WO2017006816A1 - Matériau extrudé en alliage d'aluminium pourvu d'un film d'oxyde d'électrode positive, ayant un très bon aspect extérieur, et son procédé de production - Google Patents

Matériau extrudé en alliage d'aluminium pourvu d'un film d'oxyde d'électrode positive, ayant un très bon aspect extérieur, et son procédé de production Download PDF

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WO2017006816A1
WO2017006816A1 PCT/JP2016/069211 JP2016069211W WO2017006816A1 WO 2017006816 A1 WO2017006816 A1 WO 2017006816A1 JP 2016069211 W JP2016069211 W JP 2016069211W WO 2017006816 A1 WO2017006816 A1 WO 2017006816A1
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aluminum alloy
extruded material
extrusion
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PCT/JP2016/069211
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English (en)
Japanese (ja)
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政仁 谷津倉
完聡 宮浦
藤井　高志
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日本軽金属株式会社
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Priority claimed from PCT/JP2015/072920 external-priority patent/WO2017006490A1/fr
Application filed by 日本軽金属株式会社 filed Critical 日本軽金属株式会社
Priority to KR1020187003476A priority Critical patent/KR20180025955A/ko
Priority to CN201680040087.2A priority patent/CN107735503A/zh
Priority to JP2016567441A priority patent/JP6119937B1/ja
Publication of WO2017006816A1 publication Critical patent/WO2017006816A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • 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
    • 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
    • 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
    • C22F1/053—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 zinc as the next major constituent
    • 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
    • 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

Definitions

  • the present invention relates to an aluminum alloy extruded material having an anodized film and excellent in appearance quality, and a method for producing the same, and more particularly, to an aluminum alloy extruded material for an electronic device casing excellent in anodized film property and a method for producing the same. .
  • the metal structure is a recrystallized structure
  • the streak pattern is reduced, but sufficient aesthetics cannot be obtained.
  • the inventor of the present application has conducted extensive research on the cause of streak patterns.
  • concentration segregation of elements other than aluminum in the crystal and at the grain boundaries, the crystallization state of the compound, and the recrystallization It was found that the difference in grain size between crystal structures greatly affected.
  • the portion where elements other than aluminum are segregated and the portion where there is a crystallized product tend to form an anodic oxide film less easily than other portions. This is considered to be due to the difference in electrical properties due to the effect of concentration segregation. That is, the peritectic elements are concentrated in the crystal grains, the eutectic elements are swept out to the crystal grain boundaries, and concentration segregation occurs between the crystal grains and the crystal grain boundaries.
  • the concentration segregation part When extruded, the concentration segregation part is stretched in the extrusion direction as well as the crystal grains of the cast structure, and a thin layer of Zn, Mg main element concentration segregation is formed in a streak shape, and the thickness of the anodized film Is considered to be a cause of visible streaks on the surface of the anodized film.
  • crystallized substances are present, but as crystal grains are stretched by extrusion, such crystallized substances are scattered in the extrusion direction, which causes streaks.
  • the cast structure is stretched to become a fiber-like structure.
  • the concentration segregation part and the crystallized material are also stretched. Even if recrystallization is performed and the crystal structure changes from a fiber-like structure to a recrystallized structure that is equiaxed, the concentration segregation part and the crystallized phase remain and are stretched, so the anodized film It is thought that streaks are visible when processing is performed. Further, it was found that the recrystallized structure also has a streaky portion where crystals with a large difference in crystal grain size are mixed.
  • the inventor of the present application has a high strength of 380 MPa or more, but the concentration segregation, excessive crystallization of the compound, and the crystal grain size of the recrystallized structure.
  • the range of the optimal alloy composition that suppresses the difference was found.
  • An object of the present invention is to provide a 7000 series aluminum alloy extruded material that has a desired strength and is less likely to cause a streak pattern on the surface of an anodized film.
