WO2009119724A1 - アルミニウム合金厚板およびその製造方法 - Google Patents

アルミニウム合金厚板およびその製造方法 Download PDF

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WO2009119724A1
WO2009119724A1 PCT/JP2009/056089 JP2009056089W WO2009119724A1 WO 2009119724 A1 WO2009119724 A1 WO 2009119724A1 JP 2009056089 W JP2009056089 W JP 2009056089W WO 2009119724 A1 WO2009119724 A1 WO 2009119724A1
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mass
aluminum alloy
less
thick plate
hot
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PCT/JP2009/056089
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English (en)
French (fr)
Japanese (ja)
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一徳 小林
友晴 加藤
隆 稲葉
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株式会社神戸製鋼所
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Priority to KR1020107021535A priority Critical patent/KR101251235B1/ko
Priority to EP09726074A priority patent/EP2263811A4/de
Priority to CN200980106340XA priority patent/CN101959625A/zh
Publication of WO2009119724A1 publication Critical patent/WO2009119724A1/ja

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    • 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
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B21/00—Obtaining aluminium
    • C22B21/06—Obtaining aluminium refining
    • 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
    • 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
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B2003/001—Aluminium or its alloys

Definitions

  • the present invention relates to an aluminum alloy thick plate and a manufacturing method thereof.
  • aluminum alloy materials are used in various applications such as electric and electronic parts, manufacturing equipment, daily necessities, and machine parts, in addition to semiconductor-related devices such as base substrates, transfer devices, and vacuum device chambers.
  • semiconductor-related devices such as base substrates, transfer devices, and vacuum device chambers.
  • a mold material used for a press mold steel, cast steel or the like is used for mass production, but a zinc alloy cast material, an aluminum alloy cast material or the like is used for trial production.
  • expanded materials such as aluminum alloy rolled materials or forged materials have become widespread for medium and small volume production due to the tendency to reduce the number of products.
  • the rolled material of the aluminum alloy is manufactured from the melting step S101 through the annealing step S600, and then inspected for distortion, plate thickness, surface flaws, etc. (See Kokai 2006-281348) and then covering the front and back surfaces of the roll with a resin film made of vinyl chloride or polyethylene (for example, Kobe Steel Technical Report / Vol.52 No.2, Sep. 2002, registered trademark: ALHIGHCE, a registered trademark manufactured by Furukawa-Sky Aluminum Corp., known as HIPLATE, etc.) is applied (S101 to S900).
  • a resin film made of vinyl chloride or polyethylene for example, Kobe Steel Technical Report / Vol.52 No.2, Sep. 2002, registered trademark: ALHIGHCE, a registered trademark manufactured by Furukawa-Sky Aluminum Corp., known as HIPLATE, etc.
  • the product form that covers the front and back of the rolling with resin film is because high-precision aluminum alloy thick plates are often used as parts for precision instruments. It is because it is traded through. That is, in the cut plate wholesaler, saw cutting is performed to make a small size of a dice for precision instrument parts use, and in the vacuum chamber use, end milling is partially performed, so that the non-processed part becomes the device exterior material. Therefore, for the purpose of preventing wrinkling during such cutting, the rolled front and back surfaces of high-precision aluminum alloy thick plates are distributed in the form of products covered with a resin film.
  • This rolled material of aluminum alloy is usually manufactured by hot rolling an ingot to a predetermined thickness.
  • an aluminum alloy hot-rolled plate has a plate thickness and flatness controlled only by a rolling roll, so that it is difficult to obtain good plate thickness accuracy and flatness (particularly flatness in the rolling direction).
  • a thick oxide film is formed on the rolled surface during hot rolling, it is also difficult to control the flatness.
  • a technique is disclosed in which cold rolling is performed at a rolling reduction of 5% or less that does not accumulate strain after hot rolling to improve sheet thickness accuracy (see, for example, Patent Document 1). JP 2006-316332 A (paragraphs 0027 to 0028)
  • Patent Document 1 uses an aluminum alloy material as a thin plate having a thickness of about 1 mm.
  • the surface defects described above are not only the beauty of the appearance of the product, but also a serious quality defect that impairs the function of the product, reducing the product yield, and at the same time requires a lot of man-hours to remove this defect. It is a factor that inhibits sex. For example, a customer who uses a small size of a dice, after processing the purchased product and delivering the product, discovers wrinkles at the stage where the coated resin film is peeled off at the product delivery destination. In the vacuum chamber application, if a fine flaw is a casting cavity, it becomes a functional defect, but if the flaw is fine, it is not possible to distinguish it from a damaged flaw, and it takes time to determine the flaw factor. In short, there is a problem in that sales opportunities to end customers are missed.
  • the level of wrinkles in question has recently become higher, and a wrinkle with a depth of 8 ⁇ m or more and a circle equivalent diameter of about 0.1 mm is a problem because it can be found visually. Furthermore, it is difficult to eliminate all of the above-mentioned defects by the conventional manufacturing method. Also, mainly in vacuum chamber applications, it is rarely used as it is on the surface of the material, and alumite treatment and plating treatment are performed to improve corrosion resistance and weather resistance. In recent years, despite the fact that there is no defect in the base plate, a black streak-like shape having a length of about 3 ⁇ m in the rolling parallel direction is caused after the surface treatment as described above due to the remaining undissolved Ti-B.
  • the present invention has been made in view of the above problems, and has good plate thickness accuracy and flatness that can be produced in a semiconductor-related device such as a vacuum device chamber.
  • An object of the present invention is to provide an aluminum alloy thick plate capable of suppressing surface defects caused by the above and a method for producing the same.
