EP2130931B1 - Procédé de fabrication d'une plaque épaisse d'alliage d'aluminium - Google Patents

Procédé de fabrication d'une plaque épaisse d'alliage d'aluminium Download PDF

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EP2130931B1
EP2130931B1 EP08722912.6A EP08722912A EP2130931B1 EP 2130931 B1 EP2130931 B1 EP 2130931B1 EP 08722912 A EP08722912 A EP 08722912A EP 2130931 B1 EP2130931 B1 EP 2130931B1
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Prior art keywords
aluminum alloy
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mass
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German (de)
English (en)
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EP2130931B2 (fr
EP2130931A4 (fr
EP2130931A1 (fr
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Kazunori Kobayashi
Kenji Tokuda
Tomoharu Kato
Takashi Inaba
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Kobe Steel Ltd
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Kobe Steel Ltd
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Priority claimed from JP2007095423A external-priority patent/JP4231530B2/ja
Priority claimed from JP2007095419A external-priority patent/JP4231529B2/ja
Priority claimed from JP2007098495A external-priority patent/JP4242429B2/ja
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B21/00—Obtaining aluminium
    • C22B21/06—Obtaining aluminium refining
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002—Castings of light metals
    • B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D43/00—Mechanical cleaning, e.g. skimming of molten metals
    • B22D43/001—Retaining slag during pouring molten metal
    • B22D43/004—Retaining slag during pouring molten metal by using filtering means
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B21/00—Obtaining aluminium
    • C22B21/06—Obtaining aluminium refining
    • C22B21/066—Treatment of circulating aluminium, e.g. by filtration
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
    • C22B9/02—Refining by liquating, filtering, centrifuging, distilling, or supersonic wave action including acoustic waves
    • 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
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • 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
    • C22F1/047—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 magnesium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
    • 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

Definitions

  • the present invention relates to methods for manufacturing aluminum alloy thick plates.
  • Aluminum alloy materials such as aluminum alloy thick plates are generally used for various applications including semiconductor-related devices such as base substrates, transport devices, and vacuum chambers; electrical and electronic parts and their manufacturing devices; household articles; and mechanical parts.
  • Such aluminum alloy materials are generally manufactured by melting aluminum alloy ingots, and casting the molten material to give a slab, conducting a heat treatment for homogenization, if necessary, and then rolling the slab to a predetermined thickness (see, for example, Paragraphs 0037 to 0045 of Patent Document 1).
  • Patent Document 1 Japanese Unexamined Patent Application Publication ( JP-A) No. 2005-344173
  • EP-A-2 034 035 discloses a method for manufacturing an aluminum alloy thick plate, the method comprising: a melting step for melting an aluminum alloy; a hydrogen gas removal step for removing hydrogen gas from the aluminum alloy melted in the melting step; a filtration step for removing mediators from the aluminum alloy from which hydrogen gas is removed in the hydrogen gas removal step; a casting step for casting the aluminum alloy from which the mediator is removed in the filtration step to produce a slab; and a slicing step for slicing the slab into a predetermined thickness, which are carried out in the order stated (cf. claim 1).
  • the present invention has been made and an object thereof is to provide a method for manufacturing an aluminum alloy thick plate, which method enables improved accuracy of plate thickness with high productivity and good controllability of surface condition and flatness.
  • an aluminum alloy thick plate which is manufactured by the procedures of the manufacturing method excels in surface condition, flatness, and accuracy of plate thickness.
  • a method for manufacturing an aluminum alloy thick plate from an aluminum alloy the aluminum alloy containing Mg in a content of 1.5 percent by mass or more and 12.0 percent by mass or less, and further containing at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 0.6 percent by mass or less, Mn in a content of 1.0 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a slicing step of slicing the slab into an aluminum alloy thick plate having a predetermined thickness; and a heat treatment step of thermally treating the aluminum alloy thick plate having a predetermined thickness by holding the same at a temperature of 400°C or higher but lower than its melting point for one hour or longer.
  • a method for manufacturing an aluminum alloy thick plate from an aluminum alloy the aluminum alloy containing Mn in a content of 0.3 percent by mass or more and 1.6 percent by mass or less, and further containing at least one member selected from the group consisting of Si in a.content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 0.5 percent by mass or less, Mg in a content of 1.5 percent by mass or less, Cr in a content of 0.3 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a slicing step of slicing the slab into an aluminum alloy thick plate having a predetermined thickness; and a heat treatment step of thermally treating the aluminum alloy thick plate having a predetermined thickness by holding the same at a temperature of 400°C or higher but lower than its melting point for one hour or longer.
  • a method for manufacturing an aluminum alloy thick plate from an aluminum alloy the aluminum alloy containing Si in a content of 0.2 percent by mass or more and 1.6 percent by mass or less and Mg in a content of 0.3 percent by mass or more and 1.5 percent by mass or less, and further containing at least one member selected from the group consisting of Fe in a content of 0.8 percent by mass or less, Cu in a content of 1.0 percent by mass or less, Mn in a content of 0.6 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a slicing step of slicing the slab into an aluminum alloy thick plate having a predetermined thickness; and a heat treatment step of thermally treating the aluminum alloy thick plate having a predetermined thickness by holding the same at a temperature of 400°C or higher but lower than its melting point for one hour or longer.
  • a method for manufacturing an aluminum alloy thick plate from an aluminum alloy the aluminum alloy containing Mg in a content of 0.4 percent by mass or more and 4.0 percent by mass or less and Zn in a content of 3.0 percent by mass or more and 9.0 percent by mass or less, and further containing at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 3.0 percent by mass or less, Mn in a content of 0.8 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.25 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a slicing step of slicing the slab into an aluminum alloy thick plate having a predetermined thickness; and a heat treatment step of thermally treating the aluminum alloy thick plate having a predetermined thickness by holding the same at a temperature of 350°C or higher but lower than its melting point for one hour or longer.
  • a method for manufacturing an aluminum alloy thick plate from an aluminum alloy the aluminum alloy containing Mg in a content of 1.5 percent by mass or more and 12.0 percent by mass or less, and further containing at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 0.6 percent by mass or less, Mn in a content of 1.0 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminium alloy, from which inclusions have been removed, into a slab; a heat treatment step of thermally treating the slab by holding the same at a temperature of 200°C to 350°C for one hour or longer; and a slicing step of slicing the thermally treated slab into an aluminum alloy thick plate having a predetermined thickness.
  • a method for manufacturing an aluminum alloy thick plate from an aluminum alloy the aluminum alloy containing Mn in a content of 0.3 percent by mass or more and 1.6 percent by mass or less, and further containing at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 0.5 percent by mass or less, Mg in a content of 1.5 percent by mass or less, Cr in a content of 0.3 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a heat treatment step of thermally treating the slab by holding the same at a temperature of 200°C to 350°C for one hour or longer; and a slicing step of slicing the thermally treated slab into an aluminum alloy thick plate having a predetermined thickness.
  • a method for manufacturing an aluminum alloy thick plate from an aluminum alloy the aluminum alloy containing Si in a content of 0.2 percent by mass or more and 1.6 percent by mass or less and Mg in a content of 0.3 percent by mass or more and 1.5 percent by mass or less, and further containing at least one member selected from the group consisting of Fe in a content of 0.8 percent by mass or less, Cu in a content of 1.0 percent by mass or less, Mn in a content of 0.6 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a heat treatment step of thermally treating the slab by holding the same at a temperature of 200°C or higher but lower than 400°C for one hour or longer; and a slicing step of slicing the thermally treated slab into an aluminum alloy thick plate having a predetermined thickness.
  • an aluminum alloy thick plate from an aluminum alloy, the aluminum alloy containing Mg in a content of 0.4 percent by mass or more and 4.0 percent by mass or less and Zn in a content of 3.0 percent by mass or more and 9.0 percent by mass or less, and further containing at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 3.0 percent by mass or less, Mn in a content of 0.8 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.25 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a heat treatment step of thermally treating the slab by holding the same at a temperature of 200°C or higher but lower than 350°C for one hour or longer; and a slicing step of slicing the thermally treated slab into an aluminum alloy thick plate having a predetermined thickness.
  • a method for manufacturing an aluminum alloy thick plate from an aluminum alloy the aluminum alloy containing Mg in a content of 1.5 percent by mass or more and 12.0 percent by mass or less, and further containing at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 0.6 percent by mass or less, Mn in a content of 1.0 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a slicing step of slicing the slab into an aluminum alloy thick plate having a predetermined thickness; and a heat treatment step of thermally treating the aluminum alloy thick plate having a predetermined thickness by holding the same at a temperature of 200°C or higher but lower than 400°C for one hour or longer.
  • a method for manufacturing an aluminum alloy thick plate from an aluminum alloy the aluminum alloy containing Mn in a content of 0.3 percent by mass or more and 1.6 percent by mass or less, and further containing at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 0.5 percent by mass or less, Mg in a content of 1.5 percent by mass or less, Cr in a content of 0.3 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a slicing step of slicing the slab into an aluminum alloy thick plate having a predetermined thickness; and a heat treatment step of thermally treating the aluminum alloy thick plate having a predetermined thickness by holding the same at a temperature of 200°C or higher but lower than 400°C for one hour or longer.
  • an eleventh embodiment of the present invention there is provided a method for manufacturing an aluminum alloy thick plate from an aluminum alloy, the aluminum alloy containing Si in a content of 0.2 percent by mass or more and 1.6 percent by mass or less and Mg in a content of 0.3 percent by mass or more and 1.5 percent by mass or less, and further containing at least one member selected from the group consisting of Fe in a content of 0.8 percent by mass or less, Cu in a content of 1.0 percent by mass or less, Mn in a content of 0.6 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a slicing step of slicing the slab into an aluminum alloy thick plate having a predetermined thickness; and a heat treatment step of thermally treating the aluminum alloy thick plate having a predetermined thickness by holding the same at a temperature of 200°C or higher but lower than 400°C for one hour or longer.
  • a method for manufacturing an aluminum alloy thick plate from an aluminum alloy the aluminum alloy containing Mg in a content of 0.4 percent by mass or more and 4.0 percent by mass or less and Zn in a content of 3.0 percent by mass or more and 9.0 percent by mass or less, and further containing at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 3.0 percent by mass or less, Mn in a content of 0.8 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.25 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • the method includes in the following order: a melting step of melting the aluminum alloy; a hydrogen gas removal step of removing hydrogen gas from the molten aluminum alloy; a filtration step of filtering the aluminum alloy, from which hydrogen gas has been removed, to remove inclusions from the aluminum alloy; a casting step of casting the aluminum alloy, from which inclusions have been removed, into a slab; a slicing step of slicing the slab into an aluminum alloy thick plate having a predetermined thickness; and a heat treatment step of thermally treating the aluminum alloy thick plate having a predetermined thickness by holding the same at a temperature of 200°C or higher but lower than 350°C for one hour or longer.
  • an aluminum alloy thick plate which is manufactured by the method for manufacturing an aluminum alloy thick plate, according to any one of the first to twelfth embodiments of the present invention, and includes crystal grains having an average grain size of 400 ⁇ m or less.
  • the resulting aluminum alloy thick plate includes finer intermetallic compounds and has improved strength, because the material aluminum alloy has contents of predetermined elements controlled within predetermined ranges.
  • the hydrogen gas removal step removes hydrogen to thereby control the concentration of hydrogen in the slab. Therefore, even if crystal grains in the slab become coarse, hydrogen is not accumulated or enriched at the grain boundary near the surface of the slab. This suppresses blistering of the slab and peeling of the aluminum alloy thick plate resulting from the blistering, and also suppresses potential defects on the surface of the thick plates which appear as surface defects of the thick plate.
  • the aluminum alloy thick plate has improved strength.
  • the filtration step removes inclusions such as oxides and non-metals from the aluminum alloy.
  • Slicing the slab in the slicing step reduces the thickness of the oxide film; improves the surface condition, flatness and accuracy of the plate thickness of the aluminum alloy thick plate; and also improves its productivity.
  • the heat treatment step thermally treats the aluminum alloy thick plate to thereby remove the internal stress of the aluminum alloy and uniformize its inner structure.
  • the aluminum alloy thick plate can have improved strength.
  • the aluminum alloy thick plate is manufactured by slicing a slab, and this eliminates necessity to reduce its thickness by hot rolling unlike in known aluminum alloy thick plates. This simplifies operation steps and thereby improves the productivity. This also eliminates unevenness (uneven color) of the surface and cross section of the thick plate; and improves the flatness, surface condition after anodization, and accuracy of plate thickness.
  • the internal stress of the aluminum alloy thick plate can be removed and its inner structure can be uniformized.
  • the aluminum alloy thick plate can have good flatness and satisfactory accuracy of plate thickness and can maintain its satisfactory strength.
  • the configuration (A) helps to further improve the surface condition and flatness of the aluminum alloy thick plate and eliminates the gas accumulation of the surface of the thick plate, because the surface is further smoothened.
  • the resulting aluminum alloy thick plate if used as a vacuum chamber, can provide an improved degree of vacuum.
  • the configuration (B) helps to provide an aluminum alloy thick plate excellent in appearance quality even after anodization, because the central portion of the slab is removed, which central portion will often cause unevenness in the surface and cross section of the aluminum alloy thick plate after anodization. This configuration also helps to reduce the within-lot variation.
