EP0686208B1 - Procede de fabrication d'une tole d'alliage d'aluminium a haute formabilite - Google Patents

Procede de fabrication d'une tole d'alliage d'aluminium a haute formabilite Download PDF

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Publication number
EP0686208B1
EP0686208B1 EP95905681A EP95905681A EP0686208B1 EP 0686208 B1 EP0686208 B1 EP 0686208B1 EP 95905681 A EP95905681 A EP 95905681A EP 95905681 A EP95905681 A EP 95905681A EP 0686208 B1 EP0686208 B1 EP 0686208B1
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EP
European Patent Office
Prior art keywords
weight
temperature
alloy
aluminium alloy
mechanical properties
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP95905681A
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German (de)
English (en)
French (fr)
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EP0686208A1 (fr
Inventor
Binrun Oh
Yuichi Suzuki
Kunihiko Kishino
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Constellium Issoire SAS
JFE Steel Corp
Furukawa Electric Co Ltd
Kaiser Aluminum and Chemical Corp
Original Assignee
Pechiney Rhenalu SAS
Furukawa Electric Co Ltd
Kawasaki Steel Corp
Kaiser Aluminum and Chemical Corp
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Application filed by Pechiney Rhenalu SAS, Furukawa Electric Co Ltd, Kawasaki Steel Corp, Kaiser Aluminum and Chemical Corp filed Critical Pechiney Rhenalu SAS
Publication of EP0686208A1 publication Critical patent/EP0686208A1/fr
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/057—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 copper as the next major constituent