  • an aluminum alloy thick plate according to the present invention is an aluminum alloy thick plate obtained by smoothing the surface of an aluminum alloy hot-rolled plate, and the flatness of the surface per 1 m of the length in the rolling direction. It is 0.2 mm or less, and the variation in plate thickness is within ⁇ 0.5% of the desired plate thickness.
  • the variation in the surface flatness and the plate thickness is limited to a predetermined range, so that the semiconductor-related apparatus is not subjected to thinning processing such as cold rolling.
  • thinning processing such as cold rolling.
  • an aluminum alloy material for products requiring high accuracy in shape can be used. Furthermore, it is possible to suppress surface defects caused by wrinkles and black stripes.
  • the aluminum alloy thick plate contains Mg: 1.5 to 12.0% by mass, Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.6 1 mass% or less, Mn: 1.0 mass% or less, Cr: 0.5 mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, and the remainder is It consists of Al and inevitable impurities.
  • the aluminum alloy thick plate contains Mn: 0.3 to 1.6% by mass, Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.5% 1 mass% or less, Mg: 1.5 mass% or less, Cr: 0.3 mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, and the balance is It consists of an aluminum alloy consisting of Al and inevitable impurities.
  • the aluminum alloy thick plate contains Mg: 0.3 to 1.5% by mass, Si: 0.2 to 1.6% by mass, Fe: 0.8% by mass or less, Cu: 1.0% by mass or less, Mn: 0.6% by mass or less, Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less
  • the balance is made of an aluminum alloy composed of Al and inevitable impurities.
  • the aluminum alloy thick plate contains Zn: 3.0 to 9.0 mass%, Mg: 0.4 to 4.0 mass%, Si: 0.7 mass% or less, Fe: 0.8 mass% or less, Cu: 3.0 mass% or less, Mn: 0.8 mass% or less, Cr: 0.5 mass% or less, Ti: 0.1 mass% or less, Zr: 0.25 mass% It consists of an aluminum alloy containing at least one of the following, the balance being Al and inevitable impurities.
  • the manufacturing method of the aluminum alloy thick plate which concerns on this invention is a manufacturing method of the aluminum alloy thick plate of Claim 1, Comprising: The melting process which melt
  • the plate thickness accuracy and flatness can be improved. Further, surface defects due to wrinkles, black stripes, etc. can be suppressed.
  • the soaking process is performed by a heat treatment of 400 ° C. or more and less than the melting point of the aluminum alloy for 1 hour or more before the hot rolling process.
  • the structure of the ingot can be refined and homogenized by subjecting the ingot to heat treatment before hot rolling.
  • the manufacturing method of the said aluminum alloy thick board performs the annealing process which anneals the said hot-rolled board cut
  • the characteristics of a hot-rolled sheet can be improved by annealing the hot-rolled sheet.
  • the smoothing step is performed by any one or more of a cutting method, a grinding method, and a polishing method.
  • a cutting method e.g., a cutting method, a grinding method, and a polishing method.
  • the thickness accuracy and flatness of the aluminum alloy thick plate are improved. Further, surface defects due to wrinkles, black stripes, etc. can be suppressed.
  • the aluminum alloy thick plate according to the present invention even a thick plate with less plastic deformation becomes a desired plate thickness and a flat thick plate, so that it is produced in a semiconductor-related device or the like that requires an accurate shape. Preferred.
  • the surface properties of the thick plate are good.
  • properties such as strength are improved, color unevenness on the surface is suppressed, and the surface properties of the thick plate are further improved.
  • an aluminum alloy thick plate having the above-described effects can be produced with high productivity.
  • the aluminum alloy thick plate according to the present invention is an aluminum alloy hot-rolled plate (aluminum alloy hot-rolled plate) with a smoothed surface, and the flatness of the surface is 0.2 mm or less per 1 m in the rolling direction length. The variation is within ⁇ 0.5% of the desired plate thickness.
  • the aluminum alloy thick plate according to the present invention is a plate material having a plate thickness of 15 to 200 mm, but is not particularly limited, and can be appropriately changed depending on the use of the aluminum alloy thick plate.
  • each element which comprises the aluminum alloy thick plate which concerns on this invention is demonstrated.
  • the flatness of the surface of the aluminum alloy thick plate according to the present invention is 0.2 mm / m or less. Moreover, since the flatness of the surface of a hot-rolled sheet is the most inferior in a rolling direction, it is set per 1 m in the rolling direction length. Such flatness is adjusted by a smoothing process and a correction process in the manufacturing method described later.
  • the aluminum alloy thick plate according to the present invention is manufactured in a product that requires high accuracy in shape, such as a member of a semiconductor-related device, high accuracy is also required in the plate thickness. In order to meet this requirement, the variation in thickness is within ⁇ 0.5% of the desired thickness. Such plate thickness accuracy is adjusted by the smoothing process in the manufacturing method described later.
  • the aluminum alloy thick plate according to the present invention preferably has an amount of hydrogen gas contained in 100 g of 0.2 ml or less, more preferably 0.1 ml or less.
  • Hydrogen gas is generated from hydrogen in fuel, water adhering to metal, etc., and other organic substances. If a large amount of hydrogen gas is contained, it may cause pinholes or weaken the product.
  • hydrogen accumulates and concentrates at the grain boundaries near the surface of the ingot, causing blisters in the ingot and peeling of the aluminum alloy thick plate due to blisters, as well as surface defects in the thick plate.
  • the concentration of hydrogen gas in the ingot is, for example, from a sample cut out from the ingot (before soaking) and ultrasonically cleaned with alcohol and acetone.