  • the aluminum alloy thick plate can include finer intermetallic compounds and have higher strength, because the material aluminum alloy has contents of predetermined elements controlled within predetermined ranges.
  • the hydrogen gas removal step removes hydrogen gas to thereby control the concentration of hydrogen in the slab. Therefore, even if crystal grains in the slab become coarse, hydrogen is not accumulated or enriched at the grain boundary near the surface of the slab. This suppresses blistering of the slab and peeling of the aluminum alloy thick plate resulting from the blistering; suppresses potential defects on the surface of the thick plates which appear as surface defects of the thick plate; and improves the strength of the aluminum alloy thick plate.
  • the filtration step removes inclusions such as oxides and non-metals from the aluminum alloy.
  • the heat treatment step thermally treats the slab to eliminate the internal stress and to uniformize the inner structure thereof.
  • the slicing step slices the slab so as to reduce the thickness of the oxide film and to improve the surface condition, flatness and accuracy of the plate thickness of the aluminum alloy thick plate, as well as its productivity.
  • the aluminum alloy thick plate can have improved balance among its flatness, strength, and cutting property.
  • the heat treatment at a temperature of 200°C to 350°C (fifth and sixth embodiment), 200°C or higher but lower than 400°C (seventh embodiment) (or 350°C (eighth embodiment)) applied to the slab suppresses the increase in ductility. This helps to remove the internal stress and to uniformize the inner structure of the thick plate without adversely affecting the cutting property (chip breakability) .
  • the resulting aluminum alloy thick plate can thereby have good flatness and satisfactory accuracy of plate thickness and can maintain its satisfactory strength.
  • the aluminum alloy thick plate is manufactured by slicing a slab.
  • the configuration (C) helps to further improve the surface condition and flatness of the aluminum alloy thick plate and eliminates the gas accumulation of the surface of the thick plate, because the surface is further smoothened.
  • the resulting aluminum alloy thick plate if used as a vacuum chamber, can provide an improved degree of vacuum.
  • the configuration (D) helps to provide an aluminum alloy thick plate excellent in appearance quality even after anodization, because the central portion of the slab is removed, which central portion will often cause unevenness in the surface and cross section of the aluminum alloy thick plate after anodization. This configuration also helps to reduce the within-lot variation.
  • the aluminum alloy thick plate includes finer intermetallic compounds and has improved strength, because the material aluminum alloy has contents of predetermined elements controlled within predetermined ranges.
  • the hydrogen gas removal step removes hydrogen to thereby control the concentration of hydrogen in the slab. Therefore, even if crystal grains in the slab become coarse, hydrogen is not accumulated or enriched at the grain boundary near the surface of the slab. This suppresses blistering of the slab and peeling of the aluminum alloy thick plate resulting from the blistering; suppresses potential defects on the surface of the thick plates which appear as surface defects of the thick plate; and improves the strength of the aluminum alloy thick plate.
  • the filtering step removes inclusions such as oxides and non-metals from the aluminum alloy.
  • Slicing the slab in the slicing step reduces the thickness of the oxide film; improves the surface condition, flatness and accuracy of the plate thickness of the aluminum alloy thick plate; and improves the productivity of the aluminum alloy thick plate.
  • the heat treatment step thermally treats the aluminum alloy thick plate to thereby remove the internal stress of the aluminum alloy and uniformize its inner structure.
  • the aluminum alloy thick plate can have improved strength.
  • the aluminum alloy thick plate is manufactured by slicing a slab, and this eliminates necessity to reduce its thickness by hot rolling unlike in known aluminum alloy thick plates. This simplifies operation steps; improves the productivity; eliminates unevenness (uneven color) of the surface and cross section of the thick plate; and improves the flatness, quality of appearance after anodization, and accuracy of plate thickness . Further, this also improves the balance among the flatness, strength, and cutting property of the aluminum alloy thick plate.
  • the heat treatment at a temperature of 200°C or higher but lower than 400°C (or 350°C) applied to the sliced aluminum alloy thick plate having a predetermined thickness suppresses the increase in ductility, whereby helps to remove the internal stress and uniformize the inner structure of the aluminum alloy thick plate without adversely affecting the cutting property (chip breakability).
  • the resulting aluminum alloy thick plate can thereby have good flatness and satisfactory accuracy of plate thickness and maintain its satisfactory strength.
  • the configuration (E) helps to further improve the surface condition and flatness of the aluminum alloy thick plate and eliminates the gas accumulation of the surface of the thick plate, because the surface is further smoothened.
  • the resulting aluminum alloy thick plate if used as a vacuum chamber, can provide an improved degree of vacuum.
  • the configuration (F) helps to provide an aluminum alloy thick plate excellent in appearance quality even after anodization, because the central portion of the slab is removed, which central portion will often cause unevenness in the surface and cross section of the aluminum alloy thick plate after anodization. This configuration also helps to reduce the within-lot variation.
  • the aluminum alloy thick plates obtained by the methods of the present invention excel in surface condition, flatness, and accuracy of plate thickness. They also have high quality, because their surface is smoothened and thereby is free from gas accumulation. They can be used in a wide variety of applications and can be recycled and used for other applications, because the surface appearance of them after anodization is substantially free from unevenness.
  • the methods for manufacturing an aluminum alloy thick plate each include a melting step (S1), a hydrogen gas removal step (S2), a filtration step (S3), a casting step (S4), a slicing step (S5), and a heat treatment step (S6) in this order.
  • the methods may further include, where necessary, a surface smoothing treatment step (S7) subsequent to the heat treatment step (S6).
  • aluminum alloy ingots are melted in the melting step (S1).
  • hydrogen gas is removed from the molten aluminum alloy in the hydrogen gas removal step (S2), and inclusions such as oxides and non-metals are removed therefrom in the filtration step (S3).
  • the resulting aluminum alloy is cast into a slab in the casting step (S4).
  • the slab is then sliced into an aluminum alloy thick plate having a predetermined thickness in the slicing step (S5).
  • the aluminum alloy thick plate having a predetermined thickness is then subjected to a heat treatment in the heat treatment step (S6) and, where necessary, subjected to a surface smoothing treatment in the surface smoothing treatment step (S7).
  • the manufacturing methods according to the first, second, third, and fourth embodiments of the present invention use a 5000 series Al-Mg alloy, a 3000 series Al-Mn alloy, a 6000 series Al-Mg-Si alloy, and a 7000 series Al-Zn-Mg alloy, respectively, as a raw material aluminum alloy.
  • the details of them are as follows.
  • a 5000 series Al-Mg alloy is used.
  • the aluminum alloy contains Mg in a content of 1.5 percent by mass or more and 12.0 percent by mass or less, and further contains at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 0.6 percent by mass or less, Mn in a content of 1.0 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • Magnesium (Mg) serves to improve the strength of the aluminum alloy. Mg, if its content is less than 1.5 percent by mass, may not exhibit the activity sufficiently. In contrast, Mg, if its content is more than 12.0 percent by mass, may significantly adversely affect the casting ability, and this may impede the manufacture of the product. Accordingly, the Mg content should be 1.5 percent by mass or more and 12.0 percent by mass or less.
  • Si serves to improve the strength of the aluminum alloy.
  • Si is generally contained in the aluminum alloy as an impurity in the ingot and forms an Al- (Fe) - (Mn) -Si intermetallic compound together with Mn and Fe in the slab typically in the casting step (S4).
  • Si if its content is more than 0.7 percent by mass, may cause a coarse intermetallic compound in the slab to thereby often cause unevenness in the surface appearance after anodization. Accordingly, the Si content should be 0.7 percent by mass or less.
  • Fe Iron
  • Fe allows crystal grains of the aluminum alloy to be finer and more stabilized and allows the aluminum alloy to have improved strength.
  • Fe is generally contained in the aluminum alloy as an impurity in the ingot and forms an Al-Fe- (Mn) - (Si) intermetallic compound together with Mn and/or Si in the slab typically in the casting step (S4).
  • Fe if its content is more than 0.8 percent by mass, may cause a coarse intermetallic compound in the slab to thereby often cause unevenness in the surface appearance after anodization . Accordingly, the Fe content should be 0.8 percent by mass or less.
  • Copper (Cu) serves to improve the strength of the aluminum alloy.
  • a Cu content of 0.6 percent by mass is enough to ensure a sufficient strength to be used endurably as a thick plate. Accordingly, the Cu content should be 0.6 percent by mass or less.
  • Manganese (Mn) is solidly dissolved in the aluminum alloy and thereby serves to improve the strength of the aluminum alloy. Mn, if its content is more than 1.0 percent by mass, may cause a coarse intermetallic compound to thereby often cause unevenness in the surface appearance after anodization. Accordingly, the Mn content should be 1.0 percent by mass or less.
  • Chromium (Cr) serves to suppress the grain growth by depositing as a fine compound in the casting step (S4) and heat treatment step (S6).
  • Cr if its content is more than 0.5 percent by mass, may cause a coarse Al-Cr intermetallic compound as a primary crystal to thereby often cause unevenness in the surface appearance after anodization. Accordingly, the Cr content should be 0.5 percent by mass or less.
  • Zinc (Zn) serves to improve the strength of the aluminum alloy.
  • a Zn content of 0.4 percent by mass is enough to ensure a sufficient strength to be used endurably as a thick plate. Accordingly, the Zn content should be 0.4 percent by mass or less.
  • Titanium (Ti) allows the slab to contain finer crystal grains. If the Ti content is more than 0.1 percent by mass, the activity may be saturated. Accordingly, the Ti content should be 0.1 percent by mass or less.
  • Zirconium allows the slab to contain finer crystal grains. If the Zr content is more than 0.3 percent by mass, the activity may be saturated. Accordingly, the Zr content should be 0.3 percent by mass or less.
  • the aluminum alloy contains the above-mentioned components, with the remainder being aluminum and inevitable impurities.
  • Exemplary inevitable impurities include V and B.
  • a 3000 series Al-Mn alloy is used.
  • the aluminum alloy contains Mn in a content of 0.3 percent by mass or more and 1.6 percent by mass or less, and further contains at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 0.5 percent by mass or less, Mg in a content of 1.5 percent by mass or less, Cr in a content of 0.3 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • Manganese (Mn) is solidly dissolved in the aluminum alloy and thereby serves to improve the strength of the aluminum alloy. Mn, if its content is less than 0.3 percent by mass, may not exhibit the activity sufficiently. In contrast, Mn, if its content is more than 1.6 percent by mass, may cause a coarse intermetallic compound, to thereby often cause unevenness in the surface appearance after anodization . Accordingly, the Mn content should be 0.3 percent by mass or more and 1.6 percent by mass or less.
  • Magnesium (Mg) serves to improve the strength of the aluminum alloy.
  • a Mg content of 1.5 percent by mass is enough to ensure a sufficient strength to be used endurably as a thick plate. Accordingly, the Mg content should be 1.5 percent by mass or less.
  • a 6000 series Al-Mg-Si alloy is used.
  • the aluminum alloy contains Si in a content of 0.2 percent by mass or more and 1.6 percent by mass or less and Mg in a content of 0.3 percent by mass or more and 1.5 percent by mass or less, and further contains at least one member selected from the group consisting of Fe in a content of 0.8 percent by mass or less, Cu in a content of 1.0 percent by mass or less, Mn in a content of 0.6 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Zn in a content of 0.4 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.3 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • Si serves to improve the strength of the aluminum alloy.
  • Si is generally contained in the aluminum alloy as an impurity in the ingot and forms an Al-(Fe)-Si intermetallic compound and a Si intermetallic compound in the slab typically in the casting step (S4) .
  • Si if its content is less than 0.2 percent by mass, may not exhibit the activity sufficiently. In contrast, Si, if its content is more than 1.6 percent by mass, may cause a coarse Si intermetallic compound in the slab, to thereby often cause unevenness in the surface appearance after anodization. Accordingly, the Si content should be 0.2 percent by mass or more and 1.6 percent by mass or less.
  • Mg Magnesium (Mg) forms Mg 2 Si in the coexistence with Si to thereby serve to improve the strength of the aluminum alloy. Mg, if its content is less than 0.3 percent by mass, may not exhibit the activity sufficiently. In contrast, if the Mg content is more than 1.5 percent by mass, the activity may be saturated. Accordingly, the Mg content should be 0.3 percent by mass or more and 1.5 percent by mass or less.
  • Copper (Cu) serves to improve the strength of the aluminum alloy.
  • Cu if its content is more than 1.0 percent by mass, may impair the corrosion resistance. Accordingly, the Cu content should be 1.0 percent by mass or less.
  • Zn serves to improve-the strength of the aluminum alloy. Zn, if its content is more than 0.4 percent by mass, may impair the corrosion resistance. Accordingly, the Zn content should be 0.4 percent by mass or less.
  • a 7000 series Al-Zn-Mg alloy is used.
