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EP0990058A1 - Procede de production d'une feuille en alliage d'aluminium apte au traitement thermique - Google Patents

Procede de production d'une feuille en alliage d'aluminium apte au traitement thermique

Info

Publication number
EP0990058A1
EP0990058A1 EP98930576A EP98930576A EP0990058A1 EP 0990058 A1 EP0990058 A1 EP 0990058A1 EP 98930576 A EP98930576 A EP 98930576A EP 98930576 A EP98930576 A EP 98930576A EP 0990058 A1 EP0990058 A1 EP 0990058A1
Authority
EP
European Patent Office
Prior art keywords
article
ingot
gauge
process according
thickness
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.)
Granted
Application number
EP98930576A
Other languages
German (de)
English (en)
Other versions
EP0990058B1 (fr
Inventor
Alok Kumar Gupta
Paul William Jeffrey
David James Lloyd
Gene Bruce Burger
Daniel Ronald Evans
Pierre Henry Marois
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.)
Rio Tinto Alcan International Ltd
Original Assignee
Alcan International Ltd Canada
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Alcan International Ltd Canada filed Critical Alcan International Ltd Canada
Publication of EP0990058A1 publication Critical patent/EP0990058A1/fr
Application granted granted Critical
Publication of EP0990058B1 publication Critical patent/EP0990058B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Classifications

