Young's modulus, excellent abrasion resistance and a low coefficient of linear expansion are realized by setting the Si content to 20% by mass or more, and workability is achieved by setting the Si content to 40% by mass or less.
  • the decrease in strength and toughness due to the decrease in Si phase and the coarsening of the Si phase are suppressed.
  • the Si content is more preferably 22 to 35% by mass, further preferably 24 to 30% by mass, and particularly preferably 25 to 28% by mass.
  • Mg The Mg content is 0.2 to 1.2% by mass. By setting the Mg content in this range, it is possible to improve the strength by strengthening precipitation. (Precipitation strengthening with Mg 2 Si and Al 2 Cu Mg). The more preferable Mg content is 0.55 to 0.90% by mass.
  • the Cu content is more than 0 and 2% by mass or less. By setting the Cu content in this range, it is possible to improve the strength by strengthening precipitation as in the case of Mg described above. (Precipitation strengthening with Mg 2 Si and Al 2 Cu Mg). It also contributes to improving Young's modulus and corrosion resistance. If it is more than 2% by mass, the anodizing film property is lowered. The more preferable Cu content is 0.11 to 0.30% by mass.
  • the Fe content is more than 0 and 2% by mass or less. By setting the Fe content in this range, it contributes to the improvement of Young's modulus and the improvement of corrosion resistance. If it is more than 2% by mass, elongation, thermal conductivity, and extrusion decrease. The more preferable Fe content is 0.7% by mass or less.
  • the Cr content is more than 0 and 0.4% by mass or less. By setting the Cr content in this range, the crystal is made finer and contributes to the improvement of toughness.
  • the more preferable Cr content is 0.03 to 0.26% by mass.
  • the rest is substantially composed of Al.
  • unavoidable impurities may be contained as other components.
  • the aluminum alloy base material 2 preferably has a coefficient of linear expansion of 10 ⁇ 10 -6 to 23 ⁇ 10 -6 / K.
  • the coefficient of linear expansion is close to that of a material made of silicon or the like. Further, by setting the value to 23 ⁇ 10 -6 / K or less, it is possible to suppress the displacement due to thermal expansion in a high temperature environment (for example, 200 ° C.).
  • the more preferable range of the coefficient of linear expansion is 13 ⁇ 10 -6 to 20 ⁇ 10 -6 / K
  • the most preferable range of the coefficient of linear expansion is 15 ⁇ 10 -6 to 19 ⁇ 10 -6 / K. ..
  • the film quality of the anodized film 4 is not particularly limited as long as the effects of the present invention are not impaired, and various conventionally known anodized films can be used.
  • Anodizing treatment may be performed using a sulfuric acid bath, or the aluminum alloy base material 2 may be formed by anodizing treatment in an alkaline bath.
  • anodizing is performed using a sulfuric acid bath, there is a risk that inorganic acids such as sulfuric acid and phosphoric acid may remain on the anodized film 4 on the surface of the aluminum alloy base material 2 due to this. There is.
  • the inorganic acid reacts with a basic substance such as ammonia present in the exposed atmosphere to generate a reaction product (haze) such as ammonium sulfate, and the reaction product (haze).
  • a reaction product such as ammonium sulfate
  • the reaction product haze
  • an alkaline bath for the anodizing treatment it is possible to prevent the residual inorganic acid forming the reaction product (haze) from remaining.
  • the film thickness of the anodized film 4 is not particularly limited as long as the effect of the present invention is not impaired, but it is preferably 1 to 15 ⁇ m.
  • a homogeneous anodized film 4 can be formed by setting the film thickness to 1 ⁇ m or more, and a decrease in strength of the anodized film 4 can be suppressed by setting the film thickness to 15 ⁇ m or less.
  • the metal or metal salt precipitated in the pores of the anodized film 4 contains at least one of Ni, Co, Cu, Sn, Mn, Fe, Pb, Ca, Zn and Mg. , are preferred.
  • Ni, Co, Cu, Sn, Mn, Fe, Pb, Ca, Zn and Mg. are preferred.
  • blackening of the surface can be efficiently and surely achieved.
  • fading in a high temperature environment can be reliably reduced as compared with the case of blackening with an organic dye.
  • Ni, Co, Cu and Sn are more preferable, and Ni is even more preferable.
  • the difference between the L * value before heating L * value after heating is 3 or less, are preferred. If the difference between the L * value before heating L * value after heating is 3 or less, need hardly consider the fading in a high-temperature environment in which the optical member is used.
  • the difference between the L * value before heating L * value after heating is 2 or less, and most preferably 1 or less.
  • the L * value of the aluminum alloy member 1 is more preferably 50 or less, and further preferably 45 or less.
  • the aluminum alloy member 1 is an optical member or a member for an optical member inspection device.
