WO2016100800A1 - Alliage d'aluminium approprié pour la production à grande vitesse d'une bouteille en aluminium et procédé de fabrication associé - Google Patents

Alliage d'aluminium approprié pour la production à grande vitesse d'une bouteille en aluminium et procédé de fabrication associé Download PDF

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Publication number
WO2016100800A1
WO2016100800A1 PCT/US2015/066638 US2015066638W WO2016100800A1 WO 2016100800 A1 WO2016100800 A1 WO 2016100800A1 US 2015066638 W US2015066638 W US 2015066638W WO 2016100800 A1 WO2016100800 A1 WO 2016100800A1
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WIPO (PCT)
Prior art keywords
alloy
cold rolling
aluminum
aluminum alloy
impurities
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PCT/US2015/066638
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English (en)
Inventor
Johnson Go
Wei Wen
DaeHoon KANG
Jeffrey John KADILAK
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Novelis Inc.
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Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=55229830&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=WO2016100800(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Novelis Inc. filed Critical Novelis Inc.
Priority to JP2017531172A priority Critical patent/JP2018502993A/ja
Priority to CN201580068120.8A priority patent/CN107002185A/zh
Priority to KR1020177016425A priority patent/KR101988146B1/ko
Priority to BR112017010216A priority patent/BR112017010216A2/pt
Priority to EP15828603.9A priority patent/EP3234208B1/fr
Priority to CA2968894A priority patent/CA2968894A1/fr
Priority to ES15828603T priority patent/ES2797023T3/es
Priority to MX2017007895A priority patent/MX2017007895A/es
Publication of WO2016100800A1 publication Critical patent/WO2016100800A1/fr

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Classifications

    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D15/00—Casting using a mould or core of which a part significant to the process is of high thermal conductivity, e.g. chill casting; Moulds or accessories specially adapted therefor
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D7/00—Casting ingots, e.g. from ferrous metals
    • B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B65—CONVEYING; PACKING; STORING; HANDLING THIN OR FILAMENTARY MATERIAL
    • B65D—CONTAINERS FOR STORAGE OR TRANSPORT OF ARTICLES OR MATERIALS, e.g. BAGS, BARRELS, BOTTLES, BOXES, CANS, CARTONS, CRATES, DRUMS, JARS, TANKS, HOPPERS, FORWARDING CONTAINERS; ACCESSORIES, CLOSURES, OR FITTINGS THEREFOR; PACKAGING ELEMENTS; PACKAGES
    • B65D1/00—Containers having bodies formed in one piece, e.g. by casting metallic material, by moulding plastics, by blowing vitreous material, by throwing ceramic material, by moulding pulped fibrous material, by deep-drawing operations performed on sheet material
    • B65D1/02—Bottles or similar containers with necks or like restricted apertures, designed for pouring contents
    • B65D1/0207—Bottles or similar containers with necks or like restricted apertures, designed for pouring contents characterised by material, e.g. composition, physical features
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • 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
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—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

Definitions

  • the invention is related to a new aluminum alloy.
  • the invention further relates to a method of producing highly shaped aluminum products, such as bottles or cans, using the aluminum alloy.
  • the manufacturing process typically involves first producing a cylinder using a drawing and wall ironing (DWI) process.
  • DWI drawing and wall ironing
  • the resulting cylinder is then formed into a bottle shape using, for example, a sequence of full-body necking steps, blow molding, or other mechanical shaping, or a combination of these processes.
  • the demands on any alloy used in such a process or combination of processes are complex.
  • a final requirement is the ability to form the bottles at a high speed.
  • a high throughput e.g., 1000 bottles per minute
  • the shaping of the bottle must be completed in a very short time.
  • methods are needed for making preforms from the alloy at high speeds and levels of runability, such as that demonstrated by the current can body alloy AA3104.
  • AA3104 contains a high volume fraction of coarse intermetallic particles formed during casting and modified during homogenization and rolling. These particles play a major role in die cleaning during the DWI process, helping to remove any aluminum or aluminum oxide build-up on the dies, which improves both the metal surface appearance and also the runability of the sheet.