  • an aluminum alloy extruded material Zn: 4.0 mass% or more and 7.5 mass% or less, Mg: 1.0 mass% or more and 2.2 mass% or less, Fe: 0.05 mass% or more and 0.20 mass% or less, Cu: 0.30 mass% or less, Ti: 0.005 mass% or more and 0.04 mass% or less, B: 0.001% by mass or more and 0.02% by mass or less, Si: 0.15 mass% or less, Zr: 0.05% by mass or less, Mn: 0.05% by mass or less, Cr: 0.05% by mass or less, V: 0.05 mass% or less, Containing [Zr + Mn + Cr + V + Ti], which is the total content of Zr, Mn, Cr, V and Ti, [Zr + Mn + Cr + V + Ti] ⁇ 0.10 mass% Satisfy the relationship Except for the range where the Zn content is 6.0% by mass or less and the Mg content is 1.2% by mass or less, The balance consists of aluminum and
  • a Zn high-concentration phase and a Zn low-concentration phase are present in layers in the anodized surface in parallel to the extrusion direction, and are orthogonal to the extrusion direction.
  • the Zn concentration difference is 1% or less in a range of width 0.1 mm or more and 3 mm or less.
  • the crystal grain size of the recrystallized structure on the treated surface of the anodized film is an average value of 200 ⁇ m or less, and the maximum crystal grain size is 1 mm or less.
  • the aluminum alloy extruded material is characterized in that the area ratio of the intermetallic compound (crystallized product) in the anodized surface is less than 2%.
  • the cast material is processed for 1 to 24 hours at a holding condition of the homogenization treatment of 400 to 560 ° C., and the extrusion ratio exceeds 20 in the extrusion process.
  • a method for producing an extruded aluminum alloy characterized in that extrusion is performed so that the temperature of the material is 420 ° C. or higher, and the aging treatment is performed at 100 to 180 ° C. for 1 to 30 hours.
  • a 7000 series aluminum alloy extruded material having a desired strength and excellent in appearance quality in which a streak pattern is difficult to appear on the surface of an anodized film, and a manufacturing method thereof.
  • FIG. 4 is a photograph of the crystal structure of Experimental Example L taken with a polarizing microscope. 4 is a photograph of the crystal structure of Experimental Example H taken with a polarizing microscope. 6 is a photograph of the microstructure of Experimental Example K taken.
  • A A graph showing a concentration analysis of Experimental Example B and (b) a mapping diagram. 10 is a graph showing a concentration analysis of Experimental Example G.
  • A A graph showing concentration analysis of Experimental Example H and (b) a mapping diagram.
  • the aluminum alloy extruded material having an anodized film according to this embodiment is an aluminum alloy extruded material, Zn: 4.0 mass% or more and 7.5 mass% or less, Mg: 1.0 mass% or more and 2.2 mass% or less, Fe: 0.05 mass% or more and 0.20 mass% or less, Cu: 0.30 mass% or less, Ti: 0.005 mass% or more and 0.04 mass% or less, B: 0.001% by mass or more and 0.02% by mass or less, Si: 0.15 mass% or less, Zr: 0.05% by mass or less, Mn: 0.05% by mass or less, Cr: 0.05% by mass or less, V: 0.05 mass% or less, Containing [Zr + Mn + Cr + V + Ti], which is the total content of Zr, Mn, Cr, V and Ti, [Zr + Mn + Cr + V + Ti] ⁇ 0.10 mass% Satisfy the relationship Except for the range where the Zn content is
  • the aluminum alloy extruded material having the above-described configuration has a desired strength and an effect that a streak pattern is difficult to appear on the surface of the anodized film. Below, each element which concerns on the aluminum alloy extrusion material of this embodiment is demonstrated.
  • the aluminum alloy extruded material according to the present embodiment has a Zn content of 4.0% by mass to 7.5% by mass, more preferably 4.0% by mass to 7.0% by mass, More preferably, it is 4.0 mass% or more and 6.0 mass% or less, More preferably, it is 4.0 mass% or more and less than 5.5 mass%, Most preferably, it is 4.0 mass% or more and 5.0 mass%. % Or less.
  • the Mg content is 1.0% by mass or more and 2.2% by mass or less, more preferably 1.2% by mass or more and 2.2% by mass or less. More preferably, it is 1.3 mass% or more and 2.2 mass% or less, More preferably, it is 1.4 mass% or more and 2.2 mass% or less, Most preferably, it is 1.5 mass% or more and 2.2 mass% or less. % Or less.