    • 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

  • This invention relates to a process of producing aluminum alloy sheet material having good formability and yield strength improvement when subjected to the painting and baking operations typically employed during the fabricating automotive parts. More particularly, although not exclusively, the invention relates to the production of aluminum alloy sheet material suitable for fabricating automotive parts that are visible in the finished vehicles, such as automotive skin panels and the like.
  • AA6000 series alloys contain magnesium and silicon, both with and without copper but, depending upon the Cu content, may be classified as AA2000 series alloys. These alloys are formable in the T4 temper condition and become stronger after painting and baking (steps usually carried out on formed automotive parts by vehicle manufacturers) . Good increases in strength after painting and baking are highly desirable so that thinner and therefore lighter panels may be employed. To facilitate understanding, a brief explanation of the terminology used to describe alloy tempers may be in order at this stage.
  • T4 The temper referred to as T4 is well known (see, for example, Aluminum Standards and Data (1984), page 11, published by The Aluminum Association) and refers to alloy produced in the conventional manner, i.e. without intermediate batch annealing and pre-aging. This is the temper in which automotive sheet products are normally delivered to parts manufacturers for forming into skin panels and the like.
  • T8 temper designates an alloy that has been solution heat-treated, cold worked and then artificially aged. Artificial aging involves holding the alloy at elevated temperature (s) over a period of time.
  • T8X temper refers to a T4 temper material that has been deformed in tension by 2% followed by a 30 minute treatment at 111 ° C to represent the forming plus paint baking treatment typically experienced by formed automotive panels.
  • An alloy that has only been solution heat-treated and artificially aged to peak strength is said to be in the T6 temper, whereas if the aging has taken place naturally under room temperature conditions, the alloy is said to be in the T4 temper, as indicated above.
  • Material that has undergone an intermediate batch annealing, but no pre-aging is said to have a T4A temper.
  • Material that has undergone pre-aging but not intermediate batch annealing is said to have a T4P temper, and material that has undergone both intermediate annealing and pre- aging is said to have a T4PA temper.
  • the process involves subjecting a sheet product, after cold rolling, to a solutionizing treatment (heating to 500 to 570°C) followed by a quenching or cooling process involving carefully controlled cooling steps to bring about a degree of "pre-aging.”
  • a solutionizing treatment heating to 500 to 570°C
  • a quenching or cooling process involving carefully controlled cooling steps to bring about a degree of "pre-aging.”
  • This procedure results in the formation of fine stable precipitate clusters that promote a fine, well dispersed precipitate structure during the paint/bake procedure to which automotive panels are subjected, and consequently a relatively high T8X temper.
  • the quenching or cooling process involves cooling the alloy from the solution heat treatment temperature to an intermediate temperature without interruption and, without further interruption, cooling the aluminum alloy further to ambient temperature at a significantly slower rate.
  • the intermediate target temperature may be approached in a single step or multiple steps .
  • roping has been encountered by others in this art, and it has been found that roping may be inhibited by modifying the sheet production method so that recrystallisation occurs at an intermediate stage of processing.
  • the inhibition of roping is addressed, for example, in US Patent No. 5,480,498 issued on January 2, 1996 to Armand J. Beaudoin, et al . , assigned to Reynolds Metals Company, and also in US Patent No. 4,897,124 issued on January 30, 1990 to Matsuo et al., assigned to Sky Aluminum Co., Ltd.
  • roping is controlled by introducing a batch annealing step (e.g. heating at a temperature within the range of 316 to 538 °C) at an intermediate stage of the sheet product formation, e.g.
  • An object of the present invention is to provide an improved method of reducing or inhibiting roping tendencies in aluminum alloy sheet products of the 6000 or 2000 series, while maintaining acceptable T4 and T8X properties .
  • Another object of the invention is to provide an improved process of reducing or inhibiting roping tendencies in 6000 series or 2000 series aluminum alloy sheet products.
  • a process for producing aluminum sheet articles made of 6000 or 2000 series aluminum alloy in which a cast ingot is formed by direct chill casting, the ingot is scalped to form a scalped ingot, the scalped ingot is homogenized at a temperature between 480 and 580 °C for less than 48 hours to form an homogenized ingot (preferably by a simple ingot heating practice to peak temperature at the higher end of the stated temperature range) , and the homogenized ingot is rolled to form a sheet article of final gauge, characterized in that said homogenized ingot is rolled to final gauge directly by hot rolling, or by hot and optionally cold rolling to form an article of intermediate gauge that requires a reduction in thickness in the range of 15 to less than 40% to reach final gauge, followed by cold rolling said article of intermediate gauge to form said sheet article of said final gauge.
  • the term “cold rolling” may be taken to mean rolling operations carried out at temperatures from ambient to a maximum of about 150°C.
  • the term “hot rolling” may be taken to mean rolling operations carried out at temperatures of above about 300°C, and preferably at about 520°C.
  • the invention also relates to aluminum sheet products produced by the process described above.
  • This process is based on the finding that it is the cold rolling step that introduces a tendency to exhibit roping into the finished sheet product. If the reduction in thickness brought about in the cold rolling step is excessive (40% or more) , roping effects become unacceptable .
  • the hot rolling steps do not introduce a roping tendency into the finished sheet articles. Therefore, if the reduction to final gauge can be accomplished by hot rolling alone, then the cold rolling steps may be eliminated, together with any tendency to produce roping effects.
  • the cold rolling preferably reduces the thickness of the alloy sheet by an amount in the range of 18% to less than 40% to said final gauge, more preferably 20 to 35%, and even more preferably 20 to 30%.
  • the process of the invention that employs cold rolling also preferably employs a heat treating step (e.g.