  • novel alloys that display high strain rate formability at elevated temperatures.
  • the alloys can be used for producing highly shaped aluminum products, including bottles and cans.
  • the aluminum alloy described herein comprises about 0.15-0.50 % Si, 0.35-0.65 % Fe, 0.05-0.30 % Cu, 0.60-1.10 % Mn, 0.80-1.30 % Mg, 0.000-0.0080 % Cr, 0.000-0.500 % Zn, 0.000-0.080 % Ti, up to 0.15 % of impurities, with the remainder as Al (all in weight percentage (wt. %)).
  • products e.g., bottles and cans
  • an aluminum alloy as described herein.
  • the methods include direct chill (DC) casting of an aluminum alloy as described herein to form a metal product, homogenizing the metal product, hot rolling the metal product to produce a metal sheet, cold rolling the metal sheet (e.g., with a 60 % to 90 % thickness rejection), optionally recrystallization annealing the rolled sheet, cold rolling the annealed sheet, and stabilization annealing the rolled sheet.
  • DC direct chill
  • Products e.g., bottles or cans obtained according to the methods are also provided herein.
  • Figure 1 is a scanning transmission electron microscopy (STEM) micrograph of an aluminum alloy according to an embodiment of the invention showing a substructure with average geometrically necessary boundary (GNB) spacing larger than 300 nm.
  • Figure 2 is a STEM micrograph of an aluminum alloy according to an embodiment of the invention showing a GNB-containing substructure with average GNB spacing larger than 2.5 ⁇ .
  • Figure 3 is a STEM micrograph of an aluminum alloy according to an embodiment of the invention showing a GNB-containing substructure with average GNB spacing larger than 8 ⁇ .
  • Figure 4 is a STEM micrograph of an aluminum alloy according to an embodiment of the invention showing a GNB-free substructure.
  • the following aluminum alloys are described in terms of their elemental composition in weight percentage (wt. %) based on the total weight of the alloy. In certain embodiments of each alloy, the remainder is aluminum, with a maximum wt. % of 0.15 % for the sum of the impurities.
  • the invention is related to a new aluminum alloy system for aluminum bottle applications.
  • the alloy compositions exhibit good high strain rate formability at elevated temperatures.
  • the high strain rate formability is achieved due to the elemental compositions of the alloys.
  • the invention provides highly formable alloys for use in manufacturing highly shaped cans and bottles. In one aspect, the invention provides chemistry and manufacturing processes that are optimized for the high-speed production of aluminum bottles.
  • the aluminum alloy comprises:
  • the aluminum alloy comprises:
  • the aluminum alloy comprises:
  • the aluminum alloy comprises: 0.27-0.33 wt. % Si,
  • the aluminum alloy comprises:
  • the aluminum alloy comprises:
  • the aluminum alloy comprises:
  • the aluminum alloy comprises about 0.296 wt. % Si, about 0.492 wt. % Fe, about 0.129 wt. % Cu, about 0.872 wt. % Mn, about 0.985 wt. % Mg, about 0.026 wt. % Cr, about 0.125 wt. % Zn, about 0.010 wt. Ti, up to about 0.15 wt. % impurities, with the remainder as Al.
  • the disclosed alloy includes silicon (Si) in an amount from about 0.12 % to 0.50 % (e.g., from 0.20 % to 0.40 %, from 0.22 % to 0.38 %, from 0.25 % to 0.35 %, from 0.27 % to 0.33 %, or from 0.12 % to 0.28 %) based on the total weight of the alloy.
  • Si silicon
  • the alloys can include 0.12 %, 0.13 %, 0.14 %, 0.15 %, 0.16 %, 0.17 %, 0.18 %, 0.19 %, 0.20 %, 0.21 %, 0.22 %, 0.23 %, 0.24 %, 0.25 %, 0.26 %, 0.27 %, 0.28 %, 0.29 %, 0.30 %, 0.31 %, 0.32 %, 0.33 %, 0.34 %, 0.35 %, 0.36 %, 0.37 %, 0.38 %, 0.39 %, 0.40 %, 0.41 %, 0.42 %, 0.43 %, 0.44 %, 0.45 %, 0.46 %, 0.47 %, 0.48 %, 0.49 %, or 0.50 % Si. All expressed in wt. %.