  • the hydrogen gas concentration of the aluminum alloy thick plate was obtained by, for example, cutting a sample from the aluminum alloy thick plate, dipping in NaOH, removing the oxide film on the surface with nitric acid, and performing ultrasonic cleaning with alcohol and acetone. From the above, it can be obtained by the vacuum heating extraction volume method (LIS AO6-1993).
  • the aluminum alloy thick plate according to the present invention may be made of any aluminum alloy, but Al—Mg alloy, Al—Mn alloy, Al—Mg—Si alloy, Al—Zn—Mg.
  • a material suitable for the application can be selected from any one of the alloys.
  • each element of an example of the aluminum alloy which comprises the aluminum alloy thick plate which concerns on this invention is demonstrated.
  • the Al—Mg alloy according to the present invention that is, an aluminum alloy according to the 5000 series Al alloy contains Mg: 1.5 to 12.0% by mass, Si: 0.7% by mass or less, Fe: 0 0.8 mass% or less, Cu: 0.6 mass% or less, Mn: 1.0 mass% or less, Cr: 0.5 mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less 1 or more of them, and the balance consists of Al and inevitable impurities.
  • Mg 1.5 to 12.0% by mass
  • Mg has the effect of improving the strength of the Al—Mg alloy.
  • the Mg content is less than 1.5% by mass, this effect is small.
  • the Mg content exceeds 12.0% by mass, the castability is remarkably deteriorated and the production of the product becomes impossible. Therefore, when using an Al—Mg alloy having the above component composition, the Mg content needs to be 12.0 mass%. Therefore, the Mg content is 1.5 to 12.0% by mass.
  • Si is an element unavoidably contained in the aluminum alloy as a metal base impurity. Si has the effect of improving the strength of the aluminum alloy.
  • Si is combined with Mn and Fe to produce an Al— (Fe) — (Mn) —Si intermetallic compound during casting.
  • Si content exceeds 0.7 mass%, a coarse intermetallic compound will arise in an ingot, and it will become easy to produce a color nonuniformity in the surface appearance after an alumite process. Therefore, the Si content is 0.7% by mass or less.
  • Fe 0.8% by mass or less
  • Fe is an element unavoidably contained in the aluminum alloy as a metal base impurity. Fe has the effect of refining and stabilizing the crystal grains of the aluminum alloy and improving the strength.
  • Mn Al—Fe— (Mn) — (Si) intermetallic compound.
  • the Fe content exceeds 0.8% by mass, a coarse intermetallic compound is generated in the ingot, and color unevenness tends to occur in the surface appearance after the alumite treatment. Therefore, the Fe content is 0.8% by mass or less.
  • Cu 0.6% by mass or less
  • Cu has the effect of improving the strength by dissolving in an aluminum alloy.
  • the strength for use as an Al—Mg alloy thick plate is sufficiently secured when the Cu content is 0.6% by mass, and the effect is saturated even if it is added beyond that. Therefore, Cu content shall be 0.6 mass% or less.
  • Mn 1.0% by mass or less
  • Mn has the effect of improving the strength by dissolving in an aluminum alloy.
  • the Mn content exceeds 1.0% by mass, a coarse intermetallic compound is generated in the ingot, and color unevenness is likely to occur in the surface appearance after the alumite treatment. Therefore, the Mn content is 1.0% by mass or less.
  • Cr 0.5% by mass or less
  • Cr precipitates as a fine compound during casting or heat treatment, and has the effect of suppressing crystal grain growth.
  • Cr content shall be 0.5 mass% or less.
  • Zn 0.4 mass% or less
  • Zn has the effect of improving the strength of the aluminum alloy.
  • the strength for use as an Al—Mg alloy thick plate is sufficiently secured when the Zn content is 0.4% by mass, and the effect is saturated even if it is added beyond that. Therefore, Zn content shall be 0.4 mass% or less.
  • Ti 0.1% by mass or less
  • Ti has the effect of refining the crystal grains of the aluminum alloy. Even if the Ti content exceeds 0.1% by mass, the effect is saturated. Therefore, the Ti content is 0.1% by mass or less.
  • the Al—Mn alloy according to the present invention contains Mn: 0.3 to 1.6 mass%, Si: 0.7 mass% or less, Fe: 0 0.8 mass% or less, Cu: 0.5 mass% or less, Mg: 1.5 mass% or less, Cr: 0.3 mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less 1 or more of them, and the balance consists of Al and inevitable impurities.
  • Mn 0.3 to 1.6% by mass
  • Mn has the effect of improving the strength by dissolving in an aluminum alloy.
  • the Mn content is less than 0.3% by mass, this effect is small.
  • the Mn content exceeds 1.6% by mass, coarse Al— (Fe) —Mn— (Si) -based intermetallic compounds are formed. It occurs in the ingot and color unevenness tends to occur in the surface appearance after the anodized treatment. Therefore, the Mn content is set to 0.3 to 1.6% by mass.
  • Mg has the effect of improving the strength of the aluminum alloy.
  • the strength for use as an Al—Mn alloy thick plate is sufficiently secured when the Mg content is 1.5% by mass, and the effect is saturated even if it is added beyond that. Therefore, Mg content shall be 1.5 mass% or less.
  • Si 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.5% by mass or less, Cr: 0.3% by mass or less, Zn: 0.4% by mass or less, Ti: 0. 1% by mass or less. Since the effects of Si, Fe, Cu, Cr, Zn, and Ti are the same as those in the Al—Mg alloy, they are omitted.