  • the aluminum alloy contains Mg in a content of 0.4 percent by mass or more and 4.0 percent by mass or less and Zn in a content of 3.0 percent by mass or more and 9.0 percent by mass or less, and further contains at least one member selected from the group consisting of Si in a content of 0.7 percent by mass or less, Fe in a content of 0.8 percent by mass or less, Cu in a content of 3.0 percent by mass or less, Mn in a content of 0.8 percent by mass or less, Cr in a content of 0.5 percent by mass or less, Ti in a content of 0.1 percent by mass or less, and Zr in a content of 0.25 percent by mass or less, with the remainder being aluminum and inevitable impurities.
  • Magnesium (Mg) serves to improve the strength of the aluminum alloy. Mg, if its content is less than 0.4 percent by mass, may not exhibit the activity sufficiently. In contrast, Mg, if its content is more than 4.0 percent by mass, may often cause unevenness in the surface appearance after anodization. Accordingly, the Mg content should be 0.4 percent by mass or more and 4.0 percent by mass or less.
  • Zinc (Zn) serves to improve the strength of the aluminum alloy. Zn, if its content is less than 3.0 percent by mass, may not exhibit the activity sufficiently. In contrast, Zn, if its content is more than 9.0 percent by mass, may often cause unevenness in the surface appearance after anodization. Accordingly, the Zn content should be 3.0 percent by mass or more and 9.0 percent by mass or less.
  • Silicon (Si) is generally contained in the aluminum alloy as an impurity in the ingot and forms an Al-(Fe)-Si intermetallic compound in the slab typically in the casting step (S4).
  • Si if its content is more than 0.7 percent by mass, may cause a coarse Al-(Fe)-Si intermetallic compound in the slab, to thereby often cause unevenness in the surface appearance after anodization. Accordingly, the Si content should be 0.7 percent by mass or less.
  • Iron (Fe) is generally contained in the aluminum alloy as an impurity in the ingot and forms an Al-Fe intermetallic compound in the slab typically in the casting step (S4).
  • Fe if its content is more than 0.8 percent by mass, may cause a coarse Al-Fe intermetallic compound in the slab, to thereby often cause unevenness in the surface appearance after anodization. Accordingly, the Fe content should be 0.8 percent by mass or less.
  • Copper (Cu) serves to improve the strength of the aluminum alloy.
  • Cu if its content is more than 3.0 percent by mass, may impair the corrosion resistance. Accordingly, the Cu content should be 3.0 percent by mass or less.
  • Manganese (Mn) allows the crystal structure to be finer. Mn, if its content is more than 0.8 percent by mass, may cause a coarse intermetallic compound, to thereby often cause unevenness in the surface appearance after anodization. Accordingly, the Mn content should be 0.8 percent by mass or less.
  • the melting step (S1) is a step of melting the raw material aluminum alloy.
  • the hydrogen gas removal step (S2) is a step of removing hydrogen gas from the aluminum alloy which has been melted in the melting step (S1).
  • Hydrogen gas is generated typically from hydrogen in a fuel and from water and organic substances attached typically to the ingot. Hydrogen gas, if contained in a large content, will cause the following disadvantages.
  • the amount of hydrogen gas is preferably 0.2 ml or less and more preferably 0.1 ml or less per 100 g of the aluminum alloy.
  • Removal of hydrogen gas can be suitably carried out by subjecting a molten metal typically to a fluxing process, chlorine refining, or in-line refining, and it can be more suitably carried out by using a SNIF (spinning nozzle inert flotation) system and a porous plug (see JP-ANo. 2002-146447 ) in a hydrogen gas removing apparatus.
  • SNIF spininning nozzle inert flotation
  • the concentration of hydrogen gas in a slab can be determined typically in the following manner. Specifically, a sample is cut out from the slab after the casting step; then subjected to ultrasonic cleaning with alcohol and acetone; and thereafter analyzed typically according to the inert gas fusion thermal conductivity method (LIS A06-1993).
  • the concentration of hydrogen gas in an aluminum alloy thick plate can be determined typically in the following manner. Specifically, a sample is cut out from the aluminum alloy thick plate. Next, the sample is immersed in an aqueous NaOH solution; then treated with nitric acid to remove an oxide film on the surface of the sample; and the treated sample is subjected to ultrasonic cleaning with alcohol and acetone and then analyzed according typically to the vacuum heat extraction capacitance method (LIS A06-1993).
  • the filtration step (S3) is a step of removing mainly oxide and non-metal inclusions from the aluminum alloy with a filtrating device.
  • the filtrating device is provided typically with a ceramic tube with alumina particles of about 1 mm. The inclusions are removed by allowing a molten metal to pass through the ceramic tube.
  • the hydrogen gas removal step and the filtration step ensure high quality of the aluminum alloy, and the resulting aluminum alloy is made into a high-quality slab in the subsequent casting step (S4). These steps can suppress the generation of deposits of oxides (dross), and this reduces the effort and time for removing the dross.
  • the casting step (S4) is a step of producing a slab by forming a molten metal of the aluminum alloy typically with a casting apparatus into a predetermined shape such as a rectangular parallelepiped and solidifying the metal.
  • a casting apparatus equipped with a water-cooled mold is used.
  • a semi-continuous casting process may be employed as the casting process.
  • a molten metal of the aluminum alloy is injected from above into a water-cooled metallic mold having an open bottom, and the solidified aluminum alloy is successively withdrawn from the bottom of the water-cooled mold to give slabs having predetermined thickness.
  • the semi-continuous casting process may be carried out vertically or horizontally.
  • the slicing step (S5) is a step of producing an aluminum alloy thick plate having a predetermined thickness by slicing the slab produced in the casting step (S4).
  • the slab slicing process may be employed as a slicing process.
  • the slab slicing process is a process for cutting out the slab in the cast direction by slicing the slab produced by the semi-continuous casting process typically with a band saw cutting apparatus, to give an aluminum alloy thick plate having a predetermined thickness .
  • the thickness of the aluminum alloy thick plate is preferably 15 to 200 mm, but it is not particularly limited, and can be varied suitably depending on the intended use of the aluminum alloy thick plate .
  • a band saw is preferably used in the slicing process, but it is not particularly limited, and cutting may be also performed typically with a circular saw cutting apparatus, or by laser or water pressure.
  • Slicing the slab gives an aluminum alloy thick plate superior typically in surface condition, flatness, and accuracy of the plate thickness to a rolled product.
  • a thick plate having a flatness (amount of warpage) per 1 m in the casting direction of 0.4 mm or less per 1 m length in the evaluation of flatness, and the accuracy of the plate thickness of ⁇ 100 ⁇ m or less.
  • a central portion B shaded with slanted lines is preferably removed in the slicing step (S5).
  • the central portion B has two substantially identical thicknesses in a thickness direction from the center of the thickness direction A to the both surfaces of the central portion, respectively, and has a total thickness of from one-thirtieth to one-fifth the thickness T of the slab 1 (T/30 to T/5) .
  • the central portion B in Fig. 2 is illustrated to have a thickness about one-fifth the thickness T.
  • the thicknesses b1 and b2 of the upper and lower portions of the central portion B of the slab 1 are preferably equal to each other, but a difference between them of about 30% is acceptable.
  • the center of the thickness direction A refers to a location which is the center of the slab 1 in the thickness direction and is located about a half the thickness T of the slab 1, i.e., a location of the slab 1 about T/2 deep.
  • the central portion B of the slab 1 is susceptive to unevenness in the surface and cross section of the thick plate after anodization.
  • the central portion B is removed by the slicing step (S5), and a thick plate excellent in quality of appearance after anodization with less within-lot variation can be obtained.
  • Removal of a central portion having a thickness of less than T/30 (one-thirtieth the thickness T) may often cause a thick plate suffering from unevenness in the surface appearance after anodization and often cause a large within-lot variation.
  • T/5 one-fifth the thickness T
  • the central portion B of the slab 1 is preferably removed in such an amount that the central portion has two substantially identical thicknesses in the thickness direction from the center of the thickness direction A to the both surfaces of the central portion, respectively, and has a total thickness of from one-thirtieth to one-fifth the thickness T of the slab 1 (T/30 to T/5).
  • the subsequent heat treatment step (S6) is performed in which a heat treatment is conducted in order to remove the internal stress and to uniformize the inner structure.
  • the heat treatment improves the flatness, accuracy of plate thickness, and quality of appearance after anodization.
  • the heat treatment step (S6) is a step of carrying out a heat treatment (heat treatment for homogenization) on the aluminum alloy thick plate having a predetermined thickness produced in the slicing step (S5).
  • the heat treatment may be carried out according to a common procedure. Specifically, when the aluminum alloy is a 5000 series Al-Mg alloy (the first embodiment of the present invention), a 3000 series Al-Mn alloy (the second embodiment of the present invention), and a 6000 series Al-Mg-Si alloy (the third embodiment of the present invention), the heat treatment is performed by holding the aluminum alloy thick plate at a temperature of 400°C or higher but lower than its melting point for one hour or longer. When the aluminum alloy is a 7000 series Al-Zn-Mg alloy (the fourth embodiment of the present invention), the heat treatment is performed by holding the aluminum alloy thick plate at a temperature of 350°C or higher but lower than its melting point for one hour or longer.
  • the slicing process of the slab obtained in the casting step (S4) allows the internal residual stress to be released, and this often causes warpage.
  • a heat treatment if conducted at a temperature of lower than 400°C, may not sufficiently help to remove the inner stress and to uniformize a solute element, which is segregated during casting, and the heat treatment may therefore not exhibit sufficient advantages.
  • the treatment temperature herein should be 400°C or higher. If a heat treatment is conducted at a temperature equal to or higher than the melting point, part of the surface of the slab is melted, to cause an internal defect and to impair the strength/ductility. Accordingly, the treatment temperature should be lower than the melting point.
  • a heat treatment if conducted at a temperature of lower than 350°C, may not sufficiently help to remove the inner stress and to uniformize a solute element, which is segregated during casting, and therefore may exhibit less advantages. Accordingly, the treatment temperature herein should be 350°C or higher. If a heat treatment is conducted at a temperature equal to or higher than the melting point, part of the surface of the slab ismelted, to cause an internal defect and to impair the strength/ductility. Accordingly, the treatment temperature should be lower than the melting point.
  • a heat treatment if conducted for a time shorter than one hour, may not sufficiently help intermetallic compounds to be solidly dissolved, and this may often cause the intermetallic compounds to be deposited. Accordingly, the treatment time should be one hour or longer .
  • a heat treatment if conducted for a time of longer than about 8 hours, may be saturated in its effect, and this may cause energy loss. Accordingly, the treatment time is preferably controlled to be 8 hours or shorter.
  • the aluminum alloy thick plate after the heat treatment in the heat treatment step (S6) may be subjected to a surface smoothing treatment according to necessity in order to remove crystallized substances and oxides generated on the surface of the thick plate or to eliminate gas accumulation in the surface of the thick plate.
  • the surface smoothing treatment step (S7) is a step of subjecting the surface of the aluminum alloy thick plate produced in the heat treatment step (S6) to a surface smoothing treatment.
  • exemplary surface smoothing treatments include, but are not limited to, cutting such as end mill cutting and diamond bite cutting; grinding which faces the surface typically with a grindstone; and polishing such as buff polishing.
  • a vacuum chamber suffers from a decrease in the degree of vacuum therein caused by, when the chamber is decompressed to attain high vacuum, releasing of adsorbed gas from the inner surface of the chamber and releasing of gas atoms which are solidly dissolved in the thick plate onto the surface. This elongates the time which takes to reach a target degree of vacuum and thereby lowers production efficiency.
  • the following conditions are required for the aluminum alloy thick plate used for a chamber: the amount of gas which adsorbs onto the surface of the thick plate positioned in an inner portion of the chamber is low; and the gas atoms which are solidly dissolved in the thick plate are not released even in high vacuum.
  • the surface smoothing treatment herein satisfies these conditions.
  • the methods for manufacturing an aluminum alloy thick plate each include a melting step (S1), a hydrogen gas removal step (S2), a filtration step (S3), a casting step (S4), a heat treatment step (S5), and a slicing step (S6) in this order.
  • the methods may further include, where necessary, a surface smoothing treatment step (S7) subsequent to the slicing step (S6).
  • a raw material aluminum alloy is melted in the melting step (S1).
  • hydrogen gas is removed from the molten aluminum alloy in the hydrogen gas removal step (S2), and inclusions such as oxides and non-metals are removed therefrom in the filtration step (S3).
  • the resulting aluminum alloy is cast into a slab in the casting step (S4).
  • the slab is subjected to a heat treatment in the heat treatment step (S5) and is then sliced into an aluminum alloy thick plate having a predetermined thickness in the slicing step (S6).
  • the aluminum alloy thick plate having a predetermined thickness is further subjected to a surface smoothing treatment in the surface smoothing treatment step (S7).
  • the manufacturing methods according to the fifth, sixth, seventh, and eighth embodiments of the present invention use, as a raw material aluminum alloy, a 5000 series Al-Mg alloy, a 3000 series Al-Mn alloy, a 6000 series Al-Mg-Si alloy, and a 7000 series Al-Zn-Mg alloy, respectively.
  • the details of them are as follows.
  • a 5000 series Al-Mg alloy as in the first embodiment of the present invention is used in this embodiment.
  • the composition and contents of components of the aluminum alloy, and the reasons why the contents are specified are as in the first embodiment of the present invention.