  • the aluminum alloy member of the present invention is an aluminum alloy member having high dimensional accuracy in a high temperature environment and having a blackened surface that is hard to fade even in a high temperature environment and has excellent heat resistance, it is an optical member or an optical member. It can be suitably used as a member for an inspection device.
  • the optical member inspection device an inspection light source device for a CCD / C-MOS image sensor can be exemplified.
  • the optical member include a pellicle frame, a lens holder, a barrel, a shade, a reflector, and the like.
  • the manufacturing method of the aluminum alloy member of the present embodiment includes a first step (S01) of manufacturing a base material and a first step of forming an anodized film on the surface of the base material. It includes a second step (S02) and a third step (S03) of forming an electrolytically colored layer on the surface of the base material.
  • S01 first step of manufacturing a base material
  • S02 second step of forming an anodized film on the surface of the base material.
  • S03 a third step of forming an electrolytically colored layer on the surface of the base material.
  • the base material manufacturing step (S01) is a step for manufacturing the aluminum alloy base material 2 through pressure molding, sintering, and extrusion processing using an aluminum alloy powder having a Si content of 20 to 40% by mass as a raw material. ..
  • the aluminum alloy powder contains Si: 20 to 40% by mass, Mg: 0.2 to 1.2% by mass, Cu: more than 0% by mass and less than 2% by mass, Fe: more than 0 and 2% by mass or less, Cr: more than 0 and 0.4% by mass. It is preferably mass% or less, and the balance is preferably composed of Al and unavoidable impurities.
  • the method of pressure molding on the aluminum alloy powder is not particularly limited as long as the effect of the present invention is not impaired, and various conventionally known methods can be used. For example, a press method, a CIP method, or the like can be used. ..
  • the molding pressure for pressure molding may be appropriately set according to the composition, shape, particle size, etc. of the aluminum alloy powder.
  • the conditions for sintering the pressure molded body are appropriately adjusted according to the composition, particle size and shape of the aluminum alloy powder, the density of the pressure molded body, etc., and a good extruded material is obtained by hot extrusion.
  • the sintering conditions may be used so that a sintered body in a state where it can be obtained can be obtained.
  • the pressure molded body is held in a vacuum furnace having a vacuum degree of 1 Torr or less and a furnace temperature controlled to 100 to 400 ° C. for 0.5 to 2 hours, and then the vacuum degree is 1 Torr.
  • the temperature inside the furnace may be raised to 520 to 570 ° C. and held for 1 to 6 hours while keeping the temperature below (preferably 0.1 Torr or less).
  • hot extrusion for extrusion of aluminum alloy powder sintered body.
  • the hot extrusion method and conditions are not particularly limited as long as the effects of the present invention are not impaired, and conventionally known hot extrusion methods and conditions for aluminum alloy powder sintered bodies may be used, but the hot extrusion temperature. May be set to about 400 to 500 ° C.
  • a metal plate for example, pure aluminum or a 5000 series aluminum alloy
  • a thin film having a metal plate composition can be formed on the surface of the extruded material, which causes pitting corrosion and total corrosion over time at the interface between Si and Al, which may occur when the Al—Si material is on the outermost surface. It can be suppressed.
  • the hot-extruded molded product is forged or the like to give it a desired shape, if necessary.
  • the molded product may be heat-treated prior to the forging or the like.
  • the forging property of the hot-extruded molded product can be improved by performing the heat treatment at 200 to 400 ° C. for about 0.5 to 2 hours.
  • the anodizing film forming step (S02) is a step for forming the anodizing film 4 on the surface of the aluminum alloy base material 2 obtained in the base material manufacturing step (S01).
  • the conditions of the anodizing treatment are not particularly limited as long as the effects of the present invention are not impaired, and various conventionally known anodizing treatments can be used.
  • a sulfuric acid bath or any one or more inorganic alkaline components selected from the group consisting of sodium hydroxide, potassium hydroxide, lithium hydroxide, calcium hydroxide, strontium hydroxide, and rubidium hydroxide may be used.
  • An inorganic alkaline bath containing, or a salt of any one or more organic acids selected from the group consisting of tartaric acid, citric acid, oxalic acid, and salicylic acid, and sodium hydroxide, potassium hydroxide, lithium hydroxide, and water.
  • An alkali mixed bath or the like containing any one or more inorganic alkali components selected from the group consisting of calcium oxide, strontium hydroxide, and rubidium hydroxide is preferably used.
  • Electrolytic colored layer forming step (third step: S03) is a step for precipitating a metal or a metal salt in the pores of the anodic oxide film 4 formed in the anodic oxide film forming step (S02) to form the electrolytic colored layer 6. be.
  • the aluminum alloy base material 2 on which the anodic oxide film 4 is formed is immersed in an electrolytic treatment liquid containing a soluble metal salt, subjected to a color pretreatment for constant current electrolysis using the aluminum alloy base material 2 as an anode, and then the same electrolytic treatment liquid.