Definitions

  • the present invention relates to a manufacturing method improving the mechanical properties and formability of aluminum alloy sheets intended in particular for automobile bodywork.
  • Automobile bodies are traditionally produced in cold rolled steel sheet.
  • Al-Mg-Si alloy sheet is formed into a bodywork element after a solution treatment followed by natural aging in the T4 state. After shaping, hardening by aging (baking hardening in English), during application and curing of the paints, gives it the required mechanical properties.
  • the main difficulty raised by the exploitation of aluminum alloys in automobile bodywork is the insufficient formability of this family of materials.
  • the formability of aluminum alloys and particularly that of Al-Mg-Si alloys therefore needs to be significantly improved.
  • the present invention relates to a process for manufacturing aluminum alloy sheets with high formability, characterized in that an aluminum alloy sheet composed of 0.3 to 1.7% (by weight) of Si, 0.01 to 1.2% Cu, 0.01 to 1.1% Mn, 0.4 to 1.4% Mg, less than 1.0% Fe and, for the rest, Al and inevitable impurities, is subjected to a continuous heat treatment in solution for at least 3 seconds at more than 450 ° C., followed by cooling to a temperature of 60 to 250 ° C. at a speed greater than 100 ° C / min, of a winding with maintenance at said temperature of 60 to 250 ° C and a pre-aging period of between 1 minute and 10 hours at said temperature of 60 to 250 ° C.
  • the alloy may additionally contain one or more elements chosen from 0.04 to 0.4% of Cr, less than 0.25% of Zn, less than 0.4% of Zr and less than 0.2% of Ti .
  • Aluminum alloys of the Al-Mg-Si type are alloys which harden with aging: aging induces the precipitation of a structural hardening phase, which increases the mechanical properties.
  • the process follows the following scheme: supersaturated solid solution ⁇ GP zone ⁇ Intermediate phase ⁇ Stable phase
  • the baking of the paint causes artificial aging which then precipitates an intermediate phase (hardening phase structural) which optimizes the mechanical properties of the alloy.
  • the problem of this prior process lies in the distribution of the precipitates which, being mainly concentrated in GP zones at the time of natural aging, then thwart the precipitation of the phase intermediate by artificial aging, and therefore prohibited obtaining optimal mechanical strength.
  • the alignment of the GP zones with the matrix phase (Al) harms the formability insofar as it favors, at the time of deformations, the rupture at the level of dislocations and finally the concentration of stresses in grain boundaries.
  • the present invention results from taking these various observations into account. It is mainly characterized by the permanent maintenance at a temperature above 60 ° C, without the slightest foray into the normal temperature range, during the whole process between the solution treatment and the final pre-aging.
  • the objective is in fact, by maintaining the temperature above 60 ° C. until the end of pre-aging, to prevent the formation of GP zones, knowing that the previous process precisely involves incursions at normal temperature, that this either during the quenching of natural aging or until cooking, and that these incursions are at the origin of the formation of such GP zones.
  • the sheet once pre-aged can then, without affecting its formability or its mechanical properties, be exposed for a prolonged period to a normal temperature during forming and then applying and curing the paints.
  • the manufacturing process according to the invention consists, after preparation, casting, homogenization and rolling of the above-described aluminum alloy according to a usual method, to subject it to a continuous treatment of dissolved by heating for more than 3 seconds at a temperature above 450 ° C, followed by cooling to a temperature of 60 to 250 ° C at a speed higher than 100 ° C / min, from a winding with holding at said temperature from 60 to 250 ° C and a pre-aging period between 1 minute and 10 hours at said temperature from 60 to 250 ° C.
  • the dissolution treatment improves the formability of the material by causing the temporary dissolution of elements such as Si and Mg in the matrix, and subsequently promotes the mechanical properties through the fine precipitation of compounds such as Mg 2 If during subsequent cooking.
  • the solution heating is applied for a minimum of 3 seconds at a temperature above 450 ° C. Indeed, if the temperature and the duration do not reach 450 ° C and 3 seconds, the dissolution of the elements (Si, Mg etc ...) and therefore the improvement of the mechanical properties during the subsequent cooking are insufficient .