  • the Al—Mg—Si alloy according to the present invention contains Mg: 0.3 to 1.5 mass%, Si: 0.2 to 1.6 mass%, Furthermore, Fe: 0.8 mass% or less, Cu: 1.0 mass% or less, Mn: 0.6 mass% or less, Cr: 0.5 mass% or less, Zn: 0.4 mass% or less, Ti: 0 1 or more of 1% by mass or less, with the balance being Al and inevitable impurities.
  • Mg 0.3-1.5% by mass
  • Mg has an effect of improving the strength of the aluminum alloy, and further coexists with Si to form Mg 2 Si and improve the strength of the aluminum alloy. If the Mg content is less than 0.3% by mass, these effects are small. On the other hand, when the Mg content exceeds 1.5% by mass, the characteristics of an Al—Mg-based (5000-based Al) alloy may be obtained. Therefore, the Mg content is set to 0.3 to 1.5% by mass.
  • Si 0.2-1.6% by mass
  • Si has the effect of improving the strength of the aluminum alloy, and further coexists with Mg to form Mg 2 Si and improve the strength of the aluminum alloy.
  • Si content is less than 0.2% by mass, these effects are small.
  • Si content exceeds 1.6% by mass, a coarse intermetallic compound is generated in the Al—Mg—Si based alloy, and the surface appearance after the alumite treatment tends to cause color unevenness. Therefore, the Si content is 0.2 to 1.6 mass%.
  • Cu 1.0% by mass or less
  • Cu has the effect of improving the strength by solid solution in the aluminum alloy.
  • the Cu content exceeds 1.0% by mass, the corrosion resistance of the Al—Mg—Si alloy decreases. Therefore, the Cu content is 1.0% by mass or less.
  • Zn 0.4 mass% or less
  • Zn content shall be 0.4 mass% or less.
  • Fe 0.8 mass% or less
  • Mn 0.6 mass% or less
  • Cr 0.5 mass% or less
  • Ti 0.1 mass% or less
  • the Al—Zn—Mg alloy according to the present invention contains Zn: 3.0 to 9.0% by mass, Mg: 0.4 to 4.0% by mass, Furthermore, Si: 0.7 mass% or less, Fe: 0.8 mass% or less, Cu: 3.0 mass% or less, Mn: 0.8 mass% or less, Cr: 0.5 mass% or less, Ti: 0 1 mass% or less, Zr: One or more of 0.25 mass% or less are contained, and the balance consists of Al and inevitable impurities.
  • Zn 3.0 to 9.0% by mass
  • Zn has the effect of improving the strength of the aluminum alloy.
  • the Zn content is less than 3.0% by mass, this effect is small.
  • the Zn content exceeds 9.0% by mass, a coarse intermetallic compound is produced, and the surface appearance after the alumite treatment is colored. Unevenness is likely to occur, and resistance to SCC (stress corrosion cracking) is reduced. Therefore, the Zn content is set to 3.0 to 9.0% by mass.
  • Mg 0.4-4.0% by mass
  • Mg has the effect of improving the strength of the aluminum alloy.
  • Mg content is less than 0.4% by mass, this effect is small.
  • Mg content exceeds 4.0% by mass, a coarse intermetallic compound is produced, and the surface appearance after the alumite treatment is uneven in color. It tends to occur, and the resistance to SCC (stress corrosion cracking) decreases. Therefore, the Mg content is set to 0.4 to 4.0% by mass.
  • Cu 3.0% by mass or less
  • Cu has the effect of improving the strength by solid solution in the aluminum alloy.
  • the Cu content exceeds 3.0% by mass, the corrosion resistance of the Al—Zn—Mg alloy decreases. Therefore, the Cu content is 3.0% by mass or less.
  • Zr 0.25 mass% or less
  • Zr has the effect of refining and stabilizing the crystal grains of the aluminum alloy.
  • the Zr content exceeds 0.25% by mass, a coarse intermetallic compound is produced, and color unevenness is likely to occur on the surface appearance after the alumite treatment. Therefore, the Zr content is 0.25% by mass or less.
  • Si 0.7 mass% or less, Fe: 0.8 mass% or less, Mn: 0.8 mass% or less, Cr: 0.5 mass% or less, Ti: 0.1 mass% or less
  • the contents of V, B, etc. as inevitable impurities are 0 respectively. If it is 0.01 mass% or less, it does not affect the characteristics of the aluminum alloy thick plate of the present invention.
  • Ti may be added as a refiner consisting of a master alloy with B. As will be described later, if coarse Ti-B particles remain undissolved, anodized Black streaks may occur after surface treatment such as treatment or plating. For this reason, it is preferable not to add B, such as by using an Al—Ti finer, but even if black streaks occur due to the addition of B, by performing an appropriate smoothing treatment as described later, It is possible to remove black stripes.
  • FIG. 1 is a flowchart showing a method of manufacturing an aluminum alloy thick plate according to the present invention.
  • an aluminum alloy having any one of the above compositions is melted to form a molten aluminum alloy (melting step S11), and hydrogen gas and inclusions are respectively removed from the molten aluminum alloy. (Dehydrogenation step S12, filtration step S13).
  • the molten aluminum alloy is cast to produce an ingot (casting step S14), and the ingot is hot-rolled to a predetermined thickness to produce a hot-rolled sheet (hot-rolling step S30). And a hot-rolled board is cut
  • the aluminum alloy thick plate manufactured in this way becomes a product form in which the front and back surfaces are covered with a resin film through an inspection step S80 and a resin film coating step S90.
  • finishes through resin film coating process S90 for convenience the aluminum alloy thick board which concerns on this invention is a thing of the stage which finished smoothing process S70. Details of each step will be described below.
