US20030015261A1 - Process for preparing an aluminum alloy sheet with improved bendability and aluminum alloy sheet produced therefrom - Google Patents

Process for preparing an aluminum alloy sheet with improved bendability and aluminum alloy sheet produced therefrom Download PDF

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Publication number
US20030015261A1
US20030015261A1 US10/138,846 US13884602A US2003015261A1 US 20030015261 A1 US20030015261 A1 US 20030015261A1 US 13884602 A US13884602 A US 13884602A US 2003015261 A1 US2003015261 A1 US 2003015261A1
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Prior art keywords
aluminum alloy
weight
aging
sheet material
sheet
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Abandoned
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US10/138,846
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English (en)
Inventor
Michael Bull
Alok Gupta
David Lloyd
Pierre Marois
John Sorensen
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Rio Tinto Alcan International Ltd
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Individual
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Priority to US10/138,846 priority Critical patent/US20030015261A1/en
Assigned to ALCAN INTERNATIONAL LIMITED reassignment ALCAN INTERNATIONAL LIMITED ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: BULL, MICHAEL JACKSON, SORENSEN, JOHN, LLOYD, DAVID JAMES, GUPTA, ALOK KUMAR, MAROIS, PIERRE HENRI
Publication of US20030015261A1 publication Critical patent/US20030015261A1/en
Assigned to CITICORP NORTH AMERICA, INC. reassignment CITICORP NORTH AMERICA, INC. SECURITY INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: NOVELIS CORPORATION, NOVELIS INC.
Assigned to NOVELIS CORPORATION, NOVELIS INC. reassignment NOVELIS CORPORATION RELEASE BY SECURED PARTY (SEE DOCUMENT FOR DETAILS). Assignors: CITICORP NORTH AMERICA, INC.
Abandoned legal-status Critical Current

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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
    • C22C21/06—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
    • C22C21/02—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
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • 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