  • the Zn content is 6.0% by mass or less
  • the Mg content is 1.2% by mass or more, and when the Zn content is less than 5.5% by mass, the Mg content is 1.6% by mass. The above is preferable.
  • the Fe content is 0.05% by mass or more and 0.20% by mass or less.
  • the Fe content is 0.05% by mass or more, coarse recrystallization of the cast structure can be suppressed during the homogenization treatment. If there is a coarse crystal structure in the ingot, non-uniform deformation is likely to occur during the extrusion process, and it becomes difficult to keep the dimensions of the extruded material within a predetermined size (accuracy, twist and bend). Furthermore, if there is a coarse crystal structure in the billet, recrystallized grain structures having different sizes are likely to be mixed even in an equiaxed recrystallized structure during recrystallization after extrusion. Such a structure is arranged in layers, which causes a difference in color tone in a stripe shape.
  • the content of Fe is 0.20% by mass or less, it can be suppressed that Fe forms a compound with other elements to form an excessive crystallized product and a streak pattern is generated.
  • the Fe content is more preferably 0.15% by mass or less, and the above effect is further enhanced within this range.
  • the Cu content is 0.30 mass% or less. If the Cu content exceeds 0.30% by mass, the anodized film tends to be yellowish and the corrosion resistance tends to deteriorate.
  • the Cu content is more than 0.15% by mass, mechanical strength and stress corrosion cracking resistance (SCC) are improved.
  • the Ti content is 0.005 mass% or more and 0.04 mass% or less. Further, in the aluminum alloy extruded material according to this embodiment, the content of B is 0.001% by mass or more and 0.02% by mass or less.
  • the crystal of the cast structure in the alloy is coarse, non-uniform deformation is likely to occur during extrusion, and concentration segregation and non-uniform grain size of the recrystallized structure are likely to occur. At this time, it is added as a grain refiner. When only Ti is added, it dissolves in the matrix phase and the effect as a finer becomes small. Further, since concentration segregation inside the crystal tends to occur, it is preferable to add as a TiB 2 compound using a rod hardener as a refining agent. On the other hand, excessive addition of Ti or B causes excessive crystallization as a compound and causes streak patterns, so the upper limit of the addition amount is required.
  • the Si content is 0.15% by mass or less. Since Si forms a Mg and Mg—Si-based compound and contributes to the streak pattern, it is preferably regulated to 0.15% or less. Moreover, it is more preferable that content of Si is 0.1 mass% or less. If content of Si is this range, said effect will increase more.
  • Zr zirconium, Mn: manganese, Cr: chromium, V: vanadium
  • Mn, Cr, and V have an action of suppressing recrystallization during extrusion, their content is preferably 0.05% by mass or less, more preferably 0.02% by mass or less. It is.
  • These elements also have the effect of suppressing the diffusion of Zn.
  • [Zr + Mn + Cr + V + Ti] which is the total content of Zr, Mn, Cr, V and Ti, preferably satisfies the relationship [Zr + Mn + Cr + V + Ti] ⁇ 0.10 mass%. If the amount added exceeds the specified range, recrystallization will be suppressed and a non-recrystallized structure may be formed, and grain growth may occur. Therefore, even if all are added, the content is preferably 0.10% by mass or less, more preferably 0.09% by mass or less, and still more preferably 0.08% by mass or less. More preferably, it is 0.07 mass% or less, Most preferably, it is 0.05 mass% or less.
  • the crystal structure is preferably a recrystallized structure having a uniform crystal grain size.
  • the alloy components, casting HO conditions, and extrusion conditions are controlled.
  • the form of the crystal structure can be confirmed by a method of coating with a borohydrofluoric acid aqueous solution and observing with a polarizing microscope.
  • the aluminum alloy extruded material according to this embodiment is excellent in anodized film property and is preferably used as a housing material for electronic equipment.
  • the method for producing an aluminum alloy extruded material according to another embodiment of the present invention is an aluminum alloy extruded material, which is Zn: 4.0% by mass to 7.5% by mass, Mg: 1.0% by mass to 2%. 0.2 mass% or less, Fe: 0.05 mass% or more and 0.20 mass% or less, Cu: 0.30 mass% or less, Ti: 0.005 mass% or more and 0.04 mass% or less, B: 0.001 % By mass or more and 0.02% by mass or less, Si: 0.15% by mass or less, Zr: 0.05% by mass or less, Mn: 0.05% by mass or less, Cr: 0.05% by mass or less, V: 0.00%.