  • a 3000 series Al-Mn alloy as in the second embodiment of the present invention is used in this embodiment.
  • the composition and contents of components of the aluminum alloy, and the reasons why the contents are specified are as in the second embodiment of the present invention.
  • a 6000 series Al-Mg-Si alloy as in the third embodiment of the present invention is used in this embodiment.
  • the composition and contents of components of the aluminum alloy, and the reasons why the contents are specified are as in the third embodiment of the present invention.
  • a 7000 series Al-Zn-Mg alloy as in the fourth embodiment of the present invention is used in this embodiment.
  • the composition and contents of components of the aluminum alloy, and the reasons why the contents are specified are as in the fourth embodiment of the present invention.
  • This step is the same as with the melting step (S1) in the first to fourth embodiments of the present invention.
  • This step is the same as with the hydrogen gas removal step (S2) in the first to fourth embodiments of the present invention.
  • This step is the same as with the filtration step (S3) in the first to fourth embodiments of the present invention.
  • This step is the same as with the casting step (S4) in the first to fourth embodiments of the present invention.
  • a heat treatment is carried out in the subsequent heat treatment step (S5), for the purpose of removing internal stress and uniformizing the inner structure.
  • the heat treatment of the slab helps to improve the flatness, accuracy of plate thickness, and quality of appearance after anodization.
  • the heat treatment step (S5) is a step of subjecting the slab produced in the casting step (S4) to a heat treatment (heat treatment for homogenization) .
  • the heat treatment is carried out according to a common procedure. Specifically, when the aluminum alloy is a 5000 series Al-Mg alloy (the fifth embodiment of the present invention), a 3000 series Al-Mn alloy (the sixth embodiment of the present invention), and a 6000 series Al-Mg-Si alloy (the seventh embodiment of the present invention), the heat treatment is performed by holding the slab at a temperature of 200°C to 350°C (fifth and sixth embodiments) or 200°C or higher but lower than 400°C (seventh embodiment), both for one hour or longer. When the aluminum alloy is a 7000 series Al-Zn-Mg alloy (the eighth embodiment of the present invention), the heat treatment is performed by holding the slab at a temperature of 200°C or higher but lower than 350°C for one hour or longer.
  • a heat treatment if conducted at a temperature of lower than 200°C, may not sufficiently help to remove the inner stress and therefore may not exhibit satisfactory advantages. Accordingly, the treatment temperature should be 200°C or higher.
  • a heat treatment if conducted at a temperature of more than 350°C (fith and sixth embodiments), or 400°C or higher (seventh embodiment), may excessively increase the ductility and lower the strength and cutting property.
  • cutting property refers to chip breakability. Chips (scraps) are preferably formed as small or short pieces.
  • the treatment temperature should be at most 350°C (fifth and sixth embodiment), or lower than 400°C (seventh embodiment).
  • a heat treatment performed under above-specified temperature conditions helps to improve the flatness and accuracy of plate thickness without adversely affecting the strength and cutting property.
  • a heat treatment if performed at a temperature of lower than 200°C, may not sufficiently help to remove the inner stress and therefore may not exhibit satisfactory advantages. Accordingly, the treatment temperature should be 200°C or higher. In contrast, a heat treatment, if conducted at a temperature of 350°C or higher, may excessively increase the ductility and lower the strength and cutting property.
  • cutting property refers to chip breakability. Chips (scraps) are preferably formed as small or short pieces. This is because long chips become entangled with a working tool (blade) and are rotated therewith, and this damages the surface of the thick plate and breaks the tool. Accordingly, the treatment temperature should be lower than 350°C. A heat treatment performed under above-specified temperature conditions helps to improve the flatness and accuracy of plate thickness without adversely affecting the strength and cutting property.
  • a heat treatment if conducted for a time shorter than one hour, may not sufficiently help intermetallic compounds to be solidly dissolved, and this may often cause the intermetallic compounds to be deposited. Accordingly, the treatment time should be one hour or longer. In contrast, a heat treatment, if conducted for a time of longer than about 8 hours, may be saturated in its effect, and this may cause energy loss. Accordingly, the treatment time is preferably controlled to be 8 hours or shorter.
  • the slicing step (S6) is a step of slicing the slab obtained in the heat treatment step (S5) into an aluminum alloy thick plate having a predetermined thickness.
  • the details of this step are as with the slicing step (S5) in the first to fourth embodiments of the present invention.
  • the aluminum alloy thick plate produced in the slicing step (S6) may be subjected to a surface smoothing treatment according to necessity in order to remove crystallized substances and oxides formed on the surface of the thick plate or to eliminate gas accumulation in the surface of the thick plate.
  • the surface smoothing treatment step (S7) is a step of subjecting the surface of the aluminum alloy thick plate produced in the slicing step (S6) to a surface smoothing treatment.
  • the details of this step are as with the surface smoothing treatment step (S7) in the first to fourth embodiments of the present invention.
  • the methods for manufacturing an aluminum alloy thick plate each include a melting step (S1), a hydrogen gas removal step (S2), a filtration step (S3), a casting step (S4), a slicing step (S5), and a heat treatment step (S6) in this order.
  • the methods may further include, where necessary, a surface smoothing treatment step (S7) subsequent to the heat treatment step (S6).
  • a raw material aluminum alloy is melted in the melting step (S1).
  • hydrogen gas is removed from the molten aluminum alloy in the hydrogen gas removal step (S2), and inclusions such as oxides and non-metals are removed therefrom in the filtration step (S3).
  • the resulting aluminum alloy is cast into a slab in the casting step (S4).
  • the slab is then sliced into an aluminum alloy thick plate having a predetermined thickness in the slicing step (S5).
  • the aluminum alloy thick plate having a predetermined thickness is then subjected to a heat treatment in the heat treatment step (S6) and, where necessary, further subjected to a surface smoothing treatment in the surface smoothing treatment step (S7).
  • the manufacturing methods according to the ninth, tenth, eleventh, and twelfth embodiments of the present invention use a 5000 series Al-Mg alloy, a 3000 series Al-Mn alloy, a 6000 series Al-Mg-Si alloy, and a 7000 series Al-Zn-Mg alloy, respectively, as a raw material aluminum alloy.
  • the details of them are as follows.
  • a 5000 series Al-Mg alloy as in the first embodiment of the present invention is used in this embodiment.
  • the composition and contents of components of the aluminum alloy, and the reasons why the contents are specified are as in the first embodiment of the present invention.
  • a 3000 series Al-Mn alloy as in the second embodiment of the present invention is used in this embodiment.
  • the composition and contents of components of the aluminum alloy, and the reasons why the contents are specified are as in the second embodiment of the present invention.
  • a 6000 series Al-Mg-Si alloy as in the third embodiment of the present invention is used in this embodiment.
  • the composition and contents of components of the aluminum alloy, and the reasons why the contents are specified are as in the third embodiment of the present invention.
  • a 7000 series Al-Zn-Mg alloy as in the fourth embodiment of the present invention is used in this embodiment.
  • the composition and contents of components of the aluminum alloy, and the reasons why the contents are specified are as in the fourth embodiment of the present invention.
  • This step is the same as with the melting step (S1) in the first to fourth embodiments of the present invention.
  • This step is the same as with the hydrogen gas removal step (S2) in the first to fourth embodiments of the present invention.
  • This step is the same as with the filtration step (S3) in the first to fourth embodiments of the present invention.
  • This step is the same as with the casting step (S4) in the first to fourth embodiments of the present invention.
  • This step is the same as with the slicing step (S5) in the first to fourth embodiments of the present invention.
  • the heat treatment step (S6) is a step of carrying out a heat treatment (heat treatment for homogenization) on the aluminum alloy thick plate having a predetermined thickness produced in the slicing step (S5).
  • the heat treatment may be carried out according to a common procedure. Specifically, when the aluminum alloy is a 5000 series Al-Mg alloy (the ninth embodiment of the present invention), a 3000 series Al-Mn alloy (the tenth embodiment of the present invention), and a 6000 series Al-Mg-Si alloy (the eleventh embodiment of the present invention), the heat treatment is performed by holding the aluminum alloy thick plate at a temperature of 200°C or higher but lower than 400°C for one hour or longer.
  • the heat treatment is performed by holding the aluminum alloy thick plate at a temperature of 200°C or higher but lower than 350°C for one hour or longer.
  • the details of the other conditions and procedures are as with the heat treatment step (S6) in the first to fourth embodiments of the present invention.
  • a heat treatment if conducted at a temperature of lower than 200°C may not sufficiently help to remove the inner stress and therefore may not exhibit satisfactory advantages. Accordingly, the treatment temperature should be 200°C or higher. In contrast, a heat treatment, if conducted at a temperature of 400°C or higher, may excessively increase the ductility and lower the strength and cutting property.
  • cutting property refers to chip breakability. Chips (scraps) are preferably formed as small or short pieces. This is because long chips become entangled with a working tool (blade) and are rotated therewith, and this damages the surface of the thick plate and breaks the tool. Accordingly, the treatment temperature should be lower than 400°C. A heat treatment performed under above-specified temperature conditions helps to improve the flatness and accuracy of plate thickness without adversely affecting the strength and cutting property.
  • a heat treatment if conducted at a temperature of lower than 200°C, may not sufficiently help to remove the inner stress and therefore may not exhibit satisfactory advantages. Accordingly, the treatment temperature should be 200°C or higher. In contrast, a heat treatment, if conducted at a temperature of 350°C or higher, may excessively increase the ductility and lower the strength and cutting property.
  • cutting property refers to chip breakability. Chips (scraps) are preferably formed as small or short pieces. This is because long chips become entangled with a working tool (blade) and are rotated therewith, and this damages the surface of the thick plate and breaks the tool. Accordingly, the treatment temperature should be lower than 350°C. A heat treatment performed under above-specified temperature conditions helps to improve the flatness and accuracy of plate thickness without adversely affecting the strength and cutting property.
  • a heat treatment if conducted for a time shorter than one hour, may not sufficiently help intermetallic compounds to be solidly dissolved, and this may often cause the intermetallic compounds to be deposited. Accordingly, the treatment time should be one hour or longer. In contrast, a heat treatment, if conducted for a time of longer than about 8 hours, may be saturated in its effect, and this may cause energy loss. Accordingly, the treatment time is preferably controlled to be 8 hours or shorter.
  • This step is the same as with the surface smoothing treatment step (S7) in the first to fourth embodiments of the present invention.
  • These aluminum alloy thick plates are manufactured by the procedures of the manufacturing method according to any one of the first to twelfth embodiments of the present invention and have an average crystal grain size of 400 ⁇ m or less.
  • the aluminum alloy thick plates obtained by the method according to the present invention have an average crystal grain size of 400 ⁇ m or less whereby can have improved quality of appearance after anodization and show a smaller within-lot variation.
  • a thick plate if containing intermetallic compounds having large sizes, suffers from unevenness (uneven color) of the cross section and surface of the thick plate upon anodization.
  • the aluminum alloy thick plates obtained by the method according to the present invention contain intermetallic compounds with small sizes and are thereby resistant to such unevenness.
  • the measurement of the crystal grain size may be carried out, for example, in the following manner. Specifically, measurements are conducted in cross sections at four points, i.e., at thicknesses of T/5, 2T/5, 3T/5, and 4T/5 ranging from one surface of the slab to the other, wherein T represents the thickness of the slab, and the four measured data are averaged. These measured data are determined typically according to a cutting method. In the cutting method, cross sections of the aluminum alloy thick plate are etched according to a Barker method and are observed with an optical microscope.
  • the control of the average crystal grain size to 400 ⁇ m or less may be carried out typically in the following manner. Specifically, a cooling rate (average cooling rate from the liquidus temperature to the solidus temperature) during casting is set to be 0.2°C/second or more. Additionally, the aluminum alloy contains 0.1 percent by mass or less of Ti or 0.3 percent by mass or less of Zr and thereby the crystal grain size can be more finer (smaller) in the manufacturing methods according to the first to third embodiments, the fifth to seventh embodiments, and the ninth to eleventh embodiments of the present invention.
  • the aluminum alloy contains 0.1 percent by mass or less of Ti or 0.25 percent by mass or less of Zr and thereby the crystal grain size can be more finer (smaller) in the manufacturing methods according to the fourth, eighth, and twelfth embodiments of the present invention.
  • the resulting aluminum alloy thick plates manufactured by the procedures of the manufacturing methods according to the first to twelfth embodiments of the present invention are satisfactory in the surface condition, flatness, and accuracy of plate thickness as described above and can be used for various applications including semiconductor-related devices such as base substrates, transport devices, and vacuum chambers; electrical and electronic parts and their manufacturing devices; household articles; and mechanical parts. Additionally, they can be recycled and used for other applications.
  • This experimental example relates to the first embodiment of the present invention.
  • the experimental example used 5000 series Al-Mg alloys as the aluminum alloys.
  • Alloys 1A to 12A were used as example alloys; while Alloys 13A to 22A were used as comparative example alloys .