  • the alloy also includes iron (Fe) in an amount from about 0.35 % to about 0.65 % (e.g., 0.40 % to 0.60 %, from 0.42 % to 0.58 %, from 0.44 % to 0.56 %, from 0.46 % to 0.54 %, or from 0.32 % to 0.52 %) based on the total weight of the alloy.
  • Fe iron
  • the alloys can include 0.35 %, 0.36 %, 0.37 %, 0.38 %, 0.39 %, 0.40 %, 0.41 %, 0.42 %, 0.43 %, 0.44 %, 0.45 %, 0.46 %, 0.47 %, 0.48 %, 0.49 %, 0.50 %, 0.51 %, 0.52 %, 0.53 %, 0.54 %, 0.55 %, 0.56 %, 0.57 %, 0.58 %, 0.59 %, 0.60 % 0.61 %, 0.62 %, 0.63 %, 0.64 %, or 0.65 % Fe. All expressed in wt. %.
  • the disclosed alloy includes copper (Cu) in an amount from about 0.05 % to about 0.30 % (e.g., from 0.08 % to 0.20 %, from 0.10 % to 0.18 %, from 0.09 % to 0.16 %, from 0.10% to 0.16%, from 0.109 % to 0.16 %, or from 0.11 % to 0.15 %) based on the total weight of the alloy.
  • Cu copper
  • the alloys can include 0.05 %, 0.06 %, 0.07 %, 0.08 %, 0.09 %, 0.10 %, 0.11 %, 0.12 %, 0.13 %, 0.14 %, 0.15 %, 0.16 %, 0.17 %, 0.18 %, 0.19 %, 0.20 %, 0.21 %, 0.22 %, 0.23 %, 0.24 %, 0.25 %, 0.26 %, 0.27 %, 0.28 %, 0.29 %, or 0.30 % Cu. All expressed in wt. %.
  • the disclosed alloy includes manganese (Mn) in an amount from about 0.60 % to about 1.10 % (e.g., about 0.70 % to 1.00 %, from 0.75 % to 0.98 %, from 0.78 % to 0.94 %, from 0.78 % to 0.96 %, or from 0.80 % to 0.94 %, ) based on the total weight of the alloy.
  • Mn manganese
  • the alloy can include 0.60 %, 0.61 %, 0.62 %, 0.63 %, 0.64 %, 0.65 %, 0.66 %, 0.67 %, 0.68 %, 0.69 %, 0.70 %, 0.71 %, 0.72 %, 0.73 %, 0.74 %, 0.75 %, 0.76 %, 0.77 %, 0.78 %, 0.79 %, 0.80 %, 0.81 %, 0.82 %, 0.83 %, 0.84 %, 0.85 %, 0.86 %, 0.87 %, 0.88 %, 0.89 %, 0.90 %, 0.91 %, 0.92 %, 0.93 %, 0.94 %, 0.95 %, 0.96 %, 0.97 %, 0.98 %, 0.99 %, 1.00 %, 1.01 %, 1.02 %, 1.03 %, 1.04 %, 1.05 %, 1.06 %, 1.07 %, 1.08 %, 1.09
  • the disclosed alloy includes magnesium (Mg) in an amount from about 0.80 % to about 1.30 % (e.g., from 0.85 % to 1.22 %, from 0.90 % to 1.15 %, from 0.90 % to 1.10 %, or from 0.93 % to 1.07 %) based on the total weight of the alloy.