  • the aluminum alloy base material 2 may be used as a cathode for electrolytic coloring treatment, or the coloring pretreatment may be omitted.
  • the current density of the positive component is substantially equal to the current density at the time of the coloring pretreatment, and specifically, 1 / 0.6 to 1/0 of the cathode current density at the time of electrolytic coloring. It is preferable to set it in the range of 95 times.
  • the absolute value of the maximum current density of the negative component is preferably set in the range of 0.6 to 0.95 times the absolute value of the maximum current density of the positive component. maintain.
  • the potential difference in the electrolytic coloring treatment tank is kept at 4 V or less, and the absolute value of the current density at the time of electrolytic coloring is set to 0 of the current density at the time of pre-coloring treatment. It is preferable to maintain it at about 7 times.
  • the current density of the cathode current flowing through the aluminum alloy base material 2 during electrolytic coloring is set to a value in the range of 0.6 to 0.95 times the anode current flowing through the aluminum alloy base material 2 during the pre-coloring treatment, the anode current flows.
  • the current distribution is the same and uniform depending on whether the current flows or the cathode current flows.
  • a uniform electrolytic coloring reaction occurs over the entire surface of the aluminum alloy base material 2, and a colored film having excellent color tone uniformity is formed.
  • the coloring pretreatment is applied to the anodized aluminum alloy base material 2 using the same treatment liquid as the electrolytic coloring treatment liquid used in the subsequent coloring step.
  • the non-uniformity of the current distribution during the coloring treatment is corrected by the coloring pretreatment.
  • the coloring pretreatment and the coloring treatment are carried out in different tanks, that is, in different electrolytic cell conditions and bath conditions, the optimum current density ratio Rd for homogenizing the color tone differs between the tanks, so that the same electrolysis is performed.
  • the uniformity of color tone is reduced as compared with the case of using a tank.
  • the electrolytic coloring treatment bath is not particularly restricted by the component type, concentration, etc., but usually a weakly acidic to neutral treatment bath is used.
  • Metal salts include nitrates containing at least one of Ni, Co, Cu, Sn, Mn, Fe, Pb, Ca, Zn, and Mg, inorganic acid salts such as sulfates, phosphates, and chromate, and oxalic acid.
  • organic acid salts such as salts, acetates and tartrates, which are added to the electrolytic coloring treatment bath alone or in combination. In the electrolytic coloring method, even if the same electrolytic treatment bath is used, different color tones are developed depending on the treatment conditions such as applied voltage, current, and time.
  • electrolytic conditions such as voltage, current, temperature, and time are set in order to eliminate variations in the thickness of the barrier layer in these electrolytic coloring treatment liquids.
  • the electrolytic conditions depend on the type of electrolytic coloring treatment liquid to be used, but are appropriately selected within the range of a voltage of 20 to 70 V, a current of 10 to 50 A / m 2 , a temperature of 10 to 30 ° C., and a treatment time of 100 seconds or less. It is preferable to do so.
  • a voltage of 20 to 70 V, a current of 10 to 50 A / m 2, and a current of 10 to is preferable to appropriately select the temperature within the range of 30 ° C. and the treatment time of 600 seconds or less.
  • the waveform of the current used for the coloring pretreatment and the electrolytic coloring treatment is not particularly restricted.
  • a direct current, a pulse wave, a square wave, a sine wave, a waveform similar to these, a waveform obtained by combining these, and the like can be used.
  • the positive component (anode current) during the electrolytic coloring process is used as the anode current during the pre-coloring process in order to make the current distribution of each part uniform. It is effective to make them substantially equal, or to set the anode current during the electrolytic coloring treatment to 1 / 0.6 to 1 / 0.95 of the cathode current during the electrolytic coloring pretreatment.
  • the electrolytic coloring reaction proceeds with a uniform current distribution over the entire surface, so that the electrolytic coloring layer 6 having excellent color tone uniformity is formed.
  • the electrolytically colored aluminum alloy base material 2 can be sealed or the like according to a conventional method.
  • Example 1 Aluminum alloy powder having a composition of Si: 27% by mass, Fe: 0.25% by mass, Cu: 0.25% by mass, Mg: 0.7% by mass, Cr: 0.15% by mass is 565 ° C. after CIP molding. It was sintered by holding it in a vacuum atmosphere for 4 hours, and formed into a columnar shape having a bulk density of 2.3 g / cm 3 and an outer diameter of 250 mm. The particle size of the aluminum alloy powder used as a raw material is 93%, which is less than 150 ⁇ m.
  • the obtained sintered body was hot-extruded as a billet for hot extrusion.