  • Alloy Alloy 1A 2.4 0.1 0.3 - - - 0.01 - 5000 series Alloy 2A 2.4 0.1 0.3 - 0.3 - - 0.01 - 5000 series Alloy 3A 5.0 0.1 0.3 - - - 0.01 - 5000 series Alloy 4A 8.0 0.1 0.3 - - - 0.01 0.1 5000 series Alloy 5A 11.0 0.1 0.3 - - - 0.01 - 5000 series Alloy 6A 5.0 0.3 0.5 0.3 - - - 0.01 - 5000 series Alloy 7A 5.0 0.1 0.3 - 0.05 - - 0. 0.
  • a series of slabs having a plate thickness of 500 mm was prepared by subjecting Alloys 1A to 22A to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the sliced samples and hot-rolled samples were prepared from the slabs.
  • the sliced samples were prepared by subjecting the slabs to a slicing step, while the hot-rolled samples were prepared by subjecting the slabs to a heat treatment and subsequently to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the sliced samples were further subjected to a heat treatment step in which they were held at a temperature of 500°C for 4 hours.
  • the resulting sliced samples are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the first embodiment of the present invention, but the resulting hot-rolled samples are not.
  • the sliced samples using Alloys 1A to 22A correspond to examples according to the first embodiment of the present invention.
  • the sliced samples were tested to determine their amounts of warpage (flatness) per 1 m in the casting direction, while the hot-rolled samples were tested to determine their amounts of warpage (flatness) per 1 m in the rolling direction.
  • Samples having an amount of warpage of 0.4 mm or less per 1 m length were evaluated as having accepted flatness (Accepted), while those having an amount of warpage of more than 0.4 mm per 1 m length were evaluated as having unaccepted flatness (Failed).
  • thicknesses at six positions of each sample were measured with a micrometer.
  • the six positions are the four corners of the sample thick plate, and two positions each located at a half the length of the long sides and 20 mm inside in the width direction of the thick plate.
  • Samples having thicknesses of 19.94 mm or more and 20.06 mm or less at all the six positions were evaluated as having excellent accuracy of plate thickness (Excellent) ; and those having thicknesses of 19.90 mm or more and 20.10 mm or less at all the six positions were evaluated as having accepted accuracy of plate thickness (Accepted).
  • the strength test was conducted in the following manner. Specifically, JIS No. 5 test pieces were prepared from the aluminum alloy thick plates to perform tensile test thereon, and their tensile strength and 0.2%-proof stress were measured. Samples having a tensile strength of 180 N/mm 2 or more were evaluated as having accepted strength (Accepted) ; while those having a tensile strength of less than 180 N/mm 2 were evaluated as having unaccepted strength (Failed).
  • the anodizability evaluation was carried out in the following manner. Anodized aluminum films having a thickness of 10 ⁇ m were formed on surfaces and cross sections of the aluminum alloy thick plates by sulfuric acid anodization under conditions of 15% sulfuric acid, 20°C, and a current density of 2 A/dm 2 . The appearances of surfaces and cross sections of the thick plates were observed. Samples showing no unevenness (uneven color) in their appearances were evaluated as having accepted anodizability (Accepted); while those showing unevenness in their appearances were evaluated as having unaccepted anodizability (Failed) .
  • the average crystal grain sizes of the thick plates were determined.
  • the measurements of the average crystal grain sizes were carried out in the following manner. Specifically, measurements were conducted in cross sections at four points, i.e., at thicknesses of T/5, 2T/5, 3T/5, and 4T/5 ranging from one surface of the slab to the other, wherein T represents the thickness of the slab, and the four measured data were averaged. These measured data were determined according to the cutting method. In the cutting method, cross sections of the aluminum alloy thick plate were etched according to the Barker method and were observed with an optical microscope.
  • Table 2 shows the test results of the sliced samples, in which Alloys 1A to 12A correspond to Examples, and Alloys 13A to 22A correspond to comparative examples.
  • Table 3 shows the test results of the hot-rolled samples, in which all Alloys 1A to 22A correspond to comparative examples .
  • the sample using Alloy 14A contained Mg in a content of more than its upper limit in the material aluminum alloy, thereby suffered from casting cracks, and was unproducible.
  • the sample using Alloy 13A contained Mg in a content of less than its lower limit in the material aluminum alloy and thereby had insufficient strength.
  • the samples using Alloys 1A to 13A, 17A, and 20A to 22A did not suffer from unevenness in their appearances of surfaces after anodization.
  • the samples using Alloys 15A, 16A, 18A, and 19A contained Si, Fe, Mn, and Cr, respectively, in a content of more than the upper limit in the material aluminum alloy, thereby caused a coarse intermetallic compound, and suffered from unevenness in their appearances of surfaces after anodization.
  • the samples using Alloys 1A to 13A and 15A to 22A did not suffer from unevenness in their appearances of cross sections after anodization.
  • the samples using Alloys 17A, 20A, 21A, and 22A contained Cu, Zn, Ti, and Zr, respectively, in a content of more than the upper limit in the material aluminum alloy, and advantages obtained therefrom were thereby saturated, resulting in inferior economical efficiency.
  • the sample using Alloy 14A contained Mg in a content of more than the upper limit in the material aluminum alloy, suffered from casting cracks, and was unproducible.
  • the sample using Alloy 13A contained Mg in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the samples using Alloys 15A, 16A, 18A, and 19A contained Si, Fe, Mn, and Cr, respectively, in a content of more than the upper limit in the material aluminum alloy, caused coarse intermetallic compounds, and suffered from unevenness in their appearances of surfaces after anodization.
  • This experimental example relates to the first embodiment of the present invention.
  • the experimental example used Alloy 3A in Table 1.
  • a series of slabs having a plate thickness of 500 mm was prepared by subjecting Alloy 3A to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the slabs were further subjected to a slicing step to give sliced samples .
  • the sliced samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • Samples A1 and A2, whose heat treatment conditions satisfy the conditions according to the first embodiment of the present invention, correspond to examples according to the first embodiment of the present invention; whereas Samples A3 to A5, whose heat treatment conditions do not satisfy the conditions according to the first embodiment of the present invention, correspond to comparative examples.
  • the evaluation test for accuracy of plate thickness is as in First Experimental Example.
  • Examples A1 and A2 whose heat treatment conditions satisfy the conditions specified in the first embodiment of the present invention, excelled in flatness and accuracy of plate thickness.
  • Comparative Example A3 did not undergo a heat treatment and was thereby somewhat inferior in flatness and accuracy of plate thickness to Examples A1 and A2.
  • Comparative Example A4 underwent a heat treatment at a temperature lower than the temperature range specified in the first embodiment of the present invention (lower than 400°C) and was thereby somewhat inferior in flatness to Examples A1 and A2.
  • Comparative Example A5 underwent a heat treatment at a temperature higher than the temperature range specified in the first embodiment of the present invention (higher than the melting point), whereby suffered from internal partial melting and resulting internal defects, and was unproducible.
  • This experimental example relates to the second embodiment of the present invention.
  • the experimental example used 3000 series Al-Mn alloys as the aluminum alloys.
  • Alloys 23A and 24A were used as example alloys; while Alloys 25A and 26A were used as comparative example alloys .
  • Alloy 26A - 0.1 0.3 - 1.7 - - 0.01 - 3000 series Mn content more than upper limit
  • a series of slabs having a plate thickness of 500 mm was prepared by subjecting Alloys 23A to 26A to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the sliced samples and hot-rolled samples were prepared from the slabs.
  • the sliced samples were prepared by subjecting the slabs to a slicing step, while the hot-rolled samples were prepared by subjecting the slabs to a heat treatment and subsequently to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the sliced samples were further subjected to a heat treatment step in which they were held at a temperature of 500°C for 4 hours.
  • the sliced samples after the treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the second embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 23A and 24A correspond to examples according to the second embodiment of the present invention.
  • the prepared sliced samples and hot-rolled samples were further subjected to a flatness evaluation test, an evaluation test for accuracy of plate thickness, a strength test, and an anodizability evaluation test.
  • thick plates vary depending on the type of alloy used, and the criteria for the strength were modified as follows . Specifically, samples having a tensile strength of 90 N/mm 2 or more were evaluated as having accepted strength (Accepted), whereas those having a tensile strength of less than 90 N/mm 2 were evaluated as having unaccepted strength (Failed).
  • the sample using Alloy 25A contained Mn in a content less than the lower limit in the material aluminum alloy and thereby had insufficient strength.
  • the sample using Alloy 26A contained Mn in a content of more than the upper limit in the material aluminum alloy, thereby caused coarse intermetallic compounds, and suffered from unevenness in its appearance of surface after anodization.
  • the samples using Alloys 23A to 26A did not suffer from unevenness in their appearances of cross sections after anodization.
  • the sample using Alloy 25A contained Mn in a content of less than the lower limit in the material aluminum alloy and was thereby somewhat inferior in strength to the other hot-rolled samples.
  • the sample using Alloy 26A contained Mn in a content of more than the upper limit in the material aluminum alloy, thereby caused coarse intermetallic compounds, and suffered from unevenness in its appearance of surface after anodization.
  • the samples using Alloy 23A to 26A suffered from unevenness in their appearances of cross sections after anodization.
  • This experimental example relates to the third embodiment of the present invention.
  • the experimental example used 6000 series Al-Mg-Si alloys as the aluminum alloys.
  • Alloys 27A and 28A were used as example alloys; while Alloys 29A to 32A were used as comparative example alloys.
  • [Table 7] Category Num ber Element (percent by mass) Alloy type Remarks Mg Si Fe Cu Mn Cr Zn Ti Zr
  • Alloy Alloy 27A 1.0 0.5 0.5 0.3 0.1 0.2 0.2 0.02 - 6000 series Alloy 28A 0.5 1.0 0.2 - 0.1 - - 0.02 - 6000 series Comparative Example Alloy Alloy 29A 0.9 0.1 0.5 - 0.1 - - 0.02 - 6000 series Si content less than lower limit Alloy 30A 0.9 1.8 0.4 - 0.1 - - 0.02 - 6000 series Si content more than upper limit Alloy 31A 0.2 0.5 0.5 - 0.1 - - 0.02 - 6000 series Mg content less than lower limit Alloy 32A 1.7 0.5 0.4 - 0.1 - -
  • a series of slabs having a plate thickness of 500 mm was prepared by subjecting Alloy 27A to 32A to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the sliced samples and hot-rolled samples were prepared from the slabs.
  • the sliced samples were prepared by subjecting the slabs to a slicing step, while the hot-rolled samples were prepared by subjecting the slabs to a heat treatment and subsequently to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the sliced samples were further subjected to a heat treatment step in which they were held at a temperature of 500°C for 4 hours.
  • the resulting sliced samples and hot-rolled samples were further subjected to a solution treatment at 520°C and subsequently to an aging treatment at 175°C for 8 hours.
  • the sliced samples after these treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the third embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 27A and 28A correspond to examples according to the third embodiment of the present invention.
  • thick plates vary depending on the type of alloy used, and the criteria for the strength were modified as follows . Specifically, samples having a tensile strength of 200 N/mm 2 or more were evaluated as having accepted strength (Accepted), whereas those having a tensile strength of less than 200 N/mm 2 were evaluated as having unaccepted strength (Failed).
  • the samples using Alloys 29A and 31A contained Si and Mg, respectively, in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the sample using Alloy 30A contained Si in a content of more than the upper limit in the material aluminum alloy, caused coarse intermetallic compounds, and suffered from unevenness in its appearance of surface after anodization.
  • the sample using Alloy 32A contained Mg in a content of more than the upper limit in the material aluminum alloy, and advantages obtained therefrom were saturated, resulting in inferior economical efficiency.
  • the samples using Alloys 27A to 32A did not suffer from unevenness in their appearances of cross sections after anodization.
  • the samples using Alloys 29A and 31A contained Si and Mg, respectively, in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the sample using Alloy 30A contained Si in a content of more than the upper limit in the material aluminum alloy, caused coarse intermetallic compounds, and suffered from unevenness in its appearance of surface after anodization.
  • the sample using Alloy 32A contained Mg in a content of more than the upper limit in the material aluminum alloy, and advantages obtained therefrom were saturated, resulting in inferior economical efficiency.
  • the samples using Alloy 27A to 32A suffered from unevenness in their appearances of cross sections after anodization.
  • This experimental example relates to the fourth embodiment of the present invention.
  • the experimental example used 7000 series Al-Zn-Mg alloys as the aluminum alloys.
  • Alloys 33A and 34A were used as example alloys, while Alloys 35A to 38A were used as comparative example alloys.
  • Alloy Alloy 33A 2.5 0.1 0.2 1.8 - 0.2 5.5 0.02 - 7000 series Alloy 34A 3.5 0.2 0.2 2.0 - - 8.5 0.02 0.2 7000 series
  • a series of slabs having a plate thickness of 500 mm was prepared by subjecting Alloys 33A to 38A to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the sliced samples and hot-rolled samples were prepared from the slabs.
  • the sliced samples were prepared by subjecting the slabs to a slicing step, while the hot-rolled samples were prepared by subjecting the slabs to a heat treatment and subsequently to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the sliced samples were further subjected to a heat treatment step in which they were held at a temperature of 500°C for 4 hours.
  • the resulting sliced samples and hot-rolled samples were further subjected to a solution treatment at 470°C and subsequently to an aging treatment at 120°C for 48 hours.
  • the sliced samples after these treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the fourth embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 33A and 34A correspond to examples according to the fourth embodiment of the present invention.