  • the heat treating step is carried out between cold rolling steps, it is usually carried out between the penultimate and the final cold rolling steps. The 15% to less than 40% reduction in thickness is then brought about by the final cold rolling step.
  • the processes of the invention also preferably employ a solutionizing step (e.g. heating at a temperature of 480-580°C) carried out on the sheet article of final gauge.
  • a solutionizing step e.g. heating at a temperature of 480-580°C
  • This is preferably followed by a controlled pre- aging step of the type described in the Jin et al . patent discussed above, e.g. by cooling the sheet article rapidly from the solutionizing temperature to an intermediate temperature, and then cooling from the intermediate temperature to ambient at a slower rate (e.g. ⁇ . 2°C/hour) .
  • the alloy on which the indicated processes are carried is preferably AA6111 aluminum alloy, but the processes are effective for other alloys of the 6000 or 2000 series, particularly if they contain Cu, e.g.
  • a preferred form of the invention involves direct chill casting the alloy to produce a cast ingot, scalping the cast ingot to form a scalped ingot, homogenizing the scalped ingot at a temperature between 480 and 580°C for less than 48 hours to form an homogenized ingot, hot and cold rolling the homogenized ingot to an intermediate gauge to form an intermediate sheet article, heat treating the intermediate sheet article at a temperature between 280 and 560°C for up to 18 hours to form a heat treated intermediate article, and cold rolling the intermediate article between 15 and less than 40% to a final gauge.
  • the sheet article of final gauge is then solutionized between 480 and 580°C, preferably in a continuous heat treatment furnace, rapidly cooled and then pre-aged according to the process described earlier in the Jin et al . Finally, the pre-aged material is optionally subjected to various finishing operations including levelling to obtain a flat sheet article.
  • the material produced in this manner shows an improved bend formability, no or reduced roping (paint brush) lines after being formed into panels and higher strength during the paint cure than conventionally treated alloys of the same kind (e.g. AA6111-T4 material) .
  • Figure 1 is a flow chart showing the steps of a preferred procedure according to the present invention.
  • Figure 2 is a flow chart similar to Figure 1 showing another preferred procedure according to the invention.
  • Figure 3 is a schematic representation of preferred equipment used for the procedures of Figures 1 and 2.
  • 6000 series alloy sheet materials such as AA6111 and AA6016
  • some 2000 series alloy sheet materials do not exhibit roping after hot rolling alone.
  • the hot-rolled materials tend to show signs of roping after subsequent cold rolling of ⁇ 30% and become fully roped at about 40% reduction. Therefore, the degree of cold work influences roping, although the underlying mechanism for this is not yet fully understood.
  • Conventional AA6111 alloy sheet is produced from a commercial size ingot which is scalped, homogenized, hot- and cold-rolled to .>60% before being solution heat treated (solutionized) to impart the T4 temper. Such material exhibits roping upon forming (the standard test is to strain the sheet by 15% in the transverse orientation and then to stone the surface lightly) .
  • a substantially roping-free sheet material can be produced, provided the amount of cold reduction after hot rolling (if cold rolling is required at all) is ⁇ 40%, preferably between 15% and less than 40%, and more preferably 18% to less than 40%, more preferably 20% to 35%, and most preferably between 20% and 30%. Below 15% cold reduction coarse grains may be formed during solutionizing and they produce an "orange peel" pattern after forming. Such an appearance is considered unacceptable, especially in exterior automotive panel applications .
  • the optional heat treatment involves heating the sheet to a temperature between 280 and 560°C and heat soaking for up to 18 hours .
  • the minimum time required for the heat treatment is dependent upon the temperature employed. At the high end of the temperature range, the minimum time required may be very short (essentially zero time at the peak temperature) , but a person skilled in the art will readily appreciate the time required in any particular case.
  • the material is batch heat- treated in coil form at a temperature less than or equal to 350°C for up to 18 hours.
  • higher batch annealing temperatures and shorter times may be used, subjecting the material to a temperature of about 400°C for approximately 1 hour.
  • the heat treatment times should be minimized to avoid excessive particle coarsening for reasons mentioned above.
  • the final gauge material is preferably subjected to a solutionizing step at a temperature of 480-580°C, preferably in a continuous anneal and solution heat treating line, and is the subjected to pre-aging.
  • a preferred pre-aging process involves rapidly cooling the sheet from the solutionizing temperature to a temperature in the range of 65 to 75°C, followed by slower cooling to ambient at a rate of ⁇ . 2°C/hour.
  • a more complex pre-aging process involves four uninterrupted cooling phases or sequences: first, from the solution heat treatment temperature to a temperature between about 350°C and about 220°C at a rate faster than 10°C/sec, but no more than 2000°C/sec; second, the alloy sheet is cooled from about 350°C to about 220°C to between about 270°C and about 140°C at a rate greater than about 1°C but less than about 50°C/second; third, further cooling to between about 120°C and about 50°C at a rate greater than 5°C/min. but less than 20°C/sec; and fourth, from between about 120°C and about 50°C to ambient temperature at a rate less than about 10°C/hr.
  • the above pre-aging (or quenching) process may be carried out with an additional step of coiling the sheet before the final step of cooling the sheet to ambient temperature at a rate less than 10°C/hour.
  • the quenching process may involve forced cooling the sheet by means of water cooling, water mist cooling or forced air cooling, and coiling the sheet at a temperature of 50 to 100°C, then allowing the coil to cool at a rate of less than about 10°C/hour.
  • the sheet most preferably exits the forced cooling at a temperature of between 120 to 150°C and the sheet is preferably coiled at a temperature of between 60°C and 85°C.
  • Figure 2 of the accompanying drawings shows a preferred procedure in those cases where cold rolling steps are not involved and hot rolling proceeds to final gauge. In both cases, quenching and pre-aging steps are carried out on the material of final gauge .
  • Figure 3 is representative of the apparatus employed for the various steps of the preferred form of the process of the invention.