  • Mg magnesium
  • the alloy can include 0.80 %, 0.81 %, 0.82 %, 0.83 %, 0.84 %, 0.85 %, 0.86 %, 0.87 %, 0.88 %, 0.89 %, 0.90 %, 0.91 %, 0.92 %, 0.93 %, 0.94 %, 0.95 %, 0.96 %, 0.97 %, 0.98 %, 0.99 %, 1.00 %, 1.01 %, 1.02 %, 1.03 %, 1.04 %, 1.05 %, 1.06 %, 1.07 %, 1.08 %, 1.09 %, 1.10 %, 1.11 %, 1.12 %, 1.13 %, 1.14 %, 1.15 %, 1.16 %, 1.17 %, 1.18 %, 1.19 %, 1.20 %, 1.21 %, 1.22 %, 1.23 %, 1.24 %, 1.25 %, 1.26 %, 1.27 %, 1.28 %, 1.29
  • the alloy includes chromium (Cr) in an amount up to about 0.80 % (e.g., from 0 % to 0.05 %, 0 % to 0.06 %, from 0 % to 0.07 %, from 0 % to 0.08 %, from 0.03 to 0.06 %, from 0.005 % to 0.05 %, or from 0.001 % to 0.06 %) based on the total weight of the alloy.
  • Cr chromium
  • the alloy can include 0.001 %, 0.002 %, 0.003 %, 0.004 %, 0.005 %, 0.006 %, 0.007 %, 0.008 %, 0.009 %, 0.010 %, 0.011 %, 0.012 %, 0.013 %, 0.014 %, 0.015 %, 0.016 %, 0.017 %, 0.018 %, 0.019 %, 0.020 %, 0.021 %, 0.022 %, 0.023 %, 0.024 %, 0.025 %, 0.026 %, 0.027 %, 0.028 %, 0.029 %, 0.030 %, 0.031 %, 0.032 %, 0.033 %, 0.034 %, 0.035 %, 0.036 %, 0.037 %, 0.038 %, 0.039 %, 0.040 %, 0.05 %, 0.051
  • the alloy described herein includes zinc (Zn) in an amount up to about 0.5 % (e.g., from 0 % to 0.25 %, from 0 % to 0.2 %, from 0 % to 0.30 %, from 0 % to 0.40 %, from 0.01 % to 0.35 %, or from 0.01 % to 0.25 %) based on the total weight of the alloy.
  • Zn zinc
  • the alloy can include 0.001 %, 0.002 %, 0.003 %, 0.004 %, 0.005 %, 0.006 %, 0.007 %, 0.008 %, 0.009 %, 0.01 %, 0.02 %, 0.03 %, 0.04 %, 0.05 %, 0.06 %, 0.07 %, 0.08 %, 0.09 %, 0.10 %, 0.11 %, 0.12 %, 0.13 %, 0.14 %, 0.15 %, 0.16 %, 0.17 %, 0.18 %, 0.19 %, 0.20 %, 0.21 %, 0.22 %, 0.23 %, 0.24 %, 0.25 %, 0.26 %, 0.27 %, 0.28 %, 0.29 %, 0.30 %, 0.31 %, 0.32 %, 0.33 %, 0.34 %, 0.35 %, 0.36 %, 0.37 %, 0.38 %, 0.39 %, 0.
  • the alloy includes titanium (Ti) in an amount up to about 0.08 % (e.g., from 0 % to 0.05 %, 0 % to 0.06 %, from 0 % to 0.07 %, from 0.03 to 0.06 %, from 0.005 % to 0.05 %, or from 0.001 % to 0.06 %) based on the total weight of the alloy.
  • Ti titanium
  • the alloy can include 0.001 %, 0.002 %, 0.003 %, 0.004 %, 0.005 %, 0.006 %, 0.007 %, 0.008 %, 0.009 %, 0.01 %, 0.011 %, 0.012 %, 0.013 %, 0.014 %, 0.015 %, 0.016 %, 0.017 %, 0.018 %, 0.019 %, 0.02 %, 0.021 %, 0.022 %, 0.023 %, 0.024 %, 0.025 %, 0.026 %, 0.027 %, 0.028 %, 0.029 %, 0.03 %, 0.031 %, 0.032 %, 0.033 %, 0.034 %, 0.035 %, 0.036 %, 0.037 %, 0.038 %, 0.039 %, 0.04 %, 0.05 %, 0.051 %,
  • the alloy compositions can further include other minor elements, sometimes referred to as impurities, in amounts of about 0.15 % or below, 0.14 % or below, 0.13 % or below, 0.12 % or below, 0.11 % or below, 0.10 % or below, 0.09 % or below, 0.08 % or below, 0.07 % or below, 0.06 % or below, 0.05 % or below, 0.04 % or below, 0.03 % or below, 0.02 % or below, or 0.01 % or below.