  • the melting step S11 is a step of melting an aluminum alloy having a predetermined composition to form a molten aluminum alloy, and is performed by a known facility and method.
  • the dehydrogenation step S12 is a step of removing hydrogen gas from the molten aluminum alloy, and the hydrogen gas can be suitably removed by performing fluxing, chlorine refining, in-line refining or the like on the molten aluminum alloy. Further, if the dehydrogenation gas apparatus is a rotary dehydrogenation gas apparatus such as SNIFF or a porous plug (see Japanese Patent Application Laid-Open No. 2002-146447), the removal can be performed more suitably. it can.
  • Filtration process S13 is a process of removing mainly an oxide and a nonmetallic inclusion from aluminum alloy molten metal with a filtration apparatus.
  • the filter device is provided with a ceramic tube using alumina having a particle size of about 1 mm, for example, and the oxides and inclusions can be removed by passing molten aluminum alloy through the ceramic tube.
  • the dehydrogenation step S12 and the filtration step S13 it is possible to obtain a high-quality aluminum alloy ingot in which internal defects are suppressed in the subsequent casting step S14. Further, since deposition of oxide deposits (dross) can be suppressed, the dross removal work can be reduced.
  • the casting step S14 is a step for producing an aluminum alloy ingot by forming and solidifying a molten aluminum alloy into a predetermined shape such as a rectangular parallelepiped shape, for example, with a casting apparatus configured to include a water-cooled mold.
  • a semi-continuous casting method can be used as a casting method.
  • molten metal is poured from above into a metal water-cooled mold with an open bottom, and the solidified metal is continuously removed from the bottom of the water-cooled mold to obtain an ingot of a predetermined thickness. It is.
  • This semi-continuous casting method may be performed either vertically or horizontally.
  • Soaking process-treatment temperature 400 ° C or higher and lower than the melting point of the aluminum alloy, treatment time: 1 hour or more
  • heat treatment is performed on the aluminum alloy ingot, thereby removing internal stress, homogenizing the solute elements segregated during casting, and diffusing and dissolving the intermetallic compound crystallized during casting to form a structure.
  • This is a process for homogenization.
  • the heat treatment is performed according to a conventional method by holding at 400 ° C. or higher and lower than the melting point of the aluminum alloy for 1 hour or longer. If the soaking temperature is less than 400 ° C., the above effect is insufficient.
  • the solid solution of an intermetallic compound is inadequate and it precipitates easily.
  • the soaking temperature reaches the melting point of the aluminum alloy according to the present invention, a phenomenon called burning, in which a part of the surface of the aluminum alloy ingot is melted, causes surface defects of the aluminum alloy thick plate. It is easy to become. Therefore, the soaking temperature is 400 ° C. or higher and lower than the melting point of the aluminum alloy, and the annealing is performed for 1 hour or longer.
  • the hot rolling step S30 is a step of hot rolling an aluminum alloy ingot to obtain a plate material (aluminum alloy hot rolled plate) having a predetermined thickness.
  • a reverse (reversible) hot rolling mill can be used as the hot rolling method.
  • the aluminum alloy ingot is heated to a predetermined temperature and rolled down by a reverse hot rolling mill to produce an aluminum alloy hot rolled sheet having a predetermined thickness.
  • the plate thickness in this step (the plate thickness of the aluminum alloy hot-rolled plate) is a plate thickness obtained by adding a decrease in the smoothing step S70 described later to the desired plate thickness of the aluminum alloy thick plate. About 200 mm is preferable.
  • the correction step S40 is a step of correcting and flattening the distortion generated by hot rolling of the aluminum alloy hot-rolled sheet, and is performed by a known facility or method such as a stretcher or a tension leveler.
  • the cutting step S50 is a step of cutting the aluminum alloy hot-rolled sheet into a desired length (and width).
  • the annealing step S60 is a step of removing the internal stress or homogenizing the internal structure by applying a heat treatment to the aluminum alloy thick plate. Moreover, you may give the tempering by a solution treatment and an aging treatment. These processes may be performed after the smoothing process step S70. For example, as shown in Japanese Patent Laid-Open No. 63-115617, the flatness of the surface can be improved by heat treatment.
  • the smoothing treatment step S70 is a step of smoothing the surface (rolled surface) of the aluminum alloy hot-rolled plate and adjusting the plate thickness.
  • the removal thickness of the surface of the hot-rolled sheet is 2 to 5 mm per side.
  • a black streak-like surface defect having a length of about 3 ⁇ m in the rolling parallel direction after surface treatment such as alumite treatment or plating treatment has been carried out in recent years, even though the base plate has no defect.
  • Ti-B an ingot refiner (crystal grain refiner) at the time of casting, rapidly solidifies in the vicinity of the slab ingot mold. The inventors have found out that this is due to the fact that it was not dissolved in the part. Therefore, by setting the removal thickness to 2 mm or more, it is possible to remove the undissolved portion of the ingot refining agent Ti-B, so black streaks can be obtained even if alumite treatment or plating treatment is performed. No surface defects occur.
  • the removal thickness is 5 mm or less from the viewpoint of yield and cost performance.
  • a cutting method such as end mill cutting or diamond bite cutting, a grinding method in which the surface is ground with a grindstone, or a polishing method such as buffing polishing can be used.
  • a cutting method such as end mill cutting or diamond bite cutting, a grinding method in which the surface is ground with a grindstone, or a polishing method such as buffing polishing can be used.
  • a polishing method such as buffing polishing
  • hairline processing may be further performed.
  • a hairline process By applying a hairline process, the surface of the thick plate can be rolled.