Definitions

  • the present invention is directed to a process for preparing an aluminum alloy sheet having improved bendability and paint bake response.
  • the invention is also directed to an aluminum alloy sheet obtained by the process.
  • Aluminum alloys of the AA (Aluminum Association) 6000 series are desired to have low yield strength in the as-supplied temper and high yield strength in the finished product.
  • the low yield strength in the as-supplied temper is desirable to obtain excellent formability and reduced springback, while high yield strength in the finished product is required for adequate dent resistance at the lowest possible gauge for maximum weight savings.
  • U.S. Pat. No. 5,266,130 Uchida et al., issued Nov. 30, 1993 describes a process for manufacturing an aluminum alloy sheet material having good shape fixability and bake hardenability by regulating the heat pattern in the step of cooling after the solution heat treatment.
  • the sheet is first rapidly cooled to a quench temperature of 60 to 250° C. and then further cooled at a rate based on the specific quench temperature.
  • One aluminum alloy containing 0.8% Si, 0.7% Mg, 0.20% Mn and 0.15% Fe included a pre-aging treatment incorporating a cooling rate of 4° C./min from 150 to 50° C.
  • Another alloy containing 0.8% Si, 0.7% Mg, 0.30% Cu, 0.10% Mn, 0.15% Fe, 0.02% Ti and 20 ppm B was subjected to the same pre-aging treatment.
  • U.S. Pat. No. 5,616,189 Jin et al. describes an aluminum alloy containing magnesium, silicon and optionally copper in amounts suitable for the preparation of a sheet for use in the automotive industry.
  • the patent also describes a process for preparing an aluminum alloy sheet with suitable properties for use in the automotive industry.
  • aluminum alloys tested were an alloy containing 0.30% Cu, 0.50% Mg, 0.70% Si, 0.05% Mn and 0.22% Fe and another alloy containing 0.29% Cu, 0.52% Mg, 0.68% Si, 0.07% Mn and 0.21% Fe.
  • a sheet produced from these alloys was subjected to a 5 hour pre-aging treatment at 85° C.
  • the patent also states that sheet can be coiled at 85° C. and allowed to cool slowly to ambient at a rate less than 10° C./hour.
  • the alloys of the present invention are automotive aluminum alloys of AA6000 series containing (in percentages by weight) 0.50-0.75% Mg, 0.7-0.85% Si, 0.15-0.35% Mn, 0.1-0.3% Fe and the balance being aluminum and incidental impurities.
  • the alloy also contains 0.2-0.4% Cu.
  • the alloy is cast into ingots by semi-continuous casting, e.g. direct chill (DC) casting.
  • the ingots are homogenized and hot rolled to reroll gauge, then cold rolled and solution heat treated.
  • the heat treated sheet may be quenched to a desired initial pre-aging temperature.
  • the sheet product thus obtained is subjected to the pre-aging procedure of this invention and this pre-aging can be either the final step of the solution heat treatment stage or it can be part of a separate reheating step.
  • the sheet material starts with an initial pre-aging temperature which is at least 80° C. and may be as high as 175° C. or more.
  • a preferred initial pre-aging temperature is in the range of 95 to 200° C., more preferably 95 to 185° C.
  • the sheet material is rapidly cooled to ambient, e.g. 25° C., at a rate of more than 5° C./hour. This cooling rate is preferably in the range of 10 to 600° C./hour.
  • FIG. 1 shows the effect of cooling rate on yield strength (YS) for different pre-aging temperatures
  • FIG. 2 shows the effect of cooling rate on longitudinal bendability for different pre-aging temperatures
  • FIG. 3 shows the effect of cooling rate on transverse bendability for different pre-aging temperatures.
  • the low T4P yield strength promotes improved formability, particularly hemming performance without cracking.
  • the high T8 yield strength indicates a good paint bake response, i.e. after painting and baking the sheet has sufficient strength to resist dents and withstand other impacts.
  • the target physical properties for the sheet products of this invention are as follows: T4P, YS 90-120 MPa T4P, UTS >200 MPa T4P, E1 >28% ASTM, >30% (Using JIS Specimen) BEND, r min /t ⁇ 0.5 T8 (0% strain), YS >210 MPa T8 (2% strain), YS >220 MPa
  • the alloy used in this invention is cast by direct chill (DC) casting.
  • the ingots are homogenized for more than 5 hours at a temperature of more than 550° C.
  • the ingot is hot rolled to a reroll exit gauge of about 2.5-6 mm at an exit temperature of about 300-380° C.
  • the cold roll is to about 1mm gauge and the solution heat treatment is typically at a temperature of about 530-570° C.
  • the reroll sheet is cold rolled to an intermediate gauge of about 2.0-3.0 mm.
  • This intermediate sheet is batch annealed at a temperature of about 345-410° C. and then further cold rolled to about 1.0 mm.
  • Alloys containing 0.6% Mg, 0.8% Si, 0.25% Fe and 0.20% Mn and with or without 0.25% Cu were cast as 95 mm ⁇ 228 mm ingots to carry out the experiments.
  • the ingots were scalped, homogenized at 560° C. for 6 hours, hot rolled to 3.5 mm gauge, cold rolled to 2.1 mm in one pass, batch annealed at 360° C. for one hour and cold rolled to 0.93 mm gauge. This sheet material was solution heat treated at 560° C. for 5 minutes.
  • the solution heat treated sheet material was pre-aged by cooling from different pre-aging temperatures, including 105° C., 125° C., 150° C. and 175° C. Different cooling rates were used ranging from 1.25° C./hour to 600° C./hour.
  • YS yield strength
  • UTS tensile strength
  • El total elongation
  • n strain hardening index
  • Bendability r/t
  • This r/t ratio was determined from triplicate specimens according to the ASTM E 290C standard wrap bend test method. The minimum r/t value was obtained by dividing with the sheet thickness, the minimum radius of the mandrel that produced a crack free bend.
  • the radius of the mandrels used for the measurements were 0.001′′, 0.002′′, 0.003′′, 0.004′′, 0.006′′, 0.008′′, 0.010′′, 0.012′′, 0.016′′, 0.020′′, 0.024′′, 00.28′′, 0.032′′, 0.040′′, 0.048′′, 0.056′′ and so on.
  • T4P temper with natural aging of two and four weeks.
  • P means that the sheet material has been pre-aged.
  • T8 represents the YS after a simulated paint bake of 2% strain and 30 minutes at 177° C.
  • Tables 1 and 2 show the mechanical properties for a sheet formed from an alloy containing 0.6% Mg, 0.8% Si, 0.25% Fe, 0.20% Mn and the balance Al and incidental impurities. From Table 1 (two weeks of natural aging) it can be seen that good combinations of low T4P yield strengths and high T8 yield strengths were obtained for a number of combinations of pre-aging temperatures between 105° C. and 175° C. and cooling rates between 20 and 600° C./hour. Particularly good results were obtained by cooling from 125° C. at 20° C./hour, 150° C. at 60° C./hour and 175° C. at 600° C./hour. Also shown in Tables 1 and 2 are results without a pre-age. The T8 properties are significantly reduced compared to the pre-age practice.
  • Table 2 is similar to Table 1 except that the samples were naturally aged for four weeks. The results are not significantly different from those of Table 1. The stability of properties over time is a particularly desirable feature.
  • FIGS. 1, 2 and 3 show the effects of cooling rates from different start of cooling temperatures on the yield strength and bendability.
  • FIG. 1 shows that the use of slower cooling rates from high temperatures increases the yield strength in the T4P and T8 tempers due to artificial aging and affects bendability adversely. The best combination of properties is obtained with faster cooling rates from high start of cooling temperatures as seen in Table 1.
  • Tables 3 and 4 summarize the average tensile properties of the 0.25% Cu containing alloy after two and four weeks of natural aging. The trends obtained from this alloy are very similar to the Cu free alloy. Generally, the artificial aging response of the alloy is better and this translates into a higher yield strength, especially in situations where cooling is carried out from high temperatures. In general, the paint bake response and bendability following cooling from 125° C. at 20° C./hour are excellent after two weeks of natural aging, although there is a slight deterioration after four weeks of natural aging.
  • the pre-aged sheet material obtained according to this invention can be coiled for future use. It is also possible to have the alloy sheet move directly from solution heat treatment to a cleaning bath where the rapid cooling pre-aging takes place.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Continuous Casting (AREA)
  • Metal Rolling (AREA)
US10/138,846 2001-05-03 2002-05-02 Process for preparing an aluminum alloy sheet with improved bendability and aluminum alloy sheet produced therefrom Abandoned US20030015261A1 (en)