  • [Zr + Mn + Cr + V + Ti] which is a total of the contents of Zr, Mn, Cr, V and Ti, [Zr + Mn + Cr + V + Ti] ⁇ 0.10 mass% Except for the range where the Zn content is 6.0 mass% or less and the Mg content is 1.2 mass% or less, the balance is made of aluminum and inevitable impurities, and the metal structure is a recrystallized structure.
  • a method for producing an aluminum alloy extruded material having an anodized film The casting material is processed at a holding condition of homogenization treatment at 400 to 560 ° C.
  • the aging treatment step is characterized by treating at 100 to 180 ° C. for 1 to 30 hours.
  • a molten aluminum alloy having the above alloy composition is prepared, and a known molten metal treatment such as degassing treatment, degassing treatment, and filtering is performed. Then, a cylindrical ingot (billet) is obtained by a DC casting method or the like.
  • a micronizing agent made of an Al-Ti-B alloy into the molten metal.
  • the finer added to the molten metal is preferably such that Ti and B do not exceed the above ranges in the alloy composition.
  • the molten metal is preferably poured into the mold uniformly so that the casting temperature is uniform in the mold.
  • HOT TOP (hot top) casting or the like is preferably used.
  • the billet diameter is small, preferably 14 inches or less.
  • the diameter of the billet is large, cooling of the billet center portion is slowed, and the structure of the billet center portion tends to be coarse. If the cast structure is coarse, it is difficult not only to eliminate concentration segregation during the homogenization process, but also to make the crystal structure finer in the extrusion process.
  • the billet obtained in the casting process is subjected to a homogenization process (HO process).
  • HO process homogenization process
  • the homogenization temperature is preferably 400 to 560 ° C. for 1 hour to 24 hours. If the condition of the homogenization treatment is within this range, the homogenization is sufficiently performed.
  • the homogenization temperature for 24 hours exceeds 560 ° C., the ingot crystal grows, the extrudability is lowered, the crystal grains of the extruded material are coarsened, and the recrystallized structure is locally coarsened, The difference in the grain size of the recrystallized structure becomes large, and a pattern is generated during the anodic oxide coating.
  • the homogenization temperature is more preferably 540 ° C. or lower. Even if the homogenization treatment is performed for more than 24 hours, no further effect can be expected and only the production cost is required.
  • homogenization is preferably performed at 470 ° C. or higher, and more preferably at 500 ° C.
  • the cooling rate after the homogenization treatment is low, the solid solution element is likely to be precipitated. Therefore, it is preferable to cool at an average cooling rate from the HO temperature to 150 ° C. at 100 ° C./h or more.
  • the billet that has been subjected to the homogenization treatment is extruded to obtain a predetermined processed material.
  • the extrusion ratio in the extrusion process is preferably 20 or more.
  • the extrusion ratio in the extrusion process is more preferably 40 or more. This is because the extension of the crystal causes a gradual change in concentration (concentration segregation is likely to be improved if the interval between high-concentration parts or low-concentration parts is close), and the appearance after the anodized film is a streak pattern. It is because it becomes difficult to generate
  • the formation of streaks due to the difference in crystal structure can be suppressed by setting the average grain size to 200 ⁇ m or less and the maximum crystal grain size to 1 mm or less. Since the crystal size of the extruded material becomes finer as the billet temperature is extruded at a lower temperature, the billet temperature is desirably set in consideration of the extrusion pressure and the shape material temperature, and is preferably 480 ° C. or less.
  • the extrusion conditions (billet temperature, die temperature, container temperature, extrusion pressure, extrusion speed, etc.) such that the temperature at the die outlet is 400 ° C. or higher. If the temperature of the extruded material at the die outlet is low, high strength may not be obtained.
  • the extruded material after coming out of the die is cooled so that the cooling rate in the temperature range of up to 200 ° C. after the extrusion is 0.3 to 20 ° C./s. If the cooling rate satisfies this condition, high strength can be obtained and good stress corrosion cracking resistance can be obtained.