  • a polishing method such as a belt type or a wheel type is known, but any method may be adopted, and a polishing nonwoven fabric used for a hairline processing such as a belt type or a wheel type
  • the abrasive grain type it is known that it consists of a single substance such as alumina, silicon carbide, zirconia, or a mixture thereof, and an adhesive such as resin or glue. Coarse # 120 to # 220.
  • an abrasive non-woven fabric having a rotating outer diameter of a belt or wheel of ⁇ 400 mm, it contains a grease for preventing seizure and is preferably subjected to hairline processing at a rotational speed of 1500 rpm or less, but is limited to these conditions. It is not something.
  • the size of wrinkles that can be visually recognized by the human eye is a depth of 8 ⁇ m or more, and the size of wrinkles that are difficult to determine during inspection is up to 20 ⁇ m.
  • the depth of 20 ⁇ m is an indentation caused by foreign matter or roll wrinkles, and such a defect is not originally a functional defect.
  • such indented wrinkles can be distinguished from functional defects because the smooth surface, wrinkles, and borders on the surface of the thick plate can be made smooth by applying hairline processing (2 to 3 ⁇ m in processing allowance). There is an effect that can be easily.
  • the effect of the present invention can be obtained if only 2 mm or more of hairline processing is performed per side.
  • the aluminum alloy thick plate thus manufactured is then inspected for distortion, plate thickness, surface flaws, etc. in the inspection step S80, and then the front and back surfaces are made of resin film in the resin film coating step S90. Covered.
  • Example 1 Preparation of test material
  • Al-Mg alloy Alloy No. shown in Table 1
  • An aluminum alloy having a composition of 5a to 5v (5k: JIS5052 alloy, 5l: JIS5083 alloy, 5v: no addition of Ti and B) is melted, dehydrogenated and filtered, and then cast into a casting having a thickness of 500 mm. A lump was made. This ingot was heated at 500 ° C. for 4 hours and soaked, and then hot-rolled to produce an aluminum alloy hot-rolled sheet having a thickness of about 25 mm and a thickness of about 20 mm.
  • the end mill processing was performed by modifying an end mill processing machine (milling machine) manufactured by WASSER GmbH (German machine manufacturer, GmbH is a company).
  • the rough chip was made of carbide
  • the finishing chip was made of diamond
  • the machining allowance was the amount of pressing of the disk from the zero point, and the total tip was adjusted to about 2.5 mm / side.
  • 30 rough chips and 2 finishing chips were mounted in the vicinity of the circumference of the lower surface of the disk, the disk was lowered onto the work piece, rotated, and then cut by sending it in the longitudinal direction of the plate. Since the finish chip pop-out amount is mounted so as to protrude slightly from the rough chip, the finished chip is shaped so that the surface of the rough chip cut off is followed up.
  • an aluminum plate buffing machine manufactured by Nomizu Machine Mfg. Co., Ltd. was remodeled so that a polishing nonwoven fabric wheel could be attached to the buffing roll part.
  • the wheel is made of POLITEX; manufactured by KOYO-SHA Co., Ltd. (Registered trademark) KF wheel MA (coarse (# 150), outer diameter ⁇ 400 mm, grease impregnated, using brown fused alumina as an abrasive grain type and resin bond as an adhesive) was used. Then, polishing was performed under the condition that the machining allowance was about 3.0 ⁇ m / single side (with oscillation (two reciprocations)).
  • polishing cost WHEREIN The level
  • Al-Mn alloy Al-Mn alloy Alloy No. shown in Table 1
  • An aluminum alloy having a composition of 3a to 3e (3e is not added with Ti and B) was dissolved, subjected to dehydrogenation treatment and filtration, and then cast to produce an ingot having a thickness of 500 mm.
  • This ingot was hot-rolled to produce an aluminum alloy hot-rolled sheet having a thickness of about 25 mm and a thickness of about 20 mm. After this aluminum alloy hot-rolled sheet was cut into a rolling direction length of 2000 mm ⁇ width of 1000 mm, a smoothing process was performed on the rolled surface (both sides) to obtain a 20 mm thick aluminum alloy thick plate (cut plate).
  • a Ti-B master alloy is added to prevent ingot cracking.
  • the effect of the smoothing treatment was compared by three types of methods: end milling, end milling + hairline processing (using a belt-type abrasive nonwoven fabric), and hairline processing.
  • end milling used the aluminum alloy hot-rolled sheet of about 25 mm thickness
  • hairline processing used the aluminum alloy hot-rolled sheet of about 20 mm in thickness.
  • end milling and hairline processing methods are the same as in the case of the Al—Mg alloy.
  • Example 1 Evaluation
  • the following evaluation was performed on the obtained aluminum alloy thick plate, and the results are shown in Tables 2 and 3.
  • the aluminum alloy hot-rolled board (thickness 20mm) which does not implement a smoothing process was also manufactured, and it evaluated as a comparative example. Alloy No. Since 5n could not be produced on an aluminum alloy hot-rolled sheet as will be described later, the subsequent treatment and evaluation were not performed.
  • the plate thicknesses at a total of 6 points from the four corners of the test material and from the half of the length of the side in the rolling direction to the inner 20 mm part in the width direction were measured using a micrometer. If the thickness of all six points is in the range of 20.0 ⁇ 0.06 mm (19.94 to 20.06 mm), “ ⁇ ”, 20.0 ⁇ 0.10 mm ( 20.0 mm ⁇ 0.5%, 19.90 to 20.10 mm) was evaluated as “Good” as good.