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US10/138,846 US20030015261A1 (en) 2001-05-03 2002-05-02 Process for preparing an aluminum alloy sheet with improved bendability and aluminum alloy sheet produced therefrom

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US (1) US20030015261A1 (enExample)
EP (1) EP1390553A1 (enExample)
JP (1) JP2004527658A (enExample)
BR (1) BR0209385A (enExample)
CA (1) CA2445667A1 (enExample)
IS (1) IS6998A (enExample)
NO (1) NO20034888L (enExample)
WO (1) WO2002090608A1 (enExample)

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20030029531A1 (en) * 2001-05-03 2003-02-13 Bull Michael Jackson Process for making aluminum alloy sheet having excellent bendability
US20060070689A1 (en) * 2004-10-05 2006-04-06 Corus Aluminium Walzprodukte Gmbh Method of heat treating an aluminium alloy member and apparatus therefor
US20160083825A1 (en) * 2013-05-17 2016-03-24 Constellium Neuf-Brisach Aluminium alloy sheet for metallic bottle or aerosol container
CN108796404A (zh) * 2018-06-11 2018-11-13 江苏大学 一种车身用原位纳米颗粒增强铝基复合材料的挤压工艺
CN110088315A (zh) * 2016-12-16 2019-08-02 诺维尔里斯公司 耐受自然老化硬化的高强度和高可成形铝合金及其制造方法
US10648738B2 (en) 2015-06-24 2020-05-12 Novelis Inc. Fast response heaters and associated control systems used in combination with metal treatment furnaces
US11193192B2 (en) 2014-10-28 2021-12-07 Novelis Inc. Aluminum alloy products and a method of preparation
US11447851B2 (en) * 2015-05-29 2022-09-20 Arconic Technologies Llc 6xxx aluminum alloys and methods of making the same

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10324452B4 (de) * 2002-07-01 2010-05-06 Aleris Aluminum Duffel Bvba AI-Mg-Si-Legierungsblech
DE10324453B4 (de) * 2002-07-01 2008-06-26 Corus Aluminium N.V. Gewalztes wärmebehandelbares Al-Mg-Si-Legierungsprodukt
JP5709298B2 (ja) * 2010-08-12 2015-04-30 株式会社Uacj 塗装焼付硬化性および成形性に優れたＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金板の製造方法
AU2016206897B2 (en) 2015-01-12 2019-01-17 Novelis Inc. Highly formable automotive aluminum sheet with reduced or no surface roping and a method of preparation
KR102253860B1 (ko) 2016-12-16 2021-05-24 노벨리스 인크. 알루미늄 합금 및 그 제조 방법
CN112626429B (zh) * 2019-10-08 2022-10-21 有研工程技术研究院有限公司 一种提高6000系铝合金板材抗时效稳定性的方法
CA3229084A1 (en) * 2021-10-26 2023-05-04 Novelis Inc. Heat treated aluminum sheets and processes for making

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US4718948A (en) * 1986-02-26 1988-01-12 Sky Aluminium Co., Ltd. Rolled aluminum alloy sheets for forming and method for making
US4808247A (en) * 1986-02-21 1989-02-28 Sky Aluminium Co., Ltd. Production process for aluminum-alloy rolled sheet
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US5266130A (en) * 1992-06-30 1993-11-30 Sumitomo Light Metal Industries, Ltd. Process for manufacturing aluminum alloy material having excellent shape fixability and bake hardenability
US5616189A (en) * 1993-07-28 1997-04-01 Alcan International Limited Aluminum alloys and process for making aluminum alloy sheet
US6120623A (en) * 1997-02-19 2000-09-19 Alcan International Limited Process of producing aluminum alloy sheet exhibiting reduced roping effects
US20030029531A1 (en) * 2001-05-03 2003-02-13 Bull Michael Jackson Process for making aluminum alloy sheet having excellent bendability