  • impurities may include, but are not limited to, V, Ga, Ni, Sc, Zr, Ca, Hf, Sr, or combinations thereof.
  • the alloy composition comprises only unavoidable impurities.
  • the remaining percentage of the alloy is aluminum. All expressed in wt. %.
  • the aluminum alloys of the present invention display one or more of the following properties: very low earing (maximum mean earing level of 3 %); high recycled content (e.g., at least 60 %, 65 %, 70 %, 75 %, 80 %, 82 % or 85 %); yield strength 25-36 ksi; excellent die cleaning performance which allows the application of very low die striping pressure; excellent formability which allows extensive neck shaping progression without fracture; excellent surface finished in the final bottles with no visible markings; excellent coating adhesion; high strength to meet the typical axial load (>300 lbs) and dome reversal pressure (>90 psi); overall scrap rate of the bottle making process can be as low as less than 1 %.
  • the substructure of the aluminum alloy coil made by this method has a geometrically necessary boundary (G B)-free substructure.
  • the substructure has a G B-containing substructure with an average G B spacing larger than 10 microns.
  • the substructure aluminum alloy coil made by this method has a GNB-containing substructure with average GNB spacing larger than 300 nm (e.g., FIG. 1), average GNB spacing larger than 2.5 ⁇ (FIG. 2), average GNB spacing larger than 8 ⁇ (e.g., FIG. 3), or a GNB-free substructure (e.g., FIG. 4).
  • the alloy sheet has very low earing.
  • the earing balance from the edge, sides, and center (over the coil width) is less than 1.5 % (e.g., less than 1.25 %, less than 1 %).
  • the mean earing is less than 4 %.
  • the mean earing is less than 3.75 %, less than 3.5 %, less than 3.25 %, less than 3 %, less than 2.75 %, or less than 2.5 %.
  • the alloy sheet has high recycled content.
  • the disclosed alloy composition is a product of a disclosed method.
  • aluminum alloy properties are partially determined by the formation of microstructures during the alloy's preparation.
  • the method of preparation for an alloy composition may influence or even determine whether the alloy will have properties adequate for a desired application.
  • the invention sets forth a method of making an aluminum alloy described herein.
  • can body stocks are provided to the customer in the HI 9 temper.
  • the typical H19 temper does not work well as H19 alloys are too brittle.
  • an inventive alloy must be processed in a different way, by direct chill (DC) casting, homogenizing, hot rolling, cold rolling, recrystallization annealing, cold rolling, and stabilization annealing.
  • the method of making an aluminum alloy as described herein comprises the sequential steps of:
  • the method of making the aluminum alloy as described herein comprises the sequential steps of:
  • the method of making an aluminum alloy as described herein comprises direct chill casting an aluminum ingot; homogenizing the ingot; hot rolling the homogenized ingot to form a hot rolled product; cold rolling the hot rolled product in a first cold rolling step to produce a first cold rolled product, wherein the first cold rolling step produces an about 60-90 % thickness reduction.
  • the method further comprises cold rolling the first cold rolled product in a second cold rolling step to produce a second cold rolled product, wherein the second cold rolling step produces an about 15-30 % thickness reduction.
  • the method further comprises recrystallization annealing the first cold rolled product, wherein the recrystallization annealing is at a metal temperature from about 290-500 °C for about 0.5-4 hrs. In certain embodiments, the recrystallization annealing is at a metal temperature from about 300-450 °C. In certain embodiments, the recrystallization annealing is for about 1-2 hrs.
