EP2270249A1 - Bande AIMgSi pour applications ayant des exigences de déformation élevées - Google Patents

Bande AIMgSi pour applications ayant des exigences de déformation élevées Download PDF

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Publication number
EP2270249A1
EP2270249A1 EP09164221A EP09164221A EP2270249A1 EP 2270249 A1 EP2270249 A1 EP 2270249A1 EP 09164221 A EP09164221 A EP 09164221A EP 09164221 A EP09164221 A EP 09164221A EP 2270249 A1 EP2270249 A1 EP 2270249A1
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EP
European Patent Office
Prior art keywords
hot
strip
aluminum
rolling
alloy
Prior art date
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Granted
Application number
EP09164221A
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German (de)
English (en)
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EP2270249B1 (fr
EP2270249B2 (fr
Inventor
Henk-Jan Brinkman
Thomas Dr. Wirtz
Dietmar Schröder
Eike Brünger
Kai-Friedrich Karhausen
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Hydro Aluminium Deutschland GmbH
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Hydro Aluminium Deutschland GmbH
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Application filed by Hydro Aluminium Deutschland GmbH filed Critical Hydro Aluminium Deutschland GmbH
Priority to EP09164221.5A priority Critical patent/EP2270249B2/fr
Priority to ES09164221T priority patent/ES2426226T3/es
Priority to ES10723562T priority patent/ES2746846T3/es
Priority to KR1020127001479A priority patent/KR101401060B1/ko
Priority to RU2012102976/02A priority patent/RU2516214C2/ru
Priority to JP2012518057A priority patent/JP5981842B2/ja
Priority to EP10723562.4A priority patent/EP2449145B1/fr
Priority to CA2766327A priority patent/CA2766327C/fr
Priority to CN201080029594.9A priority patent/CN102498229B/zh
Priority to PCT/EP2010/057071 priority patent/WO2011000635A1/fr
Publication of EP2270249A1 publication Critical patent/EP2270249A1/fr
Priority to US13/340,225 priority patent/US10047422B2/en
Publication of EP2270249B1 publication Critical patent/EP2270249B1/fr
Priority to US14/928,122 priority patent/US10612115B2/en
Publication of EP2270249B2 publication Critical patent/EP2270249B2/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
    • C22F1/043—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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002—Castings of light metals
    • B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D7/00—Casting ingots, e.g. from ferrous metals
    • B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • 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
    • 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
    • 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 invention relates to a method for producing a strip from an AlMgSi alloy, in which an ingot of AlMgSi alloy is cast, the roll ingot is subjected to homogenization, the roll bar rolled to rolling temperature is hot rolled and then optionally cold rolled to final thickness. Moreover, the invention relates to an aluminum strip of an AlMgSi alloy and its advantageous use.
  • AlMgSi alloys whose main alloying components are magnesium and Are silicon, have relatively high strength at the same time good forming behavior and excellent corrosion resistance.
  • AlMgSi alloys are the alloy types AA6XXX, for example, the alloy types AA6016, AA6014, AA6181, AA6060 and AA6111.
  • aluminum tapes of AlMgSi alloy are produced by casting a roll bar, homogenizing the roll bar, hot rolling the roll bar, and cold rolling the hot strip. The homogenisation of the rolling ingot takes place at a temperature of 380 to 580 ° C for more than one hour.
  • the tapes can be delivered in condition T4.
  • the state T6 is set after quenching by thermal aging at temperatures between 100 ° C and 220 ° C.
  • the problem is that coarse Mg 2 Si precipitates are present in hot-rolled aluminum strips of AlMgSi alloys, which are broken and reduced in the subsequent cold rolling by high degrees of deformation.
  • Hot strips of AlMgSi alloy are usually produced in thicknesses of 3 mm to 12 mm and fed to a cold rolling with high degrees of deformation. Since the temperature range in which the AlMgSi phases form, is traversed very slowly during conventional hot rolling, these phases form very coarse.
  • the temperature range for forming the above-mentioned phases is alloy-dependent but is between 550 ° C and 230 ° C. It was experimentally proven that these coarse phases in the hot strip negatively influence the elongation of the end product. This means that the forming behavior of Aluminum strips of AlMgSi alloys could not be fully exploited.