  • the cooling rate after dissolution is chosen to be greater than 100 ° C / min. Indeed, a speed below 100 ° C / min results in coarse precipitation, therefore in poor formability as well as in an insufficient improvement in mechanical properties during cooking.
  • the final temperature for this cooling rate is chosen in the range 60-250 ° C. Indeed, if it is below 60 ° C, it shows GP areas, and if it is above 250 ° C, it promotes the precipitation of a stable phase at the expense of formability and mechanical properties.
  • the winding in the same temperature range 60-250 ° C of the material cooled to 60-250 ° C, then the pre-aging from 1 minute to 10 hours always in the temperature range 60-250 ° C are intended to allow the formation an intermediate phase which benefits the mechanical properties and the formability of the alloy. If their temperature is below 60 ° C, GP zones are formed, and if it is above 250 ° C, there is precipitation of a stable phase, in both cases to the detriment of mechanical properties and formability of the alloy.
  • the duration of the pre-aging is chosen between 1 minutes and 10 hours. In effect, below 1 minute, insufficient precipitation of the phase intermediate risk later, when returning to normal temperature, to favor the formation of GP zones, and above 10 hours, the phase intermediate, overabundant, excessively strengthens the properties mechanical properties of the alloy to the detriment of its formability.
  • the present invention applies not only to the method of continuous manufacturing mentioned above, but also and with the same effects to classic discontinuous processes.
  • Fig. 1 is a micrograph which represents the microstructure of a sheet of aluminum alloy constituting an exemplary embodiment of the invention.
  • Fig. 2 is a micrograph which represents the microstructure of a sheet aluminum alloy constituting another embodiment of the invention.
  • Fig. 3 is a micrograph which represents the microstructure of a sheet of aluminum alloy manufactured by a process of the prior art.
  • Fig. 4 is a micrograph which represents the microstructure of a sheet of aluminum alloy made by another process of the prior art.
  • the aluminum alloys having the compositions of Table 1 were prepared, poured, suitably homogenized, hot rolled at 400 ° C, then cold rolled by the usual methods to obtain sheets of 1 mm thick.
  • the sheets were subjected to a continuous treatment of 10 seconds solution treatment at 560 ° C, then heat treatment under the conditions of Table 2, to be pre-aged between 1 minute and 10 hours at a given temperature, as the case may be 60 ° C, 120 ° C, 180 ° C or 250 ° C. Some of these sheets were finally subjected to a treatment of cooking (1 hour at 180 ° C), others not.
  • the tensile test was carried out on a JIS No.5 tensile test piece.
  • the Erichsen test was conducted using the JIS Z2247A method (measurement of the deep drawing).
  • the limit drawing test (LDR) consisted stamp a lubricated blank with a 33 mm diameter punch, measure the maximum blank diameter for which there is no rupture of said blank and calculate the ratio of this maximum diameter to the diameter of the punch.
  • the alloy of code C in Table 1 (Si 1.65%, Fe 0.08%, Mn 0.10%, Mg 1.38%, Zn 0.01%, Ti 0.02%, remains: AL ) subjected to the heat treatment 3 of Table 2 (dissolution in 10 seconds at 560 ° C, cooling to 120 ° C, winding at 120 ° C, 3 hours pre-aging at 120 ° C, no cooking) was selected as sample ( at).
  • the same alloy C subjected to the heat treatment 4 of Table 2 (treatment of the sample i (a) supplemented by baking for 1 hour at 180 ° C.) was retained as sample (b).
  • Fig. 3 and Fig. 4 demonstrate that further cooling down to 20 ° C prevents precipitation of the intermediate phase of Mg 2 Si, this even if it is followed by pre-aging and cooking treatment.
  • the method according to the invention has the great advantage from an industrial point of view of making it possible to manufacture aluminum alloy sheets guaranteeing excellent mechanical properties and formability.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)
  • Powder Metallurgy (AREA)
  • Heat Treatment Of Steel (AREA)
EP95905681A 1993-12-28 1994-12-28 Procede de fabrication d'une tole d'alliage d'aluminium a haute formabilite Expired - Lifetime EP0686208B1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP5352713A JPH07197219A (ja) 1993-12-28 1993-12-28 成形用アルミニウム合金板材の製造方法
JP35271393 1993-12-28
JP352713/93 1993-12-28
PCT/FR1994/001547 WO1995018244A1 (fr) 1993-12-28 1994-12-28 Procede de fabrication d'une tole d'alliage d'aluminium a haute formabilite