  • the method further comprises stabilization annealing of the first cold rolled product if one cold rolling step is used or stabilization annealing of the second cold rolled product if two cold rolling steps are used, wherein the stabilization annealing is at a metal temperature from about 100-300 °C for about 0.5-4 hrs. In certain embodiments, the stabilization annealing is at a metal temperature of from about 120-250 °C. In certain embodiments, the stabilization annealing is for about 1-2 hrs. In certain embodiments where the alloy has a composition including about 0.25-0.35 wt. % Si, about 0.44-0.56 wt. % Fe, about 0.09-0.160 wt.
  • the method of making an aluminum alloy as described herein comprises direct chill casting an aluminum ingot; homogenizing the ingot; hot rolling the ingot to form a hot rolled product; cold rolling the hot rolled product to form a cold rolled product, wherein the cold rolling produces an about 60-90 % thickness reduction; and stabilization annealing of the cold rolled product, wherein the stabilization annealing is at a metal temperature from about 100-300 °C for about 0.5-4 hrs. In certain embodiments the stabilization annealing is at a metal temperature of 120-250 °C. In certain embodiments the stabilization annealing is for about 1-2 hrs.
  • the alloy has a composition including about 0.12-0.28 wt. % Si, about 0.32-0.52 wt. % Fe, about 0.09-0.16 wt. % Cu, about 0.78-0.96 wt. % Mn, about 0.90-1.10 wt. % Mg, about 0.000-0.050 wt. % Cr, about 0.000-0.250 wt. % Zn, about 0.000-0.050 wt. % Ti, and up to 0.15 wt.
  • the method of making an aluminum alloy as described herein comprises direct chill casting an aluminum ingot; homogenizing the ingot; hot rolling the ingot to form a hot rolled product; cold rolling the hot rolled product in a first cold rolling step, wherein the cold rolling produces an about 60-90 % thickness reduction in the hot rolled product; recrystallization annealing of the cold rolled product, wherein the recrystallization annealing is at a metal temperature from about 290-500 °C for about 0.5-4 hrs; cold rolling the annealed product in a second cold rolling step to produce a second cold rolled product, wherein the second cold rolling step produces an about 15-30 % thickness reduction in the annealed product; and stabilization annealing of the cold rolled product, wherein the stabilization annealing is at a metal temperature from about 100-300 °C for about 0.5-4 hrs.
  • the recrystallization annealing is at a metal temperature from about 300 to 450 °C. In certain embodiments, the recrystallization annealing is for about 1-2 hrs. In certain embodiments the stabilization annealing is at a metal temperature of 120-250 °C. In certain embodiments the stabilization annealing is for about 1-2 hrs. In other embodiments where the alloy has a composition including 0.12-0.28 wt. %
  • Si about 0.32-0.52 wt. % Fe, about 0.09-0.16 wt. % Cu, about 0.78-0.96 wt. % Mn, about 0.90-1.10 wt. % Mg, about 0.000-0.050 wt. % Cr, about 0.000-0.250 wt. % Zn, about 0.000-0.050 wt. % Ti, and up to 0.15 wt.
  • the method of making an aluminum alloy as described herein comprises direct chill casting an aluminum ingot; homogenizing the ingot; hot rolling the ingot to form a hot rolled product; cold rolling the hot rolled product in a first cold rolling step to form a first cold rolled product, wherein the first cold rolling step produces an about 60-90 % thickness reduction in the hot rolled product; cold rolling the first cold rolled product in a second cold rolling step, wherein the second cold rolling step produces an about 15-30 % thickness reduction in the product; and stabilization annealing of the second cold rolled product, wherein the stabilization annealing is at a metal temperature from about 100-300 °C for about 0.5-4 hrs.
  • the stabilization annealing is at a metal temperature from about 120-250 °C. In certain embodiments, the stabilization annealing is for about 1-2 hrs.
  • the final temper of the alloys could be either H2x (without interannealing) or H3x or Hlx (with interannealing).
  • the combination of rolling reduction gives optimized earing and excellent performance in the bodymaker.