  • a DC cast ingot 10 is first subjected to homogenization at 11 and then hot rolling in a rolling mill 12 to form a hot-rolled material (re-roll) in coil form 13.
  • the arrows 14, 15 and 16 indicate alternative routs.
  • Arrow 14 relate to a re-roll material 13 hot rolled to final gauge.
  • This material is subjected to a solutionizing step and pre-aging procedure in a continuous annealing and solutionizing heat treatment line 17 to give a final product in T4 temper suitable for delivery to an automobile parts manufacturer.
  • Arrow 15 indicates a route taken by hot rolled material 13 that is not in final gauge.
  • the material is first subjected to a cold rolling step at 18 to produce a material that is still not in final gauge.
  • This material is then subjected to a heat treatment in a batch annealing furnace 19 or in a continuous annealing line 20.
  • the heat treated product is then subjected to final cold rolling to gauge in a rolling mill 21, undergoing the stated reduction in thickness of 15% to less than 40%.
  • the same solutionizing and pre-aging steps may then be carried out in line 17, as previously described.
  • Arrow 16 shows the option of carrying out cold rolling only after the heat treatment in furnace 19 or line 20, as previously described (i.e., there is no preliminary cold rolling in mill 18 in this case) .
  • the subsequent steps are then the same as for the material following arrow 15.
  • cold rolling is either not employed at all, or it is used after the heat treatment to reduce the thickness of the intermediate product to final gauge by an amount in the range of 15% to less than 40%. If this degree of thickness reduction between the hot-rolled re-roll 13 and the final gauge product is not sufficient, preliminary cold rolling may be carried out prior to the heat treatment in rolling mill 18. The degree of thickness reduction produced by cold rolling prior to the heat treatment step does not influence the roping effect. It is cold rolling after this the heat treatment that has to be carefully controlled to avoid imparting roping characteristics to the product .
  • the process of the invention is designed to produce an optimized sheet material with a good combination of bend formability, surface appearance after forming and paint bake response.
  • the material produced in this manner is believed to be superior to the conventional product commercially available at the present time.
  • Tensile properties in the transverse direction were determined using standard ASTM specimens at a cross head speed of 2.54 mm/minute to 0.025 strain followed by 12.7 mm/minute to failure.
  • the bendability of the materials was determined using the standard ASTM E290-B7 test method.
  • the microstructure of the material was optically examined.
  • a roping test was performed by straining 45 mm wide panels by 15% in the transverse orientation and then lightly stoning the surface to highlight the topography.
  • Table 1 summarizes the properties of conventional and batch annealed materials as received from the plant .
  • Example 1 in Table 1 in the as-received and paint bake tempers are 140 MPa YS, 276 MPa UTS and 26%E1 and 269 MPa YS, 344 MPa and 19%E1, respectively.
  • the as-received material showed bend formabilities (r/t) of 0.4 and 0.5 in the longitudinal and transverse directions, respectively.
  • the grain size of the material was 35 x 15 ⁇ m.
  • the material showed considerable roping after straining 15% in the transverse orientation.
  • Example 2 and 3 in Table 1 represent properties of two AA6111 coils that were batch annealed together in a batch furnace.
  • the batch annealed material did not show roping and this is consistent with the teaching of the US Patent Nos . 4,897,124 and 5,480,498 assigned to Sky Aluminum and Reynolds Metal Company, respectively.
  • the batch annealed products could not provide paint bake strength to a level normally seen in the non-batch annealed product.
  • the properties of the batch annealed material are difficult to control in a commercial processing environment. This illustrates a need to develop a better fabrication process for automotive sheet applications.
  • Two ingots of AA6111 composition of commercial size were commercially direct chill cast.
  • the ingots were scalped and fully homogenized at 560°C.
  • One of the ingots was hot rolled to 2.54 mm gauge and the other was hot rolled to 2.3 mm gauge.
  • the hot rolled coils at 2.54 and 2.3 mm gauges were cold rolled to 1.5 and 1.3 mm gauges, respectively.
  • the cold rolled coils were then heat treated at 550°C in a continuous annealing furnace and rapidly cooled.
  • the heat treated coils at 1.5 and 1.3 mm gauge, respectively, were cold rolled by 33 and 20% to the final 1.0 mm gauge.
  • the cold rolled coils were solutionized at 550°C, rapidly cooled and coiled at between 65 and 75°C and then cooled to room temperature at a rate ⁇ 2°C/h.
  • the material was then subjected to the cut-to-length operation without any levelling.
  • the cut-to-length samples were used to characterize the materials .
  • the YS of the as-received materials in Table 2 are lower than that of Comparative Example 1 (Table 1) . This difference is primarily because the fact that the materials were not subjected to levelling operations.
  • the bend formability of the materials in Examples 1 and 2 are different from one another but represent an improvement from that of the regular material - compare Comparative Example 1 in Table 1 with Examples 1 and 2 in Table 2.
  • the paint bake response of the Examples 1 and 2 materials is better than those obtained from the batch annealed materials in Table 1.
  • the 33% cold rolled material showed reduced roping while 20% rolled material did not show any roping.
  • the surface appearance of the two materials after subjecting to the roping test were better than the conventional material.
  • the grain size of the 20% cold rolled material is higher than that of its 33% cold rolled counterpart .
  • the grain size ranges obtained from both these Examples are within the normal product range .
  • AA6111 composition One commercial sized ingot of AA6111 composition was direct chill cast, scalped, homogenized at 560 °C, hot and cold rolled to an intermediate 1.25 mm gauge. The material was then heat treated at 300°C for 4 hours in a batch furnace and cold rolled to the final 1.00 mm gauge. The cold rolled coils were solutionized at 550°C and rapidly cooled on a continuous annealing line, coiled at between 65 and 75 °C and then cooled to room temperature at a rate ⁇ 2°C/h. The material was sampled to evaluate different properties. The tensile properties of the AA6111 material are listed in Table 3.
  • the properties are similar to those obtained from Examples 1 and 2 in Table 2.
  • the bend formability and paint bake response are better than conventional material (Comparative Example 1 in Table 1) .
  • the roping characteristics of the material are also better than the conventional material.