  • Alloy No. The aluminum alloy thick plate consisting of 5a to 5l and 5v has an additive element content within an appropriate range, and has been subjected to appropriate smoothing treatment on the surface, so that strength, flatness, plate thickness accuracy, And the surface properties were good. Moreover, sufficient strength and good surface properties were obtained even when compared with an aluminum alloy hot-rolled sheet that had not been smoothed. In contrast, alloy no. The aluminum alloy thick plate made of 5 m was insufficient in strength because the Mg content was insufficient. On the other hand, Alloy No. Since the aluminum alloy thick plate made of 5n has an excessive Mg content, casting cracks occurred, and the specimens could not be produced. Alloy No.
  • the aluminum alloy thick plate made of 5o, 5p, 5r, and 5s has excessive Si, Fe, Mn, and Cr contents, so that a coarse intermetallic compound is formed, and the surface appearance after the alumite treatment is uneven in color.
  • Alloy No. The aluminum alloy thick plates made of 5q, 5t, and 5u have Cu, Zn, and Ti contents exceeding the appropriate ranges, respectively. As compared with 5f, 5j, and 5c, no improvement in strength and surface properties was observed.
  • the surface properties due to wrinkles are improved in the case of end milling + hairline processing with proper removal amount or end milling only compared to hairline processing with a small amount of removal. Confirmed to do.
  • the wrinkles found in the conventional hot-rolled sheet cutting plate are identified as including fine wrinkles of a size that can barely be found with the naked eye, but with only hairline processing. The wrinkles found on the board were clearly visible. Therefore, the effect that the functional defect can be easily distinguished only by the hairline processing was confirmed.
  • the amount of removal is small, so black streaks cannot be prevented.
  • the amount of removal is appropriate, preventing black streaks. It was confirmed that it was possible.
  • the 5v aluminum alloy thick plate does not use the ingot refining agent Ti-B at the time of slab ingoting, so any surface is not affected by the difference in the surface smoothing method. It was confirmed that black stripes can be prevented from occurring even by the smoothing method.
  • the aluminum alloy thick plate made of 3a, 3b, 3e has an additive element content within an appropriate range, and has been subjected to an appropriate smoothing treatment on the surface, so that strength, flatness, plate thickness accuracy, and The surface properties were good. Moreover, sufficient strength and good surface properties were obtained even when compared with an aluminum alloy hot-rolled sheet that had not been smoothed. In contrast, alloy no. The aluminum alloy thick plate made of 3c was insufficient in Mn content, so that sufficient strength was not obtained. On the other hand, Alloy No. Since the aluminum alloy thick plate made of 3d has an excessive Mn content, a coarse intermetallic compound was formed, and the appearance of the surface after the alumite treatment was uneven in color.
  • the surface properties due to wrinkles are improved in the case of end milling + hairline processing with proper removal amount or end milling only compared to hairline processing with a small amount of removal. Confirmed to do.
  • the wrinkles found in the conventional hot-rolled sheet cutting plate are identified as including fine wrinkles of a size that can barely be found with the naked eye, but with only hairline processing. The wrinkles found on the board were clearly visible. Therefore, the effect that the functional defect can be easily distinguished only by the hairline processing was confirmed.
  • the amount of removal is small, so black streaks cannot be prevented.
  • the amount of removal is appropriate, preventing black streaks. It was confirmed that it was possible. Note that the aluminum alloy thick plate made of 3e does not use the ingot refining agent Ti-B at the time of slab ingoting, so that any surface is not affected by the difference in surface smoothing method. It was confirmed that black stripes can be prevented from occurring even by the smoothing method.
  • the aluminum alloy hot-rolled sheet that had not been smoothed had accumulated processing strain, warped in the rolling direction, and had poor flatness.
  • the plate thickness accuracy was often inferior to that of aluminum alloy thick plates having the same composition.
  • the surface properties due to wrinkles and black stripes were poor.
  • the flatness value only for hairline processing and the evaluation of the thickness accuracy of the cut plate are almost the same as the evaluation of the flatness value of the aluminum hot rolled plate (without smoothing treatment) and the thickness accuracy of the cut plate. (If the machining allowance is 2 to 3 ⁇ m, the accumulated machining strain is not reduced, so the warpage is large in the rolling direction and the flatness is poor).
  • Example 2 Preparation of test material
  • Al-Mg-Si alloy Alloy No. shown in Table 4
  • An aluminum alloy having a composition of 6a to 6g was melted, dehydrogenated, filtered, and cast to produce an ingot having a thickness of 500 mm.
  • This ingot was hot-rolled to produce an aluminum alloy hot-rolled sheet having a thickness of about 25 mm and a thickness of about 20 mm.
  • After this aluminum alloy hot-rolled sheet was cut into a rolling direction length of 2000 mm ⁇ width of 1000 mm, a smoothing process was performed on the rolled surface (both sides) to obtain a 20 mm thick aluminum alloy thick plate (cut plate).
  • a Ti-B master alloy is added to prevent ingot cracking.
  • the effect of the smoothing treatment was compared by three types of methods: end milling, end milling + hairline processing (using a belt-type abrasive nonwoven fabric), and hairline processing.
  • end milling used the aluminum alloy hot-rolled sheet of about 25 mm thickness
  • hairline processing used the aluminum alloy hot-rolled sheet of about 20 mm in thickness.
  • the end milling and hairline processing methods are the same as in the case of the Al—Mg alloy.
  • the obtained aluminum alloy thick plate was subjected to a solution treatment at 520 ° C. and an aging treatment at 175 ° C. for 8 hours.
  • Al-Zn-Mg alloy Alloy No. shown in Table 4
  • An aluminum alloy having a composition of 7a to 7g was melted, dehydrogenated and filtered, and then cast to produce an ingot having a thickness of 500 mm.