  • thick plates vary depending on the type of alloy used, and the criteria for the strength were modified as follows . Specifically, samples having a tensile strength of 250 N/mm 2 or more were evaluated as having accepted strength (Accepted), whereas those having a tensile strength of less than 250 N/mm 2 were evaluated as having unaccepted strength (Failed).
  • the samples using Alloys 35A and 37A contained Mg and Zn, respectively, in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the samples using Alloys 36A and 38A contained Mg and Zn, respectively, in a content of more than the upper limit in the material aluminum alloy and suffered from unevenness in their appearances of surfaces after anodization.
  • the samples using Alloys 33A to 38A did not suffer from unevenness in their appearances of cross sections after anodization.
  • the samples using Alloys 35A and 37A contained Mg and Zn, respectively, in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the samples using Alloys 36A and 38A contained Mg and Zn, respectively, in a content of more than the upper limit in the material aluminum alloy and suffered from unevenness in their appearances of surfaces after anodization.
  • the samples using Alloys 33A to 38A suffered from unevenness in their appearances of cross sections after anodization .
  • This experimental example relates to the fifth embodiment of the present invention.
  • the experimental example used 5000 series Al-Mg alloys as the aluminum alloys.
  • a series of slabs having a plate thickness of 500 mm was prepared by subjecting Alloys 1B to 22B to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the slabs were further subjected to a treatment in a heat treatment step, in which they were held at a temperature of 350°C for 4 hours.
  • sliced samples and hot-rolled samples were prepared from the thermally treated slabs.
  • the sliced samples were prepared by slicing the slabs in a slicing step, while the hot-rolled samples were prepared by subjecting the slabs to hot rolling.
  • the sliced samples andhot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the sliced samples after these treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the fifth embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 1B to 22B correspond to examples according to the fifth embodiment of the present invention.
  • Table 12 shows the test results of the sliced samples.
  • the samples using Alloys 1B to 12B correspond to examples according to the fifth embodiment of the present invention, whereas the samples using Alloys 13B to 22B correspond to comparative examples.
  • Table 13 shows the test results of the hot-rolled samples. In Table 13, all the samples using Alloys 1B to 22B correspond to comparative examples.
  • the sample using Alloy 14B contained Mg in a content of more than the upper limit in the material aluminum alloy, thereby suffered from casting cracks, and was unproducible.
  • the sample using Alloy 13B contained Mg in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the samples using Alloys 1B to 13B, 17B, and 20B to 22B did not suffer from unevenness in their appearances of surfaces after anodization .
  • the samples using Alloys 15B, 16B, 18B, and 19B contained Si, Fe, Mn, and. Cr, respectively, in a content of more than the upper limit in the material aluminum alloy, caused coarse intermetallic compounds, and suffered from unevenness in their appearances of surfaces after anodization.
  • the samples using Alloys 1B to 13B and 15B to 22B did not suffer from unevenness in their appearances of cross sections after anodization.
  • Alloys 17B, 20B, 21B, and 22B contained Cu, Zn, Ti, and Zr, respectively, in a content of more than the upper limit in the material aluminum alloy, and advantages obtained therefrom were saturated, resulting in inferior economical efficiency.
  • the sample using Alloy 14B contained Mg in a content of more than the upper limit in the material aluminum alloy, suffered from casting cracks, and was unproducible.
  • the sample using Alloy 13B contained Mg in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the samples using Alloys 15B, 16B, 18B, and 19B contained Si, Fe, Mn, and Cr, respectively, in a content of more than the upper limit in the material aluminum alloy, caused coarse intermetallic compounds, and suffered from unevenness in their appearances of surfaces after anodization.
  • This experimental example relates to the fifth embodiment of the present invention.
  • the experimental example used Alloy 3B in Table 11.
  • a series of slabs having a plate thickness of 500 mm was prepared by subjecting Alloy 3B to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the slabs were further subjected to a treatment in a heat treatment step, in which they were further subjected to a heat treatment under conditions given in Table 14.
  • Samples B1 and B2, whose heat treatment conditions satisfy the conditions specified in the fifth embodiment of the present invention, correspond to examples according to the fifth embodiment of the present invention; whereas Samples B3 to B5, whose heat treatment conditions do not satisfy the conditions specified in the fifth embodiment of the present invention, correspond to comparative examples.
  • the sliced samples after the treatments were subjected to a flatness evaluation test, an evaluation test for accuracy of plate thickness, and a cutting property evaluation test.
  • the evaluation test for accuracy of plate thickness is as in First Experimental Example.
  • the evaluation of cutting property i.e., chip breakability was performed by drilling a sample and measuring the number of chips per unit mass. Specifically, the sample was drilled with a drill having a diameter of 5 mm at a number of revolutions of 7000 rpm and a feed rate of 300 mm/minute, and the number of generated chips per 10 g was measured. Samples having a number of chips of 1000 or more per 10 g were evaluated as having accepted cutting property (Accepted) ; whereas those having a number of chips of less than 1000 per 10 g were evaluated as having unaccepted cutting property (Failed).
  • Examples B1 and B2 whose heat treatment conditions satisfy the conditions specified in the fifth embodiment of the present invention, excelled in flatness, accuracy of plate thickness, and cutting property.
  • Comparative Example B3 did not undergo a heat treatment, thereby show poor flatness, and was somewhat inferior in accuracy of plate thickness to Examples B1 and B2.
  • Comparative Example B4 whose heat treatment had been performed at a temperature higher than the range specified in the fifth embodiment of the present invention, was thereby inferior in cutting property.
  • This experimental example relates to the sixth embodiment of the present invention.
  • the experimental example used 3000 series Al-Mn alloys as the aluminum alloys.
  • a series of slabs having a plate thickness of 500 mm was prepared by subj ecting Alloys 23B to 26B to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the slabs were further subjected to a treatment in a heat treatment step, in which they were held at a temperature of 350°C for 4 hours.
  • sliced samples and hot-rolled samples were prepared from the thermally treated slabs.
  • the sliced samples were prepared by slicing the slabs in a slicing step, while the hot-rolled samples were prepared by subj ecting the slabs to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the sliced samples after these treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the sixth embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 23B and 24B correspond to examples according to the sixth embodiment of the present invention.
  • the sliced samples and hot-rolled samples after the treatments were subjected to a flatness evaluation test, an evaluation test for accuracy of plate thickness, a strength test, and an anodizability evaluation test.
  • thick plates vary depending on the type of alloy used, and the criteria for the strength were modified as follows . Specifically, samples having a tensile strength of 90 N/mm 2 or more were evaluated as having accepted strength (Accepted); whereas those having a tensile strength of less than 90 N/mm 2 were evaluated as having unaccepted strength (Failed).
  • the sample using Alloy 25B contained Mn in a content less than the lower limit in the material aluminum alloy and thereby had insufficient strength.
  • the sample using Alloy 26B contained Mn in a content of more than the upper limit in the material aluminum alloy, thereby caused coarse intermetallic compounds, and suffered from unevenness in its appearance of surface after anodization.
  • the samples using Alloys 23B to 26B did not suffer from unevenness in their appearances of cross sections after anodization.
  • the sample using Alloy 25B contained Mn in a content of less than the lower limit in the material aluminum alloy and was thereby somewhat inferior in strength to the other hot-rolled samples.
  • the sample using Alloy 26B contained Mn in a content of more than the upper limit in the material aluminum alloy, thereby caused coarse intermetallic compounds, and suffered from unevenness in its appearance of surface after anodization.
  • the samples using Alloys 23B to 26B suffered from unevenness in their appearances of cross sections after anodization.
  • This experimental example relates to the seventh embodiment of the present invention.
  • the experimental example used 6000 series Al-Mg-Si alloys as the aluminum alloys.
  • a series of slabs having a plate thickness of 500 mm was prepared by subj ecting Alloys 27B to 32B to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the slabs were further subjected to a treatment in a heat treatment step, in which they were held at a temperature of 350°C for 4 hours.
  • sliced samples and hot-rolled samples were prepared from the thermally treated slabs.
  • the sliced samples were prepared by slicing the slabs in a slicing step, while the hot-rolled samples were prepared by subj ecting the slabs to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the resulting sliced samples and hot-rolled samples were further subjected to a solution treatment at 520°C and subsequently to an aging treatment at 175°C for 8 hours.
  • the sliced samples after these treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the seventh embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 27B and 28B correspond to examples according to the seventh embodiment of the present invention.
  • thick plates vary depending on the type of alloy used, and the criteria for the strength were modified as follows . Specifically, samples having a tensile strength of 200 N/mm 2 or more were evaluated as having accepted strength (Accepted) ; while those having a tensile strength of less.than 200 N/mm 2 were evaluated as having unaccepted strength (Failed).
  • the samples using Alloys 29B and 31B contained Si and Mg, respectively, in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the sample using Alloy 30B contained Si in a content of more than the upper limit in the material aluminum alloy, thereby caused coarse intermetallic compounds, and suffered from unevenness in its appearance of surface after anodization.
  • the sample using Alloy 32B contained Mg in a content of more than the upper limit in the material aluminum alloy, and advantages obtained therefrom were saturated, resulting in inferior economical efficiency.
  • the samples using Alloys 27B to 32B did not suffer from unevenness in their appearances of cross sections after anodization.
  • the samples using Alloys 29B and 31B contained Si and Mg, respectively, in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the sample using Alloy 30B contained Si in a content of more than the upper limit in the material aluminum alloy, caused coarse intermetallic compounds, and suffered from unevenness in its appearance of surfaces after anodization.
  • the sample using Alloy 32B contained Mg in a content of more than the upper limit in the material aluminum alloy, and advantages obtained therefrom were saturated, resulting in inferior economical efficiency.
  • the samples using Alloys 27B to 32B suffered from unevenness in their appearances of cross sections after anodization.
  • This experimental example relates to the eighth embodiment of the present invention.
  • the experimental example used 7000 series Al-Zn-Mg alloys as the aluminum alloys.
  • Alloys 33B and 34B were used as example alloys; while Alloys 35B to 38B were used as comparative example alloys .
  • Alloy Alloy 33B 2.5 0.1 0.2 1.8 - 0.2 4.0 0.02 - 7000 series Alloy 34B 3.5 0.2 0.2 2.0 - - 8.0 0.02 0.2 7000 series
  • a series of slabs having a plate thickness of 500 mm was prepared by subj ecting Alloys 33B to 38B to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the slabs were further subjected to a treatment in a heat treatment step, in which they were held at a temperature of 300°C for 4 hours.
  • sliced samples and hot-rolled samples were prepared from the thermally treated slabs.
  • the sliced samples were prepared by slicing the slabs in a slicing step, while the hot-rolled samples were prepared by subj ecting the slabs to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the resulting sliced samples and hot-rolled samples were further subjected to a solution treatment at 470°C and subsequently to an aging treatment at 120°C for 48 hours.
  • the sliced samples after these treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the eighth embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 33B and 34B correspond to examples according to the eighth embodiment of the present invention.
  • thick plates vary depending on the type of alloy used, and the criteria for the strength were modified as follows . Specifically, samples having a tensile strength of 250 N/mm 2 or more were evaluated as having accepted strength (Accepted) ; while those having a tensile strength of less than 250 N/mm 2 were evaluated as having unaccepted strength (Failed).
  • the samples using Alloy 35B and 37B contained Mg and Zn, respectively, in a content of less than the lower limit .in the material aluminum alloy and showed insufficient strength.
  • the samples using Alloys 36B and 38B contained Mg and Zn, respectively, in a content of more than the upper limit in the material aluminum alloy and suffered from unevenness in their appearances of surfaces after anodization.
  • the samples using Alloys 33B to 38B did not suffer from unevenness in their appearances of cross sections after anodization.
  • the samples using Alloys 35B and 37B contained Mg and Zn, respectively, in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the samples using Alloys 36B and 38B contained Mg and Zn, respectively, in a content of more than the upper limit in the material aluminum alloy and thereby suffered from unevenness in their appearances of surfaces after anodization.
  • This experimental example relates to the ninth embodiment of the present invention.
  • the experimental example used 5000 series Al-Mg alloys as the aluminum alloys.
  • a series of slabs having a plate thickness of 500 mm was prepared by subjecting Alloys 1C to 22C to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the sliced samples and hot-rolled samples were prepared from the slabs.
  • the sliced samples were prepared by subjecting the slabs to a slicing step, while the hot-rolled samples were prepared by subjecting the slabs to a heat treatment and subsequently to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the sliced samples were further subjected to a heat treatment step in which they were held at a temperature of 350°C for 4 hours.
  • the sliced samples after these treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the ninth embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 1C to 22C correspond to examples according to the ninth embodiment of the present invention.
  • the average crystal grain sizes of the thick plates were determined in the same manner as in First Experimental Example, because the crystal grain size of a thick plate affects the anodizability thereof.
  • Table 22 shows the test results of the sliced samples, in which the samples using Alloys 1C to 12C correspond to examples according to the ninth embodiment of the present invention; while the samples using Alloys 13C to 22C correspond to comparative examples.
  • Table 23 shows the test results of the hot-rolled samples, in which all the samples using Alloys 1C to 22C correspond to comparative examples.