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JPH06136478A (ja) * 1992-10-23 1994-05-17 Kobe Steel Ltd 成形加工性に優れた焼付硬化型Ａｌ合金板及びその製造方法
KR100374104B1 (ko) * 1994-09-06 2003-04-18 알칸 인터내셔널 리미티드 알루미늄합금시이트제조방법
JPH11350058A (ja) * 1998-06-12 1999-12-21 Shinko Alcoa Yuso Kizai Kk 成形性及び焼き付け硬化性に優れるアルミニウム合金板及びその製造方法

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US4082578A (en) * 1976-08-05 1978-04-04 Aluminum Company Of America Aluminum structural members for vehicles
US4808247A (en) * 1986-02-21 1989-02-28 Sky Aluminium Co., Ltd. Production process for aluminum-alloy rolled sheet
US4718948A (en) * 1986-02-26 1988-01-12 Sky Aluminium Co., Ltd. Rolled aluminum alloy sheets for forming and method for making
US4897124A (en) * 1987-07-02 1990-01-30 Sky Aluminium Co., Ltd. Aluminum-alloy rolled sheet for forming and production method therefor
US5266130A (en) * 1992-06-30 1993-11-30 Sumitomo Light Metal Industries, Ltd. Process for manufacturing aluminum alloy material having excellent shape fixability and bake hardenability
US5616189A (en) * 1993-07-28 1997-04-01 Alcan International Limited Aluminum alloys and process for making aluminum alloy sheet
US6120623A (en) * 1997-02-19 2000-09-19 Alcan International Limited Process of producing aluminum alloy sheet exhibiting reduced roping effects
US20030029531A1 (en) * 2001-05-03 2003-02-13 Bull Michael Jackson Process for making aluminum alloy sheet having excellent bendability

Cited By (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6780259B2 (en) * 2001-05-03 2004-08-24 Alcan International Limited Process for making aluminum alloy sheet having excellent bendability
US20040250928A1 (en) * 2001-05-03 2004-12-16 Bull Michael Jackson Process for making aluminum alloy sheet having excellent bendability
US7029543B2 (en) 2001-05-03 2006-04-18 Novelis, Inc. Process for making aluminum alloy sheet having excellent bendability
US20030029531A1 (en) * 2001-05-03 2003-02-13 Bull Michael Jackson Process for making aluminum alloy sheet having excellent bendability
US20060070689A1 (en) * 2004-10-05 2006-04-06 Corus Aluminium Walzprodukte Gmbh Method of heat treating an aluminium alloy member and apparatus therefor
US7491278B2 (en) * 2004-10-05 2009-02-17 Aleris Aluminum Koblenz Gmbh Method of heat treating an aluminium alloy member and apparatus therefor
US20160083825A1 (en) * 2013-05-17 2016-03-24 Constellium Neuf-Brisach Aluminium alloy sheet for metallic bottle or aerosol container
US10577683B2 (en) * 2013-05-17 2020-03-03 Constellium France Aluminium alloy sheet for metallic bottle or aerosol container
US11193192B2 (en) 2014-10-28 2021-12-07 Novelis Inc. Aluminum alloy products and a method of preparation
US12410499B2 (en) 2014-10-28 2025-09-09 Novelis Inc. Aluminum alloy products and a method of preparation
US11447851B2 (en) * 2015-05-29 2022-09-20 Arconic Technologies Llc 6xxx aluminum alloys and methods of making the same
US11268765B2 (en) 2015-06-24 2022-03-08 Novelis Inc. Fast response heaters and associated control systems used in combination with metal treatment furnaces
US10648738B2 (en) 2015-06-24 2020-05-12 Novelis Inc. Fast response heaters and associated control systems used in combination with metal treatment furnaces
CN110088315A (zh) * 2016-12-16 2019-08-02 诺维尔里斯公司 耐受自然老化硬化的高强度和高可成形铝合金及其制造方法
US11530473B2 (en) 2016-12-16 2022-12-20 Novelis Inc. High strength and highly formable aluminum alloys resistant to natural age hardening and methods of making the same
CN108796404A (zh) * 2018-06-11 2018-11-13 江苏大学 一种车身用原位纳米颗粒增强铝基复合材料的挤压工艺

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Publication number Publication date
CA2445667A1 (en) 2002-11-14
NO20034888L (no) 2004-01-02
WO2002090608A1 (en) 2002-11-14
EP1390553A1 (en) 2004-02-25
IS6998A (is) 2003-10-22
JP2004527658A (ja) 2004-09-09
BR0209385A (pt) 2004-07-06
NO20034888D0 (no) 2003-11-03

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