EP0990058B1 - Verfahren zur herstellung eines bleches aus wärmebehandlungsfähiger aluminium-legierung - Google Patents

Verfahren zur herstellung eines bleches aus wärmebehandlungsfähiger aluminium-legierung Download PDF

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Publication number
EP0990058B1
EP0990058B1 EP98930576A EP98930576A EP0990058B1 EP 0990058 B1 EP0990058 B1 EP 0990058B1 EP 98930576 A EP98930576 A EP 98930576A EP 98930576 A EP98930576 A EP 98930576A EP 0990058 B1 EP0990058 B1 EP 0990058B1
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Prior art keywords
article
gauge
temperature
ingot
cold rolling
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EP98930576A
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French (fr)
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EP0990058A1 (de
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Alok Kumar Gupta
Paul William Jeffrey
David James Lloyd
Gene Bruce Burger
Daniel Ronald Evans
Pierre Henry Marois
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Rio Tinto Alcan International Ltd
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Alcan International Ltd Canada
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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

  • 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.
  • 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 177°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 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. after hot rolling but before cold rolling, or after an early stage of cold rolling.
  • a batch annealing step e.g. heating at a temperature within the range of 316 to 538°C
  • 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 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, and the homogenized ingot is rolled to form a sheet article of final gauge, wherein said homogenized ingot is reduced in thickness 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 30% to reach final gauge, followed by cold rolling said article of intermediate gauge to form said sheet article of said final gauge, provided that, when both hot and cold rolling are employed to produce said article of intermediate gauge, a heat treatment step is carried out on said article of intermediate gauge to anneal said article, prior to said cold rolling to final gauge.
  • cold rolling may be taken to mean rolling operations carried out at temperatures from ambient to a maximum of about 150°C.
  • hot rolling may be taken to mean rolling operations carried out at temperatures of above about 300°C, and preferably at about 520°C.
  • 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 (30% or more), roping effects become unacceptable.
  • the cold rolling to final gauge preferably reduces the thickness of the alloy sheet by an amount in the range of 18% to less than 30% to said final gauge, more preferably 20 to 30%.
  • the process of the invention that employs cold rolling to intermediate gauge also employs a heat treating step (e.g. heating the sheet to a temperature in the range of 280-560°C for up to 18 hours) to bring about annealing at a stage in the reduction of the thickness of the sheet following, if necessary, the hot rolling step, e.g. before cold rolling commences, or, as claimed, between cold rolling steps when more than one is employed.
  • a heat treating step e.g. heating the sheet to a temperature in the range of 280-560°C for up to 18 hours
  • the hot rolling step e.g. before cold rolling commences, or, as claimed, between cold rolling steps when more than one is employed.
  • 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 30% 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. alloy AA6016.
  • 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 30% 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).
  • 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 is between 15% and less than 30%, and more preferably 18% to less than 30%, more 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 intermediate heat treatment preferably 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 1 of the accompanying drawings shows the use of cold rolling steps and an intermediate heat treatment.
  • Figure 2 of the accompanying drawings shows a procedure which does not belong to the invention 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.
  • FIG. 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 routes.
  • Arrow 14 relate to a re-roll material 13 hot rolled to final gauge, a procedure not belonging to the invention.
  • 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 30%.
  • 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 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 30%. 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.
  • Mechanical Properties of AA6111 Alloys in Different Tempers Comparative Example No. Tempers Tensile Properties Min. Bend Radius Roping Mean Grain Size L x T, ⁇ m YS MPa UTS MPa %El n L T 1
  • Batch Annealing As-received 116 240 25 0.28 0.40 0.30 No 23 x 19 Paint-Bake 205 283 20 -- - -- -- -- -- 3 Batch Annealing As-received 131 259 25 0.27 0.49 0.39 No 27 x 18 Paint Bake 235 312 21 -- -- -- - --
  • Example 1 in Table 1 in the as-received and paint bake tempers are 140 MPa YS, 276 MPa UTS and 26%El and 269 MPa YS, 344 MPa and 19%El, 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. It can be seen that the properties of the two coils differed significantly from each other, which clearly shows problems associated with the batch annealing process when attempting to achieve consistent properties. These differences were due to the differences in the amount of precipitated coarse Mg 2 Si/Si. The alloy of Example 2 showed more coarse particles than those in Example 3. Generally, the paint bake responses of the batch annealed material was lower than its non-batch annealed counterpart (compare Example 1 with Examples 2 and 3 in Table 1). As mentioned above, this difference is mostly related to the fact that the batch annealed material does not respond to the pre-aging treatment.
  • 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.
  • 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. Mechanical Properties of AA6111 Alloy Produced According to the Present Invention Example No. Tempers Tensile Properties Min. Bend Radius Roping Mean Grain Size L x T, ⁇ m YS MPa UTS MPa %EI n L T 3 As-received 124 260 26 0.29 0.3 0.3 No 48 x 19 Paint-Bake 254 329 20 -- -- -- -- --
  • 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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Claims (9)