  • the sample using Alloy 14C contained Mg in a content of more than the upper limit in the material aluminum alloy, suffered from casting cracks, and was unproducible.
  • the sample using Alloy 13C contained Mg in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the samples using Alloys 1C to 13C, 17C, and 20C to 22C did not suffer from unevenness in their appearances of surfaces after anodization.
  • the samples using Alloys 15C, 16C, 18C, and 19C contained Si, Fe, Mn, and Cr, respectively, in a content of more than the upper limit in the material aluminum alloy, caused coarse intermetallic compounds, and suffered from unevenness in their appearances of surfaces after anodization.
  • the samples using Alloys 1C to 13C and 15C to 22C did not suffer from unevenness in their appearances of cross sections after anodization.
  • the samples using Alloys 17C, 20C, 21C, and 22C contained Cu, Zn, Ti, and Zr, respectively, in a content of more than the upper limit in the material aluminum alloy, and advantages obtained therefrom were saturated, resulting in inferior economical efficiency.
  • the sample using Alloy 14C contained Mg in a content of more than the upper limit in the material aluminum alloy, suffered from casting cracks, and was unproducible.
  • the sample using Alloy 13C contained Mg in a content of less than the lower limit in the material aluminum alloy and showed insufficient strength.
  • the samples using Alloy 15C, 16C, 18C, and 19C contain Si, Fe, Mn, and Cr, respectively, in a content of more than the upper limit, caused coarse intermetallic compounds, and suffered from unevenness in their appearances of surfaces after anodization.
  • This experimental example relates to the ninth embodiment of the present invention.
  • the experimental example used Alloy 3C in Table 21.
  • a series of slabs having a plate thickness of 500 mm was prepared by subjecting Alloy 3C to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the slabs were subjected to a slicing step to give sliced samples.
  • the sliced samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • Samples C1 and C2, whose heat treatment conditions satisfy the conditions specified in the ninth embodiment of the present invention, correspond to examples according to the ninth embodiment of the present invention; while Samples C3 to C5, whose heat treatment conditions do not satisfy the conditions specified in the ninth embodiment of the present invention, correspond to comparative examples.
  • the sliced samples after the treatments were subjected to a flatness evaluation test and an evaluation test for accuracy of plate thickness.
  • the evaluation test for accuracy of plate thickness is as in First Experimental Example.
  • the cutting property evaluation test is as in Seventh Experimental Example.
  • Examples C1 and C2 whose heat treatment conditions satisfy the conditions specified in the ninth embodiment of the present invention, excelled in flatness, accuracy of plate thickness, and cutting property.
  • Comparative Example C4 had been thermally treated at a temperature higher than the range specified in the ninth embodiment of the present invention and thereby showed poor cutting property.
  • Comparative Example C5 had been thermally treated at a temperature lower than the range specified in the ninth embodiment of the present invention, thereby showed poor flatness, and was somewhat inferior in accuracy of plate thickness to Examples C1 and C2.
  • This experimental example relates to the tenth embodiment of the present invention.
  • the experimental example used 3000 series Al-Mn alloys as the aluminum alloys.
  • a series of slabs having a plate thickness of 500 mm was prepared by subj ecting Alloys 23C to 26C to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the sliced samples and hot-rolled samples were prepared from the slabs.
  • the sliced samples were prepared by subjecting the slabs to a slicing step, while the hot-rolled samples were prepared by subjecting the slabs to a heat treatment and subsequently to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the sliced samples were further subjected to a heat treatment step in which they were held at a temperature of 350°C for 4 hours.
  • the sliced samples after these treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the tenth embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 23C and 24C correspond to examples according to the tenth embodiment of the present invention.
  • the sliced samples and hot-rolled samples after the treatments were subjected to a flatness evaluation test, an evaluation test for accuracy of plate thickness, a strength test, and an anodizability evaluation test.
  • thick plates vary depending on the type of alloy used, and the criteria for the strength were modified as follows . Specifically, samples having a tensile strength of 90 N/mm 2 or more were evaluated as having accepted strength (Accepted), whereas those having a tensile strength of less than 90 N/mm 2 were evaluated as having unaccepted strength (Failed).
  • the sample using Alloy 25C contained Mn in a content less than the lower limit in the material aluminum alloy and thereby had insufficient strength.
  • the sample using Alloy 26C contained Mn in a content of more than the upper limit in the material aluminum alloy, thereby caused coarse intermetallic compounds, and suffered from unevenness in its appearance of surface after anodization.
  • the samples using Alloys 23C to 26C didnot suffer from unevenness in their appearances of cross sections after anodization.
  • the sample using Alloy 25C contained Mn in a content of less than the lower limit in the material aluminum alloy and was thereby somewhat inferior in strength to the other hot-rolled samples.
  • the sample using Alloy 26C contained Mn in a content of more than the upper limit in the material aluminum alloy, thereby caused coarse intermetallic compounds, and suffered from unevenness in its appearance of surface after anodization.
  • the samples using Alloys 23C to 26C suffered from unevenness in their appearances of cross sections after anodization.
  • This experimental example relates to the eleventh embodiment of the present invention.
  • the experimental example used 6000 series Al-Mg-Si alloys as the aluminum alloys.
  • a series of slabs having a plate thickness of 500 mm was prepared by subj ecting Alloys 27C to 32C to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the sliced samples and hot-rolled samples were prepared from the slabs.
  • the sliced samples were prepared by subjecting the slabs to a slicing step, while the hot-rolled samples were prepared by subj ecting the slabs to a heat treatment and subsequently to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the sliced samples were further subjected to a heat treatment step in which they were held at a temperature of 350°C for 4 hours.
  • the resulting sliced samples and hot-rolled samples were further subjected to a solution treatment at 520°C and subsequently to an aging treatment at 175°C for 8 hours.
  • the sliced samples after these treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the eleventh embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 27C and 28C correspond to examples according to the eleventh embodiment of the present invention.
  • thick plates vary depending on the type of alloy used, and the criteria for the strength were modified as follows . Specifically, samples having a tensile strength of 200 N/mm 2 or more were evaluated as having accepted strength (Accepted) ; while those having a tensile strength of less than 200 N/mm 2 were evaluated as having unaccepted strength (Failed).
  • the samples using Alloys 29C and 31C contained Si and Mg, respectively, in a content of less than its lower limit in the material aluminum alloy and showed insufficient strength.
  • the sample using Alloy 30C contained Si in a content of more than the upper limit in the material aluminum alloy, caused coarse intermetallic compounds, and suffered from unevenness in their appearances of surfaces after anodization.
  • the sample using Alloy 32C contained Mg in a content of more than the upper limit in the material aluminum alloy, and advantages obtained therefrom were saturated, resulting in inferior economical efficiency.
  • the samples using Alloys 27C to 32C did not suffer from unevenness in their appearances of cross sections after anodization.
  • the samples using Alloys 29C and 31C contain Si and Mg, respectively, in a content of less than the lower limit in the material aluminum alloy, and showed insufficient strength.
  • the sample using Alloy 30C contained Si in a content of more than the upper limit in the material aluminum alloy, caused coarse intermetallic compounds, and suffered from unevenness in their appearances of surfaces after anodization.
  • the sample using Alloy 32C contained Mg in a content of more than the upper limit in the material aluminum alloy, and advantages obtained therefrom were .saturated, resulting in inferior economical efficiency.
  • the samples using Alloy 27C to 32C suffered from unevenness in their appearances of cross sections after anodization.
  • This experimental example relates to the twelfth embodiment of the present invention.
  • the experimental example used 7000 series Al-Zn-Mg alloys as the aluminum alloys.
  • a series of slabs having a plate thickness of 500 mm was prepared by subj ecting Alloys 33C to 38C to a melting step, a hydrogen gas removal step, a filtration step, and a casting step sequentially in this order.
  • the sliced samples and hot-rolled samples were prepared from the slabs.
  • the sliced samples were prepared by subjecting the slabs to a slicing step, while the hot-rolled samples were prepared by subjecting the slabs to a heat treatment and subsequently to hot rolling.
  • the sliced samples and hot-rolled samples are aluminum alloy thick plates each 20 mm thick, 1000 mm wide, and 2000 mm long.
  • the sliced samples were further subjected to a heat treatment step in which they were held at a temperature of 300°C for 4 hours.
  • the resulting sliced samples and hot-rolled samples were further subjected to a solution treatment at 470°C and subsequently to an aging treatment at 120°C for 48 hours.
  • the sliced samples after these treatments are aluminum alloy thick plates manufactured by the procedures of the manufacturing method according to the twelfth embodiment of the present invention, whereas the hot-rolled samples after the treatments are not.
  • the sliced samples using Alloys 33C and 34C correspond to examples according to the twelfth embodiment of the present invention.
  • thick plates vary depending on the type of alloy used, and the criteria for the strength were modified as follows . Specifically, samples having a tensile strength of 250 N/mm 2 or more were evaluated as having accepted strength (Accepted) ; while those having a tensile strength of less than 250 N/mm 2 were evaluated as having unaccepted strength (Failed).
  • the samples using Alloys 35C and 37C contained Mg and Zn, respectively, in a content of less than the lower limit in the material aluminum alloy, and showed insufficient strength.
  • the samples using Alloys 36C and 38C contained Mg and Zn, respectively, in a content of more than the upper limit in the material aluminum alloy, and thereby suffered from unevenness in their appearances of surfaces after anodization.
  • the samples using Alloys 33C to 38C did not suffer from unevenness in their appearances of cross sections after anodization.
  • the samples using Alloys 35C and 37C contained Mg and Zn, respectively, in a content of less than the lower limit in the material aluminum alloy, and thereby showed insufficient strength.
  • the samples using Alloys 36C and 38C contained Mg and Zn, respectively, in a content of more than the upper limit in the material aluminum alloy and thereby suffered from unevenness in their appearances of surfaces after anodization.
  • Methods for manufacturing aluminum alloy thick plates show superior productivity, can easily control the surface condition and flatness to improve the accuracy of plate thickness, and are thereby industrially very useful.

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Claims (21)

  1. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Mg dans une teneur de 1,5 pour-cent en masse ou plus et de 12,0 pour-cent en masse ou moins, et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Si dans une teneur de 0,7 pour-cent en masse ou moins, en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 0,6 pour-cent en masse ou moins, en Mn dans une teneur de 1,0 pour-cent en masse ou moins, en Cr dans une teneur de 0,5 pour-cent en masse ou moins, en Zn dans une teneur de 0,4 pour-cent en masse ou moins, en Ti dans une teneur de 0,1 pour-cent en masse ou moins et de Zr dans une teneur de 0,3 pour-cent en masse ou moins, le restant étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant, dans l'ordre suivant:
    une étape de fusion où l'on fond l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de tranchage où l'on tranche la tôle en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée; et
    une étape de traitement thermique où l'on traite thermiquement l'épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée en maintenant celle-ci à une température de 400°C ou supérieure, mais inférieure à son point de fusion pendant une heure ou plus.
  2. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Mn dans une teneur de 0,3 pour-cent en masse ou plus et de 1,6 pour-cent en masse ou moins, et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Si dans une teneur de 0,7 pour-cent en masse ou moins, en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 0,5 pour-cent en masse ou moins, en Mg dans une teneur de 1,5 pour-cent en masse ou moins, en Cr dans une teneur de 0,3 pour-cent en masse ou moins, en Zn dans une teneur de 0,4 pour-cent en masse ou moins, en Ti dans une teneur de 0,1 pour-cent en masse ou moins et de Zr dans une teneur de 0,3 pour-cent en masse ou moins, le reste étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de tranchage où l'on tranche la tôle en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée; et
    une étape de traitement thermique où l'on traite thermiquement l'épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée en maintenant celle-ci à une température de 400°C ou supérieure, mais inférieure à son point de fusion pendant une heure ou plus.
  3. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Si dans une teneur de 0,2 pour-cent en masse ou plus et de 1,6 pour-cent en masse ou moins et du Mg dans une teneur de 0,3 pour-cent en masse ou plus et 1,5 pour-cent en masse ou moins et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 1,0 pour-cent en masse ou moins, en Mn dans une teneur de 0,6 pour-cent en masse ou moins, en Cr dans une teneur de 0,5 pour-cent en masse ou moins, en Zn dans une teneur de 0,4 pour-cent en masse ou moins, Ti dans une teneur de 0,1 pour-cent en masse ou moins et Zr dans une teneur de 0,3 pour-cent en masse ou moins, le reste étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de tranchage où l'on tranche la tôle en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée; et
    une étape de traitement thermique où l'on traite thermiquement l'épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée en maintenant celle-ci à une température de 400°C ou supérieure, mais inférieure à son point de fusion pendant une heure ou plus.
  4. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Mg dans une teneur de 0,4 pour-cent en masse ou plus et 4,0 pour-cent en masse ou moins et du Zn dans une teneur de 3,0 pour-cent en masse ou plus et 9,0 pour-cent en masse ou moins, et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Si dans une teneur de 0,7 pour-cent en masse ou moins, en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 3,0 pour-cent en masse ou moins, Mn dans une teneur de 0,8 pour-cent en masse ou moins, Cr dans une teneur de 0,5 pour-cent en masse ou moins, Ti dans une teneur de 0,1 pour-cent en masse ou moins et Zr dans une teneur de 0,25 pour-cent en masse ou moins, le reste étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de tranchage où l'on tranche la tôle en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée; et
    une étape de traitement thermique où l'on traite thermiquement l'épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée en maintenant celle-ci à une température de 350°C ou supérieure, mais inférieure à son point de fusion pendant une heure ou plus.