Publications (2)

Publication Number Publication Date
EP0686208A1 EP0686208A1 (fr) 1995-12-13
EP0686208B1 true EP0686208B1 (fr) 2002-05-15

Family

ID=18425926

Family Applications (1)

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EP95905681A Expired - Lifetime EP0686208B1 (fr) 1993-12-28 1994-12-28 Procede de fabrication d'une tole d'alliage d'aluminium a haute formabilite

Country Status (8)

Country Link
US (1) US5690758A (ja)
EP (1) EP0686208B1 (ja)
JP (1) JPH07197219A (ja)
KR (1) KR0158723B1 (ja)
CA (1) CA2157000A1 (ja)
DE (1) DE69430622T2 (ja)
ES (1) ES2176313T3 (ja)
WO (1) WO1995018244A1 (ja)

Families Citing this family (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5616189A (en) * 1993-07-28 1997-04-01 Alcan International Limited Aluminum alloys and process for making aluminum alloy sheet
GB9318041D0 (en) * 1993-08-31 1993-10-20 Alcan Int Ltd Extrudable a1-mg-si alloys
FR2748035B1 (fr) * 1996-04-29 1998-07-03 Pechiney Rhenalu Alliage aluminium-silicium-magnesium pour carrosserie automobile
US6224693B1 (en) * 1999-12-10 2001-05-01 Tenedora Nemak, S.A. De C.V. Method and apparatus for simplified production of heat treatable aluminum alloy castings with artificial self-aging
AUPQ485399A0 (en) * 1999-12-23 2000-02-03 Commonwealth Scientific And Industrial Research Organisation Heat treatment of age-hardenable aluminium alloys
AUPR360801A0 (en) * 2001-03-08 2001-04-05 Commonwealth Scientific And Industrial Research Organisation Heat treatment of age-hardenable aluminium alloys utilising secondary precipitation
JP4101749B2 (ja) * 2001-07-23 2008-06-18 コラス・アルミニウム・バルツプロドウクテ・ゲーエムベーハー 溶接可能な高強度Ａｌ−Ｍｇ−Ｓｉ合金
DE10163039C1 (de) * 2001-12-21 2003-07-24 Daimler Chrysler Ag Warm- und kaltumformbares Bauteil aus einer Aluminiumlegierung und Verfahren zu seiner Herstellung
JP4932473B2 (ja) * 2003-03-17 2012-05-16 アレリス、アルミナム、コブレンツ、ゲゼルシャフト、ミット、ベシュレンクテル、ハフツング 一体化されたモノリシックアルミニウム構造の製造方法およびその構造から機械加工されたアルミニウム製品
US20060070686A1 (en) * 2004-10-05 2006-04-06 Corus Aluminium Walzprodukte Gmbh High hardness moulding plate and method for producing said plate
FR2902442B1 (fr) * 2006-06-16 2010-09-03 Aleris Aluminum Koblenz Gmbh Alliage de la serie aa6xxx, a grande tolerance aux dommages pour l'industrie aerospatiale
JP2008303449A (ja) * 2007-06-11 2008-12-18 Furukawa Sky Kk 成形加工用アルミニウム合金板および成形加工用アルミニウム合金板の製造方法
JP5432439B2 (ja) * 2007-06-27 2014-03-05 株式会社神戸製鋼所 温間成形用アルミニウム合金板
JP5204517B2 (ja) * 2008-03-19 2013-06-05 株式会社神戸製鋼所 電池ケース用アルミニウム合金板およびその製造方法
KR20130104740A (ko) * 2012-03-15 2013-09-25 (주)경남금속 충격 흡수성 및 열적 안정성이 우수한 고강도 알루미늄 합금
KR102437942B1 (ko) 2014-01-21 2022-08-29 아르코닉 테크놀로지스 엘엘씨 6xxx 알루미늄 합금
KR102228792B1 (ko) 2015-12-18 2021-03-19 노벨리스 인크. 고 강도 6ｘｘｘ 알루미늄 합금들 및 이를 만드는 방법들
US10428412B2 (en) * 2016-11-04 2019-10-01 Ford Motor Company Artificial aging of strained sheet metal for strength uniformity
EP3765647B1 (en) 2018-03-15 2023-05-31 Aleris Aluminum Duffel BVBA Method of manufacturing an almgsi alloy sheet product
WO2019222236A1 (en) 2018-05-15 2019-11-21 Novelis Inc. High strength 6xxx and 7xxx aluminum alloys and methods of making the same
CN112522550B (zh) * 2020-11-04 2022-10-04 佛山科学技术学院 一种快速时效响应的铝合金及其制备方法和应用

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3135633A (en) * 1959-09-08 1964-06-02 Duralumin Heat treatment process improving the mechanical properties of aluminiummagnesium-silicon alloys
FR2493345A1 (fr) * 1980-11-05 1982-05-07 Pechiney Aluminium Methode de trempe interrompue des alliages a base d'aluminium
US5098490A (en) * 1990-10-05 1992-03-24 Shin Huu Super position aluminum alloy can stock manufacturing process
US5582660A (en) * 1994-12-22 1996-12-10 Aluminum Company Of America Highly formable aluminum alloy rolled sheet

Also Published As

Publication number Publication date
EP0686208A1 (fr) 1995-12-13
DE69430622D1 (de) 2002-06-20
ES2176313T3 (es) 2002-12-01
WO1995018244A1 (fr) 1995-07-06
JPH07197219A (ja) 1995-08-01
US5690758A (en) 1997-11-25
KR950018595A (ko) 1995-07-22
KR0158723B1 (ko) 1999-01-15
DE69430622T2 (de) 2002-12-05
CA2157000A1 (en) 1995-07-06

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