  • This ingot was hot-rolled to produce an aluminum alloy hot-rolled sheet having a thickness of about 25 mm and a thickness of about 20 mm.
  • After this aluminum alloy hot-rolled sheet was cut into a rolling direction length of 2000 mm ⁇ width of 1000 mm, a smoothing process was performed on the rolled surface (both sides) to obtain a 20 mm thick aluminum alloy thick plate (cut plate).
  • a Ti-B master alloy is added to prevent ingot cracking.
  • the effect of the smoothing treatment was compared by three types of methods: end milling, end milling + hairline processing (using a belt-type abrasive nonwoven fabric), and hairline processing.
  • end milling used the aluminum alloy hot-rolled sheet of about 25 mm thickness
  • hairline process used the aluminum alloy hot-rolled sheet of about 20 mm in thickness.
  • the end milling and hairline processing methods are the same as in the case of the Al—Mg alloy.
  • the obtained aluminum alloy thick plate was subjected to a solution treatment at 470 ° C., and an aging treatment was performed at 120 ° C. for 48 hours.
  • Example 2 Evaluation
  • the obtained aluminum alloy thick plate was evaluated for strength and surface properties in the same manner as in Example 1, and the results are shown in Tables 5 and 6.
  • the aluminum alloy hot-rolled sheet (thickness 20 mm) which does not implement a smoothing process was also manufactured, the solution treatment and the aging treatment were performed on the same conditions, and it evaluated as a comparative example.
  • the acceptance criteria for strength is alloy no. 6a to 6g (Al—Mg—Si based alloys) have a tensile strength of 200 N / mm 2 or more, alloy no. 7a to 7g (Al—Zn—Mg alloy) had a tensile strength of 250 N / mm 2 or more.
  • strength only by end mill process + hairline process and hairline process is the same as the intensity value only by end mill process, description is abbreviate
  • surface since the value of intensity
  • Alloy No. The aluminum alloy thick plates made of 6a, 6b, and 6g had good strength and surface properties because the content of additive elements was within an appropriate range and the surface was appropriately smoothed. Moreover, sufficient strength and good surface properties were obtained even when compared with an aluminum alloy hot-rolled sheet that had not been smoothed. In contrast, alloy no. The aluminum alloy thick plates made of 6c and 6e were insufficient in Si and Mg contents, so that sufficient strength was not obtained. On the other hand, Alloy No. Since the 6d aluminum alloy thick plate has an excessive Si content, a coarse intermetallic compound was formed, and the surface appearance after the alumite treatment was uneven in color. In addition, Alloy No.
  • the aluminum alloy thick plate made of 6f has the characteristics of an Al—Mg-based (5000-based Al) alloy due to the excessive Mg content, so the effect of improving the strength by solution treatment and aging treatment cannot be obtained. Alloy No. with Mg content in proper range Compared with 6a and 6b, the strength decreased.
  • the surface properties due to wrinkles are improved in the case of end milling + hairline processing with proper removal amount or end milling only compared to hairline processing with a small amount of removal. Confirmed to do.
  • the wrinkles found in the conventional hot-rolled sheet cutting plate are identified as including fine wrinkles of a size that can barely be found with the naked eye, but with only hairline processing. The wrinkles found on the board were clearly visible. Therefore, the effect that the functional defect can be easily distinguished only by the hairline processing was confirmed.
  • the amount of removal is small, so black streaks cannot be prevented.
  • the amount of removal is appropriate, preventing black streaks. It was confirmed that it was possible. Note that the aluminum alloy thick plate made of 6 g does not use Ti-B as the ingot refining agent when slab ingot, so any surface is not affected by the difference in surface smoothing method. It was confirmed that black stripes can be prevented from occurring even by the smoothing method.
  • the aluminum alloy thick plates made of 7a, 7b, and 7g had good strength and surface properties because the content of additive elements was within an appropriate range and the surface was appropriately smoothed. Moreover, sufficient strength and good surface properties were obtained even when compared with an aluminum alloy hot-rolled sheet that had not been smoothed. In contrast, alloy no.
  • the aluminum alloy thick plates made of 7c and 7e were insufficient in Mg and Zn contents, so that sufficient strength was not obtained.
  • the surface properties due to wrinkles are improved in the case of end milling + hairline processing with proper removal amount or end milling only compared to hairline processing with a small amount of removal. Confirmed to do.
  • the wrinkles found in the conventional hot-rolled sheet cutting plate are identified as including fine wrinkles of a size that can barely be found with the naked eye, but with only hairline processing. The wrinkles found on the board were clearly visible. Therefore, the effect that the functional defect can be easily distinguished only by the hairline processing was confirmed.
  • the amount of removal is small, so black streaks cannot be prevented.
  • the amount of removal is appropriate, preventing black streaks. It was confirmed that it was possible.
  • the aluminum alloy thick plate made of 7 g does not use the ingot refining agent Ti-B at the time of slab ingot formation, any surface is not affected by the difference in the surface smoothing method. It was confirmed that black stripes can be prevented from occurring even by the smoothing method.
  • the aluminum alloy thick plate according to the present invention has good flatness and plate thickness accuracy, and surface defects caused by wrinkles and black streaks are suppressed and has good surface properties. It can also be seen that by making the composition of the various alloy components appropriate, properties such as strength can be improved, color unevenness on the surface is suppressed, and surface properties are further improved.

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JP4410835B2 (ja) 2010-02-03
KR20100116698A (ko) 2010-11-01
CN101959625A (zh) 2011-01-26
KR101251235B1 (ko) 2013-04-08
TWI355301B (en) 2012-01-01

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