  • the stabilization annealing cycle was designed to induce specific working hardening characteristics and formability in the alloys allowing extensive neck shaping without fracture.
  • the alloys described herein can be cast into ingots using a direct chill (DC) process.
  • the DC casting process is performed according to standards commonly used in the aluminum industry as known to one of skill in the art.
  • the casting process can include a continuous casting process.
  • the continuous casting may include, but are not limited to, twin roll casters, twin belt casters, and block casters.
  • the alloys are not processed using continuous casting methods.
  • the cast ingot can then be subjected to further processing steps to form a metal sheet.
  • the further processing steps include subjecting a metal ingot to a homogenization cycle, a hot rolling step, a cold rolling step, an optional recrystallization annealing step, a second cold rolling step, and a stabilization annealing step.
  • the homogenization step can involve a one-step homogenization or a two-step homogenization. In some embodiments of the homogenization step, a one-step
  • homogenization is performed in which an ingot prepared from the alloy compositions described herein is heated to attain a peak metal temperature (PMT). The ingot is then allowed to soak (i.e., held at the indicated temperature) for a period of time during the first stage.
  • PMT peak metal temperature
  • a two-step homogenization is performed where an ingot prepared from an alloy composition described herein is heated to attain a first temperature and then allowed to soak for a period of time In the second stage, the ingot can be cooled to a temperature lower than the temperature used in the first stage and then allowed to soak for a period of time during the second stage.
  • the ingots can be hot rolled to an 5 mm thick gauge or less.
  • the ingots can be hot rolled to a 4 mm thick gauge or less, 3 mm thick gauge or less, 2 mm thick gauge or less, or 1 mm thick gauge or less.
  • the hot rolling speed and temperature can be controlled such that full recrystallization of the hot rolled materials is achieved during coiling at the exit of the tandem mill.
  • a first cold rolling step produces a reduction in thickness of from about 60-90 % (e.g. about 50-80 %, about 60-70 %, about 50-90 %, or about 60-80 %).
  • the first cold rolling step produces a reduction in thickness of about 65 %, about 70 %, about 75 %, about 80 %, about 85 %, or about 90 %.
  • a second cold rolling step produces a further reduction in thickness of from about 15-30 % (e.g., from about 20-25%, about 15-25%, about 15-20%, about 20-30%, or about 25-30 %).
  • the second cold rolling step produces a further reduction in thickness of about 15 %, 20 %, 25 %, or 30 %.
  • an annealing step is a recrystallization annealing (e.g., after the initial cold rolling).
  • the recrystallization annealing is at a metal temperature from about 290-500 °C for about 0.5-4 hrs. In one embodiment, the
  • recrystallization annealing is at a metal temperature from about 300-450 °C. In one embodiment, the recrystallization is for about 1-2 hrs.
  • the recrystallization annealing step can include heating the alloy from room temperature to a temperature from about 290 °C to about 500 °C (e.g., from about 300 °C to about 450 °C, from about 325 °C to about 425 °C, from about 300 °C to about 400 °C, from about 400 °C to about 500 °C, from about 330 °C to about 470 °C, from about 375 °C to about 450 °C, or from about 450 °C to about 500 °C).
  • a temperature from about 290 °C to about 500 °C e.g., from about 300 °C to about 450 °C, from about 325 °C to about 425 °C, from about 300 °C to about 400 °C, from about 400 °
  • an annealing step is stabilization annealing (e.g., after the final cold rolling).
  • the stabilization annealing is at a metal temperature from about 100-300 °C for about 0.5-4 hrs. In one embodiment, the stabilization annealing is at a metal temperature from about 120-250 °C for about 1-2 hrs.
  • the stabilization annealing step can include heating the alloy from room temperature to a temperature from about 100°C to about 300 °C (e.g., from about 120 °C to about 250 °C, from about 125 °C to about 200 °C, from about 200 °C to about 300 °C, from about 150 °C to about 275 °C, from about 225 °C to about 300 °C, or from about 100 °C to about 175 °C).