  • Aging treatment is performed on the extruded material.
  • the holding temperature in the aging treatment step is 1 to 30 hours under the condition of 100 to 180 ° C.
  • the aging treatment may be performed in two stages in order to obtain higher strength and stress corrosion cracking resistance.
  • An extruded material obtained by sequentially passing through a casting process, a homogenization process, an extrusion process, and an aging process is cut into a predetermined shape and then anodized.
  • the anodized film treatment is performed under known conditions.
  • the homogenization treatment step is performed at a holding temperature of 400 ° C. to 560 ° C.
  • the extrusion step is performed at an extrusion ratio of 20 or more. It is characterized in that the outlet temperature is 420 ° C. or higher, the cooling rate between after extrusion and 200 ° C. is 0.3 to 20 ° C./s, and the aging treatment step is performed under the condition of holding temperature 100 ° C. to 180 ° C.
  • a method for producing an aluminum alloy extruded material having an anodic oxide coating is provided.
  • Billets having the components of Experimental Examples A to N shown in [Table 1] below were obtained.
  • the diameter of the billet was 325 mm.
  • These billets were subjected to HO treatment under the conditions of [Table 2] and then extruded under the conditions of [Table 2].
  • Extrusion was performed under the condition of a billet temperature of 400 ° C., (a) was a flat bar with a width of 100 mm and a thickness of 10 mm, and (b) was performed with two extruded shapes, a flat bar with a width of 120 mm and a thickness of 25 mm.
  • heat treatment was performed under the conditions described in Table 2. After the heat treatment, tempering was performed under the conditions of A to J and L to N for T5 (after extrusion, artificial aging) and K for T6 (after solution treatment, artificial aging).
  • the crystal grain size after casting and after HO was measured by the cross line method, and those having crystal grains with a size exceeding 1 mm were marked as x.
  • the intersecting line method means that a straight line is drawn in an arbitrary direction from an image taken with an optical microscope, and the number of crystal grain boundaries intersecting with the straight line is n, and the length of the straight line is divided by (n-1). Thus, the average crystal grain size is calculated.
  • the surface of the aluminum alloy test material was chamfered (buffed) in an amount corresponding to 20% of the wall thickness, and the anodized film treatment was performed on the chamfered surface.
  • the treatment conditions for the anodized film treatment were 1.5 A / dm 2 in a 15% sulfuric acid aqueous solution at 20 ° C., and the film thickness was about 5 ⁇ m.
  • the color tone was judged based on the fact that the gloss retention before and after the treatment was 40% or more, and the L value was 78 or more and the b value was 1 or less. Those satisfying the above values were marked with ⁇ , and those not satisfying were marked with x. In addition, the presence or absence of streak patterns was evaluated. In “ ⁇ ”, a streak pattern hardly occurred, and in “ ⁇ ”, a thin streak pattern was observed in a limited part. In “X”, a dark streak pattern was generated. The color tone is based on the value of JIS Z8730.
  • the surface of the aluminum alloy test material was chamfered in an amount corresponding to 20% of the wall thickness, and the mirror surface was polished and coated with a borohydrofluoric acid aqueous solution.
  • the structure was observed with a polarizing microscope to determine the structure.
  • the observation surface is an L-LT surface (a wide surface among the surfaces parallel to the extrusion direction).
  • a to G and L to N were equiaxed crystals in which recrystallized structures were observed, and the aspect ratio (average crystal diameter in the extrusion length direction / average crystal diameter in the direction perpendicular to the extrusion) was 2 or less.
  • the aspect ratio average crystal diameter in the extrusion length direction / average crystal diameter in the direction perpendicular to the extrusion
  • HK it was a fiber-like crystal structure.
  • a to E and G, M, and N in which recrystallized structures were observed had uniform fine crystals with an average grain size of 200 ⁇ m or less measured by the intersection method. Coarse crystal grains exceeding 1 mm were present. Crystal growth is confirmed in the ingot structure after F and L HO, and this is the effect.