  5. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium, selon l'une quelconque des revendications 1 à 4, comprenant en outre, après l'étape de traitement thermique, une étape de traitement de lissage superficiel où l'on soumet la surface de l'épaisse plaque en alliage d'aluminium à un traitement de lissage superficiel.
  6. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium selon la revendication 5, dans lequel on effectue le traitement de lissage superficiel par au moins un processus sélectionné parmi le groupe consistant en découpage, broyage et polissage.
  7. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium, selon l'une quelconque des revendications 1 à 4, dans lequel l'étape de tranchage comprend l'élimination d'une partie centrale dans le sens de l'épaisseur de la tôle, la partie centrale ayant deux épaisseurs substantiellement identiques dans le sens de l'épaisseur depuis le centre du sens de l'épaisseur jusqu'aux deux surfaces de la partie centrale, respectivement et ayant une épaisseur totale allant d'un trentième à un cinquième de l'épaisseur T de la tôle (T/30 à T/5).
  8. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Mg dans une teneur de 1,5 pour-cent en masse ou plus et 12,0 pour-cent en masse ou moins, et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Si dans une teneur de 0,7 pour-cent en masse ou moins, en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 0,6 pour-cent en masse ou moins, en Mn dans une teneur de 1,0 pour-cent en masse ou moins, en Cr dans une teneur de 0,5 pour-cent en masse ou moins, en Zn dans une teneur de 0,4 pour-cent en masse ou moins, en Ti dans une teneur de 0,1 pour-cent en masse ou moins et de Zr dans une teneur de 0,3 pour-cent en masse ou moins, le reste étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de traitement thermique où l'on traite thermiquement la tôle en maintenant celle-ci à une température de 200°C à 350°C pendant une heure ou plus; et
    une étape de tranchage où l'on tranche la tôle traitée thermiquement en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée.
  9. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    cl't alliage d'aluminium contenant du Mn dans une teneur de 0,3 pour-cent en masse ou plus et 1,6 pour-cent en masse ou moins, et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Si dans une teneur de 0,7 pour-cent en masse ou moins, en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 0,5 pour-cent en masse ou moins, en Mg dans une teneur de 1,5 pour-cent en masse ou moins, en Cr dans une teneur de 0,3 pour-cent en masse ou moins, en Zn dans une teneur de 0,4 pour-cent en masse ou moins, en Ti dans une teneur de 0,1 pour-cent en masse ou moins et en Zr dans une teneur de 0,3 pour-cent en masse ou moins, le reste étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de traitement thermique où l'on traite thermiquement la tôle en la maintenant à une température de 200°C à 350°C pendant une heure ou plus; et
    une étape de tranchage où l'on tranche la tôle traitée thermiquement en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée.
  10. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Si dans une teneur de 0,2 pour-cent en masse ou plus et 1,6 pour-cent en masse ou moins et du Mg dans une teneur de 0,3 pour-cent en masse ou plus et 1,5 pour-cent en masse ou moins et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 1,0 pour-cent en masse ou moins, en Mn dans une teneur de 0,6 pour-cent en masse ou moins, en Cr dans une teneur de 0,5 pour-cent en masse ou moins, Zn dans une teneur de 0,4 pour-cent en masse ou moins, Ti dans une teneur de 0,1 pour-cent en masse ou moins et Zr dans une teneur de 0,3 pour-cent en masse ou moins, le reste étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de traitement thermique où l'on traite thermiquement la tôle en la maintenant à une température de 200°C ou supérieure mais inférieure à 400°C pendant une heure ou plus; et
    une étape de tranchage où l'on tranche la tôle traitée thermiquement en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée.
  11. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Mg dans une teneur de 0,4 pour-cent en masse ou plus et 4,0 pour-cent en masse ou moins et du Zn dans une teneur de 3,0 pour-cent en masse ou plus et 9,0 pour-cent en masse ou moins, et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Si dans une teneur de 0,7 pour-cent en masse ou moins, en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 3,0 pour-cent en masse ou moins, Mn dans une teneur de 0,8 pour-cent en masse ou moins, Cr dans une teneur de 0,5 pour-cent en masse ou moins, Ti dans une teneur de 0,1 pour-cent en masse ou moins et Zr dans une teneur de 0,25 pour-cent en masse ou moins, le reste étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de traitement thermique où l'on traite thermiquement la tôle en la maintenant à une température de 200°C ou supérieure mais inférieure à 350°C pendant une heure ou plus; et
    une étape de tranchage où l'on tranche la tôle traitée thermiquement en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée.
  12. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium, selon l'une quelconque des revendications 8 à 11, comprenant en outre, après l'étape de découpage, une étape de traitement de lissage superficiel où l'on soumet la surface de l'épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée à un traitement de lissage superficiel.
  13. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium selon la revendication 12, dans lequel on effectue le traitement de lissage superficiel par au moins un processus sélectionné parmi le groupe consistant en découpage, broyage et polissage.
  14. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium selon l'une quelconque des revendications 8 à 11, dans lequel l'étape de découpage comprend l'élimination d'une partie centrale dans le sens de l'épaisseur de la tôle, la partie centrale ayant deux épaisseurs substantiellement identiques dans le sens de l'épaisseur depuis le centre du sens de l'épaisseur jusqu'aux deux surfaces de la partie centrale, respectivement et ayant une épaisseur totale allant d'un trentième à un cinquième de l'épaisseur T de la tôle (T/30 à T/5).
  15. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Mg dans une teneur de 1,5 pour-cent en masse ou plus et de 12,0 pour-cent en masse ou moins, et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Si dans une teneur de 0,7 pour-cent en masse ou moins, en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 0,6 pour-cent en masse ou moins, en Mn dans une teneur de 1,0 pour-cent en masse ou moins, en Cr dans une teneur de 0,5 pour-cent en masse ou moins, en Zn dans une teneur de 0,4 pour-cent en masse ou moins, en Ti dans une teneur de 0,1 pour-cent en masse ou moins et de Zr dans une teneur de 0,3 pour-cent en masse ou moins, le restant étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de tranchage où l'on tranche la tôle en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée; et
    une étape de traitement thermique où l'on traite thermiquement l'épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée en maintenant celle-ci à une température de 200°C ou supérieure mais inférieure à 400°C pendant une heure ou plus.
  16. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Mn dans une teneur de 0,3 pour-cent en masse ou plus et 1,6 pour-cent en masse ou moins, et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Si dans une teneur de 0,7 pour-cent en masse ou moins, en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 0,5 pour-cent en masse ou moins, en Mg dans une teneur de 1,5 pour-cent en masse ou moins, en Cr dans une teneur de 0,3 pour-cent en masse ou moins, en Zn dans une teneur de 0,4 pour-cent en masse ou moins, en Ti dans une teneur de 0,1 pour-cent en masse ou moins et de Zr dans une teneur de 0,3 pour-cent en masse ou moins, le reste étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de tranchage où l'on tranche la tôle en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée; et
    une étape de traitement thermique où l'on traite thermiquement l'épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée en maintenant celle-ci à une température de 200°C ou supérieure mais inférieure à 400°C pendant une heure ou plus.
  17. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Si dans une teneur de 0,2 pour-cent en masse ou plus et 1,6 pour-cent en masse ou moins et du Mg dans une teneur de 0,3 pour-cent en masse ou plus et 1,5 pour-cent en masse ou moins et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 1,0 pour-cent en masse ou moins, en Mn dans une teneur de 0,6 pour-cent en masse ou moins, en Cr dans une teneur de 0,5 pour-cent en masse ou moins, Zn dans une teneur de 0,4 pour-cent en masse ou moins, Ti dans une teneur de 0,1 pour-cent en masse ou moins et Zr dans une teneur de 0,3 pour-cent en masse ou moins, le reste étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de tranchage où l'on tranche la tôle en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée; et
    une étape de traitement thermique où l'on traite thermiquement l'épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée en maintenant celle-ci à une température de 200°C ou supérieure mais inférieure à 400°C pendant une heure ou plus.
  18. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium à partir d'un alliage d'aluminium,
    l'alliage d'aluminium contenant du Mg dans une teneur de 0,4 pour-cent en masse ou plus et 4,0 pour-cent en masse ou moins et du Zn dans une teneur de 3,0 pour-cent en masse ou plus et 9,0 pour-cent en masse ou moins, et contenant en outre au moins un élément sélectionné parmi le groupe consistant en Si dans une teneur de 0,7 pour-cent en masse ou moins, en Fe dans une teneur de 0,8 pour-cent en masse ou moins, en Cu dans une teneur de 3,0 pour-cent en masse ou moins, Mn dans une teneur de 0,8 pour-cent en masse ou moins, Cr dans une teneur de 0,5 pour-cent en masse ou moins, Ti dans une teneur de 0,1 pour-cent en masse ou moins et Zr dans une teneur de 0,25 pour-cent en masse ou moins, le reste étant de l'aluminium et des impuretés inévitables,
    le procédé comprenant dans l'ordre suivant:
    une étape de fusion où l'on fait fondre l'alliage d'aluminium;
    une étape d'élimination de l'hydrogène gazeux où l'on élimine l'hydrogène gazeux de l'alliage d'aluminium en fusion;
    une étape de filtration où l'on filtre l'alliage d'aluminium, duquel l'hydrogène gazeux a été éliminé, pour éliminer des inclusions provenant de l'alliage d'aluminium;
    une étape de coulage où l'on coule l'alliage d'aluminium, duquel les inclusions ont été éliminées, en une tôle;
    une étape de tranchage où l'on tranche la tôle en une épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée;
    une étape de traitement thermique où l'on traite thermiquement l'épaisse plaque en alliage d'aluminium présentant une épaisseur prédéterminée en maintenant celle-ci à une température de 200°C ou supérieure mais inférieure à 350°C pendant une heure ou plus.
  19. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium, selon l'une quelconque des revendications 15 à 18, comprenant en outre, après l'étape de traitement thermique, une étape de traitement de lissage superficiel où l'on soumet la surface de l'épaisse plaque en alliage d'aluminium à un traitement de lissage superficiel.
  20. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium selon la revendication 19, dans lequel on effectue le traitement de lissage superficiel par au moins un processus sélectionné parmi le groupe consistant en découpage, broyage et polissage.
  21. Procédé de fabrication d'une épaisse plaque en alliage d'aluminium,
    selon l'une quelconque des revendications 15 à 18, l'étape de découpage comprenant l'élimination d'une partie centrale dans le sens de l'épaisseur de la tôle, la partie centrale ayant deux épaisseurs substantiellement identiques dans le sens de l'épaisseur depuis le centre du sens de l'épaisseur jusqu'aux deux surfaces de la partie centrale, respectivement et ayant une épaisseur totale allant d'un trentième à un cinquième de l'épaisseur T de la tôle (T/30 à T/5).
EP08722912.6A 2007-03-30 2008-03-27 Procédé de fabrication d'une plaque épaisse d'alliage d'aluminium Active EP2130931B2 (fr)

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JP2007098495A JP4242429B2 (ja) 2007-04-04 2007-04-04 アルミニウム合金厚板の製造方法およびアルミニウム合金厚板
PCT/JP2008/055873 WO2008123355A1 (fr) 2007-03-30 2008-03-27 Procédé de fabrication d'une plaque épaisse d'alliage d'aluminium et plaque épaisse d'alliage d'aluminium

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ANONYMOUS: "АЛЮМИНИЙ И СПЛАВЫ АЛЮМИНИЕВЫЕ ДЕФОРМИРУЕМЫЕ Марки /Aluminium and Wrought Aluminium Alloys.Grades", ГОСТ 4784 97, 1997, pages i-iii,1 - 11, XP055713794
CATRIN KAMMER: "Aluminium Handbook Volume 1: Fundamentals and Materials ,", 1999, ALUMINIUM VERLAG, article "6.4 Full annealing, stabilisation", pages: 250 - 251, XP055713803
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J. D. ROBSON ET AL.: "Dispersoid precipitation and process modelling in zirconium containing commercial aluminium alloys", ACTA MATER, vol. 49, 2001, pages 599 - 613, XP055713767
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WILLIAM G. WOOD: "Metals Handbook Ninth Edition Volume 5 Surface Cleaning, Finishing, and Coating,", 1982, ASM INTERNATIONAL, article "Aluminium", pages: 585 - 591, XP055713814

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KR20090117951A (ko) 2009-11-16
KR101197952B1 (ko) 2012-11-05
EP2130931B2 (fr) 2022-08-03
KR20110118186A (ko) 2011-10-28
EP2130931A4 (fr) 2011-03-23
EP2130931A1 (fr) 2009-12-09
TW200900512A (en) 2009-01-01
TWI468527B (zh) 2015-01-11

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