  • the billet was heated at 450 ° C. and inserted into a container of a 10-inch extruder to obtain a plate-shaped extruder having a width of 100 mm and a thickness of 8 mm by extrusion molding.
  • the obtained extruded material was cut to produce an aluminum alloy base material having a size of 50 ⁇ 50 ⁇ 10 mm.
  • the aluminum alloy base material was subjected to an anodic oxide film treatment under the conditions of a current density of 15 mA / cm 2 and a treatment time of 1333 seconds using a sulfuric acid bath having a concentration of 180 g / l to form an anodic oxide film.
  • the aluminum alloy base material after forming the anodic oxide film is used as the anode, SUS304 pole is used as the counter electrode, and nickel sulfate hexahydrate: 140 g / l, boric acid: 40 g / l, and tartrate acid: 4 g / l as the electrolytic bath.
  • Aluminum alloy group after pre-coloring treatment in which a DC current is passed under the conditions of an anode current density of 2.5 mA / cm 2 and an energization time of 5 seconds in an electrolytic bath having a composition (pH 5, temperature 30 ° C.)
  • a DC current with a pulsed voltage superimposed on the counter electrode SUS304
  • cathode current density 2.5 mA / cm. 2.
  • the electrolytic coloring layer was formed by performing the electrolytic coloring treatment under the conditions of the electrolytic time: 360 seconds, and the aluminum alloy member of Example 1 was obtained.
  • Comparative Example 1 A 50 ⁇ 50 ⁇ 10 mm aluminum alloy base material was produced by cutting a JIS-A5052 aluminum alloy material. Using this aluminum alloy base material, the aluminum alloy of Comparative Example 1 is subjected to a dyeing treatment in which an organic dye (TAC411 manufactured by Okuno Pharmaceutical Co., Ltd.) is placed in an aqueous solution containing a concentration of 10 g / L and immersed at a temperature of 55 ° C. for 10 minutes. Obtained a member.
  • an organic dye TAC411 manufactured by Okuno Pharmaceutical Co., Ltd.
  • Comparative Example 2 An aluminum alloy base material was produced in the same manner as in Example 1, and an anodized film was formed on the aluminum alloy base material in the same manner as in Example 1. The aluminum alloy base material after the formation of the anodized film was dyed in the same manner as in Comparative Example 1 to obtain the aluminum alloy member of Comparative Example 2.
  • Electrolytic coloring layer 1 ... Aluminum alloy member, 2 ... Aluminum alloy base material, 4 ... Anodized film, 6 . Electrolytic coloring layer.

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JPS60110895A (ja) * 1983-11-21 1985-06-17 Nippon Alum Mfg Co Ltd:The アルミニウム及びアルミニウム合金の電解着色方法
JP2010237282A (ja) 2009-03-30 2010-10-21 Nippon Light Metal Co Ltd ペリクル用支持枠の製造方法及びペリクル用支持枠並びにペリクル
JP2016177120A (ja) 2015-03-20 2016-10-06 日本特殊陶業株式会社 ペリクル枠およびペリクル枠の製造方法
JP2016216763A (ja) * 2015-05-15 2016-12-22 株式会社豊田中央研究所 被覆部材およびその製造方法
WO2018012324A1 (ja) * 2016-07-12 2018-01-18 日本軽金属株式会社 ペリクル枠及びペリクル
JP2019105714A (ja) * 2017-12-12 2019-06-27 日本軽金属株式会社 Ｆｐｄ（フラットパネルディスプレイ）用ペリクル枠体及びその製造方法

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DE19950595C1 (de) * 1999-10-21 2001-02-01 Dorn Gmbh C Verfahren zur Herstellung von Sinterteilen aus einer Aluminiumsintermischung
JP5864359B2 (ja) * 2011-05-20 2016-02-17 日本軽金属株式会社 ペリクル用支持枠の製造方法
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JPS60110895A (ja) * 1983-11-21 1985-06-17 Nippon Alum Mfg Co Ltd:The アルミニウム及びアルミニウム合金の電解着色方法
JP2010237282A (ja) 2009-03-30 2010-10-21 Nippon Light Metal Co Ltd ペリクル用支持枠の製造方法及びペリクル用支持枠並びにペリクル
JP2016177120A (ja) 2015-03-20 2016-10-06 日本特殊陶業株式会社 ペリクル枠およびペリクル枠の製造方法
JP2016216763A (ja) * 2015-05-15 2016-12-22 株式会社豊田中央研究所 被覆部材およびその製造方法
WO2018012324A1 (ja) * 2016-07-12 2018-01-18 日本軽金属株式会社 ペリクル枠及びペリクル
JP2019105714A (ja) * 2017-12-12 2019-06-27 日本軽金属株式会社 Ｆｐｄ（フラットパネルディスプレイ）用ペリクル枠体及びその製造方法

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