  • the surface of the aluminum alloy test material was chamfered in an amount corresponding to 20% of the wall thickness, and after polishing to a mirror surface, the area occupied by the crystallized material was measured with an image analyzer and an optical microscope.
  • the observation surface is an L-LT surface (a wide surface among the surfaces parallel to the extrusion direction).
  • Stress corrosion cracking test Only A to E, M, and N were subjected to stress corrosion cracking tests in accordance with JIS H8711.
  • a stress corresponding to 50% of 0.2% proof stress was applied in the direction perpendicular to the extrusion direction.
  • the corrosive solution was immersed in 3.5% NaCl at 25 ° C. for 10 minutes and then dried for 50 minutes for one cycle.
  • the test was conducted for 30 days, and the material without cracks was set as a pass “ ⁇ ”. A, M, and N are inferior in the results of the SCC test, which is thought to be due to the low Cu content.
  • FIG. 2 shows the microstructure of Experimental Example B (Inventive Example). It can be seen that the crystallized substance is diffused and no extreme continuity of the compound is observed.
  • 3 (a) and 3 (b) are obtained by observing the crystal structure of the sample cross section of Experimental Example L (Comparative Example) with a polarizing microscope. It can be seen that the size of the crystal grains varies depending on the observation location, and partially coarse crystal grains are formed. This is because the recrystallized structure is locally coarsened depending on the temperature condition of the HO treatment.
  • FIG. 4 is an observation of the crystal structure of Experimental Example H (Comparative Example). It can be seen that the crystal structure is a fiber structure.
  • FIG. 5 is an observation of the microstructure of Experimental Example K (Comparative Example). The content of Fe, Cu, Mg and Cr is large, and the portion where the crystallized material segregates is stretched by extrusion processing, and the continuity of the compound can be seen in a streak shape.
  • FIG. 6 is a graph showing a Zn concentration analysis and mapping diagram of Experimental Example B (Inventive Example). Zn concentration segregation in a width of 3 mm is 1.0% by mass or less.
  • FIG. 7 is a graph showing the Zn concentration distribution of Experimental Example G (Comparative Example), and FIG. 8 is a graph showing the Zn concentration distribution and mapping diagram of Experimental Example H (Comparative Example).
  • Experimental Examples G and H which are comparative examples, have locations where concentration segregation in which the Zn concentration exceeds 1.0 mass% occurs within a width of 3 mm. Further, it can be seen from the mapping diagram that the concentration segregation is layered.
  • an aluminum alloy extruded material that satisfies these conditions can be preferably used for a housing of an electronic device such as a portable personal computer, a mobile phone, and a smartphone.
  • the extrusion ratio of A to D, M, and N is larger than that of E, that is, the degree of processing is high, so that the surface uniformity is higher.
  • G has a lack of Ti and B which are crystal refining agents during casting, and the ingot structure after casting becomes coarse.
  • concentration segregation of Zn is not sufficiently eliminated, and concentration segregation occurs in which the Zn concentration difference exceeds 1% in the range of more than 0.1 mm and 3 mm or less. Streaks occurred after the oxide film treatment.
  • the Zr addition amount exceeds the upper limit, and the diffusion of Zn is inhibited by Zr because the crystal structure of the extruded material is maintained in the fiber structure due to the pinning effect, and even when homogenization is performed. Zn concentration segregation was not sufficiently eliminated, and streaks were generated after the anodic oxide film treatment of the extruded material. Furthermore, although I has a high Zn content, the mechanical strength is low even in a fiber structure because the Mg content is low.
  • J also has a Zr addition amount, a Cr addition amount, and a Mn addition amount exceeding the upper limit values, and the diffusion of Zn is inhibited by the fact that the crystal structure of the extruded material is maintained in the fiber structure due to the pinning effect, and Zr is homogeneous. Zn concentration segregation is not sufficiently eliminated even when the oxidization treatment is performed, and concentration segregation in which the Zn concentration difference exceeds 1% occurs in the range of more than 0.1 mm and 3 mm or less. There has occurred.
  • J has a high Mg content
  • the mechanical strength is low even in a fiber structure because the Zn content is low.