  1. Verfahren zur Herstellung von Blechartikeln aus Aluminiumlegierung der 6000er Serie, worin ein Gußbarren durch Direktkühlguß gebildet wird, der Barren wird unter Bildung eines geschälten Barrens geschält, der geschälte Barren wird bei einer Temperatur zwischen 480 und 580°C für weniger als 48 Stunden homogenisiert, wodurch ein homogenisierter Barren gebildet wird, und der Barren wird unter Ausbildung eines Blechartikels auf Enddicke gewalzt, worin die Dicke des homogenisierten Barrens durch Heiß- und gegebenenfalls Kaltwalzen verringert wird, wodurch ein Artikel in Zwischendicke gebildet wird, der eine Verringerung der Dicke im Bereich von 15 bis weniger als 30 % zum Erreichen der Enddicke benötigt, gefolgt von Kaltwalzen des Artikels in Zwischendicke, wodurch der Blechartikel in Enddicke gebildet wird, mit der Maßgabe, daß wenn sowohl Heißals auch Kaltwalzen zur Herstellung des Artikels in Zwischendicke angewandt wird, ein Wärmebehandlungsschritt mit dem Artikel in Zwischendicke zur Temperung des Artikels vor dem Kaltwalzen auf die Enddicke durchgeführt wird.
  2. Verfahren gemäß Anspruch 1, dadurch gekennzeichnet, daß durch das Heißwalzen ein Artikel in Zwischendicke gebildet wird, der eine weitere Verringerung der Dicke von 18 bis weniger als 30 % zum Erreichen der Enddicke benötigt.
  3. Verfahren gemäß Anspruch 1, dadurch gekennzeichnet, daß durch das Heißwalzen ein Artikel in Zwischendicke gebildet wird, der eine weitere Verringerung der Dicke von 20 bis weniger als 30 % zum Erreichen der Enddicke benötigt.
  4. Verfahren gemäß Anspruch 1, dadurch gekennzeichnet, daß mindestens ein Kaltwalzschritt nach dem Heißwalzschritt zur Vervollständigung der Ausbildung des Artikels in Zwischendicke angewandt wird.
  5. Verfahren gemäß Anspruch 1, dadurch gekennzeichnet, daß die Wärmebehandlung die Erwärmung des Artikels auf eine Temperatur im Bereich von 280 bis 560°C für bis zu 18 Stunden umfaßt.
  6. Verfahren gemäß mindestens einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, daß ein Lösungsbehandlungsschritt mit dem Artikel in Enddicke durchgeführt wird.
  7. Verfahren gemäß Anspruch 6, dadurch gekennzeichnet, daß der Lösungsbehandlungsschritt bei einer Temperatur im Bereich von 480 bis 580°C durchgeführt wird.
  8. Verfahren gemäß Anspruch 6 oder 7, dadurch gekennzeichnet, daß der Artikel im Anschluß an den Lösungsbehandlungsschritt mit einer Geschwindigkeit von mehr als 2°C/h auf eine Zwischentemperatur und dann von dieser Zwischentemperatur mit einer Geschwindigkeit von 2°C/h oder weniger auf Umgebungstemperatur abgekühlt wird.
  9. Verfahren gemäß mindestens einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, daß die Aluminiumlegierung AA6111 ist.
EP98930576A 1997-06-20 1998-06-18 Verfahren zur herstellung eines bleches aus wärmebehandlungsfähiger aluminium-legierung Expired - Lifetime EP0990058B1 (de)

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US5034197P 1997-06-20 1997-06-20
US50341P 1997-06-20
PCT/CA1998/000596 WO1998059086A1 (en) 1997-06-20 1998-06-18 Process of producing heat-treatable aluminum alloy sheet

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EP0990058A1 EP0990058A1 (de) 2000-04-05
EP0990058B1 true EP0990058B1 (de) 2003-11-26

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JP (1) JP2002508030A (de)
BR (1) BR9810204A (de)
CA (1) CA2294122A1 (de)
DE (1) DE69820058T2 (de)
NO (1) NO996280L (de)
WO (1) WO1998059086A1 (de)

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DE102004030021A1 (de) * 2003-07-09 2005-05-04 Corus Aluminium Nv Aluminiumlegierung
EP3341502B1 (de) 2015-12-18 2021-03-17 Novelis Inc. Verfahren zur herstellung von hochfesten 6xxx-aluminiumlegierungen
EP3555332B1 (de) 2016-12-16 2022-01-26 Novelis Inc. Hochfeste und hochverformbare aluminiumlegierungen, die gegen natürliche altershärtung resistent sind, und verfahren zur herstellung davon

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US6780259B2 (en) * 2001-05-03 2004-08-24 Alcan International Limited Process for making aluminum alloy sheet having excellent bendability
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
KR102228792B1 (ko) 2015-12-18 2021-03-19 노벨리스 인크. 고 강도 6ｘｘｘ 알루미늄 합금들 및 이를 만드는 방법들
WO2019222236A1 (en) 2018-05-15 2019-11-21 Novelis Inc. High strength 6xxx and 7xxx aluminum alloys and methods of making the same
CN112969806B (zh) * 2018-10-31 2022-07-05 爱励轧制产品德国有限责任公司 制造具有改善的耐疲劳失效性的2xxx系列铝合金板材产品的方法
US20220002853A1 (en) * 2018-11-12 2022-01-06 Airbus Sas Method of producing a high-energy hydroformed structure from a 7xxx-series alloy
EP3839085B1 (de) 2019-12-17 2023-04-26 Constellium Neuf-Brisach Verbessertes verfahren zur herstellung eines strukturteils für eine kraftfahrzeugkarosserie
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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US5582660A (en) * 1994-12-22 1996-12-10 Aluminum Company Of America Highly formable aluminum alloy rolled sheet
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EP3341502B1 (de) 2015-12-18 2021-03-17 Novelis Inc. Verfahren zur herstellung von hochfesten 6xxx-aluminiumlegierungen
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CA2294122A1 (en) 1998-12-30
WO1998059086A1 (en) 1998-12-30
BR9810204A (pt) 2000-10-17
JP2002508030A (ja) 2002-03-12
DE69820058T2 (de) 2004-06-03
NO996280L (no) 2000-02-21
NO996280D0 (no) 1999-12-17
EP0990058A1 (de) 2000-04-05

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