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  • 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)
  • Metal Rolling (AREA)

Abstract

On décrit un procédé de production d'articles en feuille d'aluminium constituée d'un alliage d'aluminium des séries 6000 ou 2000, qui convient pour la fabrication de pièces pour véhicules automobiles. Le procédé consiste à couler l'alliage par refroidissement intense et direct pour obtenir un lingot moulé, puis à scalper le lingot moulé pour former un lingot scalpé. Il consiste ensuite à homogénéiser le lingot scalpé à une température comprise entre 480 et 580 °C pendant moins de 48 heures pour former un lingot homogénéisé, puis à laminer à chaud le lingot homogénéisé pour lui conférer un calibre intermédiaire et former un article d'épaisseur intermédiaire. Le procédé consiste enfin à laminer à froid l'article d'épaisseur intermédiaire pour lui conférer un calibre définitif. Le laminage à froid permet de réduire l'épaisseur de l'article en feuille intermédaire de l'ordre de 15 à 40 % par rapport au calibre définitif. En limitant le pourcentage de réduction obtenu par laminage à froid, on peut réduire ou supprimer l'effet de boudinage dans le produit fini présentant un degré de dureté T4 (normalement après mise en solution et pré-viellissement). En fait, les étapes du laminage à froid peuvent être supprimées complètement si l'on parvient à réduire convenablement l'épaisseur de la feuille uniquement par laminage à chaud.
EP98930576A 1997-06-20 1998-06-18 Procede de production d'une feuille en alliage d'aluminium apte au traitement thermique Expired - Lifetime EP0990058B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
US5034197P 1997-06-20 1997-06-20
US50341P 1997-06-20
PCT/CA1998/000596 WO1998059086A1 (fr) 1997-06-20 1998-06-18 Procede de production d'une feuille en alliage d'aluminium apte au traitement thermique