  • the Mn content is large, the crystal structure of the extruded material is maintained in the fiber structure due to the pinning effect, and the diffusion of Zn is inhibited by Mn. Even if homogenization is performed, the Zn concentration is sufficiently segregated. However, concentration segregation in which the Zn concentration difference exceeded 1% occurred in a range exceeding 0.1 mm and 3 mm or less, and streaks were generated after the anodic oxide film treatment of the extruded material.
  • the HO temperature exceeded the upper limit temperature, and the crystal structure of the ingot grew.
  • some crystal grains exceeding 1 mm were generated, and the crystal grain size of the extruded material was uneven.
  • streaks were generated after the anodized film treatment.

Abstract

L'objectif de la présente invention est de fournir un matériau extrudé en alliage d'aluminium série 7000 ayant une résistance souhaitée et étant peu susceptible de présenter un motif de stries formé sur la surface d'un film d'oxyde d'électrode positive. La présente invention concerne : un matériau extrudé en alliage d'aluminium présentant un très bon aspect extérieur et ayant un film d'oxyde d'électrode positive ayant une composition métallique qui est une composition recristallisée ; et un procédé de production associé. Le matériau extrudé en alliage d'aluminium contient de 4,0 % à 7,5 % en masse de Zn, de 1,0 % à 2,2 % en masse de Mg, de 0,05 % à 0,20 % en masse de Fe, pas plus de 0,30 % en masse de Cu, de 0,005 % à 0,04 % en masse de Ti, de 0,001 % à 0,02 % en masse de B, pas plus de 0,15 % en masse de Si, pas plus de 0,05 % en masse de Zr, pas plus de 0,05 % en masse de Mn, pas plus de 0,05 % en masse de C, et pas plus de 0,05 % en masse de V. La teneur totale en Zr, Mn, Cr, V et Ti, exprimée par [Zr + Mn + Cr + V + Ti] satisfait à la relation [Zr + Mn + Cr + V + Ti] ≤ 0,10 % en masse. Le reste comprend de l'aluminium et les impuretés inévitables, excepté lorsque la teneur en Zn n'excède pas 6,0 % en masse et que la teneur en Mg n'excède pas 1,2 % en masse.
PCT/JP2016/069211 2015-07-08 2016-06-29 Matériau extrudé en alliage d'aluminium pourvu d'un film d'oxyde d'électrode positive, ayant un très bon aspect extérieur, et son procédé de production WO2017006816A1 (fr)

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KR1020187003476A KR20180025955A (ko) 2015-07-08 2016-06-29 양극 산화피막을 갖는 외관 품질이 우수한 알루미늄 합금 압출재 및 그 제조 방법
CN201680040087.2A CN107735503A (zh) 2015-07-08 2016-06-29 具有阳极氧化皮膜的外观品质优良的铝合金挤出材料及其制造方法
JP2016567441A JP6119937B1 (ja) 2015-07-08 2016-06-29 陽極酸化皮膜を有する外観品質に優れたアルミニウム合金押出材及びその製造方法

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PCT/JP2015/072920 WO2017006490A1 (fr) 2015-07-08 2015-08-13 Matériau extrudé en alliage d'aluminium comportant un film d'oxyde d'électrode positive et ayant une excellente qualité d'apparence externe et son procédé de production
JPPCT/JP2015/072920 2015-08-13

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JP2018090839A (ja) * 2016-11-30 2018-06-14 アイシン軽金属株式会社 押出材用アルミニウム合金及びそれを用いた押出材並びに押出材の製造方法
EP3594369A4 (fr) * 2017-03-07 2020-12-16 LG Electronics Inc. -1- Alliage d'aluminium
CN113403507A (zh) * 2021-06-21 2021-09-17 合肥标兵新材料科技有限公司 电子产品用高强高阳极氧化效果的6系铝合金制备方法

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2018090839A (ja) * 2016-11-30 2018-06-14 アイシン軽金属株式会社 押出材用アルミニウム合金及びそれを用いた押出材並びに押出材の製造方法
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EP3594369A4 (fr) * 2017-03-07 2020-12-16 LG Electronics Inc. -1- Alliage d'aluminium
CN113403507A (zh) * 2021-06-21 2021-09-17 合肥标兵新材料科技有限公司 电子产品用高强高阳极氧化效果的6系铝合金制备方法

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