  • a temperature from about 100°C to about 300 °C (e.g., from about 120 °C to about 250 °C, from about 125 °C to about 200 °C, from about 200 °C to about 300 °C, from about 150 °C to about 275 °C, from about 225 °C to about 300 °C, or from about 100 °C to about 175 °C).
  • the methods described herein can be used to prepare highly shaped metal objects, such as aluminum cans or bottles.
  • the cold rolled sheets described above can be subjected to a series of conventional can and bottle making processes to produce preforms.
  • the preforms can then be annealed to form annealed preforms.
  • the preforms are prepared from the aluminum alloys using a drawing and wall ironing (DWI) process and the cans and bottles are made according to other shaping processes as known to those of ordinary skill in the art.
  • DWI drawing and wall ironing
  • the shaped aluminum bottle of the present invention may be used for beverages including but not limited to soft drinks, water, beer, energy drinks and other beverages.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Ceramic Engineering (AREA)
  • Continuous Casting (AREA)
  • Containers Having Bodies Formed In One Piece (AREA)

Abstract

L'invention concerne des compositions et des procédés intégrant un nouveau système d'alliage d'aluminium utile pour des applications à des bouteilles en aluminium. Selon un aspect, l'invention concerne également un procédé de production de produits en aluminium très façonnés, telles des bouteilles ou des canettes, contenant l'alliage d'aluminium.
PCT/US2015/066638 2014-12-19 2015-12-18 Alliage d'aluminium approprié pour la production à grande vitesse d'une bouteille en aluminium et procédé de fabrication associé WO2016100800A1 (fr)

Priority Applications (8)

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JP2017531172A JP2018502993A (ja) 2014-12-19 2015-12-18 アルミニウムボトルの高速生産に適したアルミニウム合金及びその製造方法
CN201580068120.8A CN107002185A (zh) 2014-12-19 2015-12-18 适合于铝瓶的高速生产的铝合金及其制造工艺
KR1020177016425A KR101988146B1 (ko) 2014-12-19 2015-12-18 알루미늄 병의 고속 제조에 적합한 알루미늄 합금 및 이의 제조 방법
BR112017010216A BR112017010216A2 (pt) 2014-12-19 2015-12-18 liga de alumínio, garrafa de alumínio conformada, e, método de produção de uma liga de alumínio.
EP15828603.9A EP3234208B1 (fr) 2014-12-19 2015-12-18 Alliage d'aluminium approprié pour la production à grande vitesse d'une bouteille en aluminium et procédé de fabrication associé
CA2968894A CA2968894A1 (fr) 2014-12-19 2015-12-18 Alliage d'aluminium approprie pour la production a grande vitesse d'une bouteille en aluminium et procede de fabrication associe
ES15828603T ES2797023T3 (es) 2014-12-19 2015-12-18 Aleación de aluminio adecuada para la producción a alta velocidad de botella de aluminio y proceso de fabricación de la misma
MX2017007895A MX2017007895A (es) 2014-12-19 2015-12-18 Aleación de aluminio adecuada para la producción a alta velocidad de botellas de aluminio y su proceso de fabricación.

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US62/094,358 2014-12-19

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Publication number Priority date Publication date Assignee Title
WO2017192382A1 (fr) * 2016-05-02 2017-11-09 Novelis Inc. Alliages d'aluminium à aptitude au formage améliorée et procédés associés
WO2019232374A1 (fr) * 2018-06-01 2019-12-05 Novelis Inc. Tôle de corps de boîte égalisée à jauge basse et son procédé de fabrication
EP4050115A1 (fr) 2021-02-26 2022-08-31 Constellium Rolled Products Singen GmbH & Co.KG Tole mince durable en alliage d'aluminium pour applications décoratives
WO2022179856A1 (fr) 2021-02-26 2022-09-01 Constellium Rolled Products Singen Gmbh & Co.Kg Feuille d'alliage d'aluminium durable pour applications décoratives

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US20160177425A1 (en) 2016-06-23
ES2797023T3 (es) 2020-12-01
EP3234208A1 (fr) 2017-10-25
KR101988146B1 (ko) 2019-06-11
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