Publications (2)

Publication Number Publication Date
EP0990058A1 true EP0990058A1 (fr) 2000-04-05
EP0990058B1 EP0990058B1 (fr) 2003-11-26

Family

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP98930576A Expired - Lifetime EP0990058B1 (fr) 1997-06-20 1998-06-18 Procede de production d'une feuille en alliage d'aluminium apte au traitement thermique

Country Status (7)

Country Link
EP (1) EP0990058B1 (fr)
JP (1) JP2002508030A (fr)
BR (1) BR9810204A (fr)
CA (1) CA2294122A1 (fr)
DE (1) DE69820058T2 (fr)
NO (1) NO996280L (fr)
WO (1) WO1998059086A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11920229B2 (en) 2015-12-18 2024-03-05 Novelis Inc. High strength 6XXX aluminum alloys and methods of making the same

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US6780259B2 (en) * 2001-05-03 2004-08-24 Alcan International Limited Process for making aluminum alloy sheet having excellent bendability
DE102004030021B4 (de) * 2003-07-09 2009-11-26 Aleris Aluminum Duffel Bvba Gewalztes Produkt
CN104451477A (zh) * 2014-11-21 2015-03-25 广西南南铝加工有限公司 提高6xxx系铝合金烘烤硬化性能及自然时效稳定性的热处理方法
KR102063133B1 (ko) 2015-12-18 2020-01-07 노벨리스 인크. 고-강도 6xxx 알루미늄 합금 및 이것의 제조 방법
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
US11932928B2 (en) 2018-05-15 2024-03-19 Novelis Inc. High strength 6xxx and 7xxx aluminum alloys and methods of making the same
WO2020089007A1 (fr) * 2018-10-31 2020-05-07 Aleris Rolled Products Germany Gmbh Procédé de fabrication d'un produit en plaque d'alliage d'aluminium de la série 2xxx ayant une résistance améliorée à la rupture par fatigue
WO2020099124A1 (fr) * 2018-11-12 2020-05-22 Aleris Rolled Products Germany Gmbh Procédé de production d'une structure hydroformée à haute énergie à partir d'un alliage de la série 7xxx
EP3839085B1 (fr) 2019-12-17 2023-04-26 Constellium Neuf-Brisach Procédé amélioré de fabrication d'un composant de structure d'une carrosserie de véhicule automobile
CN114653771A (zh) * 2022-02-10 2022-06-24 山东南山铝业股份有限公司 一种绿色循环保级6系高成型汽车板生产方法

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US5616189A (en) * 1993-07-28 1997-04-01 Alcan International Limited Aluminum alloys and process for making aluminum alloy sheet
US5480498A (en) * 1994-05-20 1996-01-02 Reynolds Metals Company Method of making aluminum sheet product and product therefrom
US5582660A (en) * 1994-12-22 1996-12-10 Aluminum Company Of America Highly formable aluminum alloy rolled sheet
JPH11502264A (ja) * 1995-03-21 1999-02-23 カイザー アルミナム アンド ケミカル コーポレーシヨン 航空機用アルミニウムシートの製造方法
JP2001503473A (ja) * 1996-06-14 2001-03-13 アルミナム カンパニー オブ アメリカ 成形性の高いアルミニウム合金製圧延シート

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11920229B2 (en) 2015-12-18 2024-03-05 Novelis Inc. High strength 6XXX aluminum alloys and methods of making the same
US12043887B2 (en) 2015-12-18 2024-07-23 Novelis Inc. High strength 6xxx aluminum alloys and methods of making the same

Also Published As

Publication number Publication date
EP0990058B1 (fr) 2003-11-26
NO996280D0 (no) 1999-12-17
DE69820058D1 (de) 2004-01-08
CA2294122A1 (fr) 1998-12-30
WO1998059086A1 (fr) 1998-12-30
JP2002508030A (ja) 2002-03-12
BR9810204A (pt) 2000-10-17
NO996280L (no) 2000-02-21
DE69820058T2 (de) 2004-06-03

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