  • the present invention is therefore based on the object to provide a method for producing an aluminum strip of an AlMgSi alloy and an aluminum strip available, which has a higher elongation in the state T4 and thus allows higher degrees of deformation in the production of structural components.
  • the present invention is based on the object to propose advantageous uses of a sheet produced from the aluminum strip according to the invention.
  • the above-described object is achieved for a method for producing a strip of an AlMgSi alloy, that the hot strip immediately after the discharge from the last hot roll pass a temperature of 130 ° C, preferably a temperature of has a maximum of 100 ° C and the hot strip is wound at this or a lower temperature.
  • the size of the Mg 2 Si precipitates in a hot strip of an AlMgSi alloy can be significantly reduced by quenching, ie by accelerated cooling. Due to the rapid cooling from a hot strip temperature between 230 ° C and 550 ° C to a maximum of 130 ° C, preferably at most 100 ° C at the outlet of the last hot roll pass, the microstructure state of the hot strip is frozen, so that coarse precipitates can no longer form.
  • the resulting aluminum strip after solution heat treatment and quenching to final thickness, exhibits significantly improved elongation at conventional T4 state strengths and an equal or even improved curability to state T6. This combination of properties has not yet been achieved for strips of AlMgSi alloys.
  • this cooling process takes place within the last two hot rolling passes, i. cooling to 130 ° C and less takes place within seconds, within a maximum of five minutes. It has been shown that in this procedure, the increased elongation values at the usual strength or expansion limits in the condition T4 and the improved hardenability in the condition T6 are achieved particularly reliably.
  • a particularly economical realization of the method is achieved by quenching the hot strip itself to coiling temperature using at least one sinker cooler and the hot rolling passes applied with emulsion.
  • a board cooler consists of an array of coolant or lubricant nozzles which spray a rolling emulsion onto the aluminum strip.
  • the sinker cooler is often present in a hot rolling mill to cool rolled hot strip to roll temperature before hot rolling and to set the coiling temperature.
  • the method according to the invention can thus be used on conventional systems without special ancillary equipment.
  • the hot rolling temperature is above the recrystallization temperature of a metal, that is, above 230 ° C for aluminum.
  • the coiling temperature is 130 ° C but well below these normal process conditions.
  • the hot rolling temperature of the hot strip prior to the penultimate hot rolling pass at least 230 ° C, preferably above 400 ° C is achieved according to a next embodiment of the method that particularly small Mg 2 Si precipitates are present in the quenched hot strip, since the largest proportion of alloying components Magnesium and silicon are present at these temperatures in the dissolved state in the aluminum matrix.
  • This advantageous state of the hot strip is quasi “frozen” by quenching.
  • the thickness of the finished hot strip is 3 mm to 12 mm, preferably 3.5 mm to 8 mm, so that conventional cold rolling stands for cold rolling can be used.
  • the aluminum alloy used is of the alloy type AA6xxx, preferably AA6014, AA6016, AA6060, AA6111 or AA6181.
  • All alloy types AA6xxx have in common that they have a particularly good forming behavior characterized by high elongation values in the state T4 and very high strength or yield strength in use state T6, for example, after a heat aging at 205 ° C / 30 min.
  • An aluminum alloy of the type AA6016 has the following alloy constituents in percent by weight: 0 . 25 % ⁇ mg ⁇ 0 . 6 % . 1 . 0 % ⁇ Si ⁇ 1 . 5 % . Fe ⁇ 0 . 5 % . Cu ⁇ 0 . 2 % . Mn ⁇ 0 . 2 % . Cr ⁇ 0 . 1 % . Zn ⁇ 0 . 1 % . Ti ⁇ 0 . 1 % and residual Al and unavoidable impurities in the sum total of 0.15%, individually a maximum of 0.05%.
  • the manganese content of less than 0.2% by weight reduces the tendency to form coarser manganese precipitates.
  • chromium ensures a fine microstructure, it should be limited to 0.1% by weight in order to avoid coarse precipitation.
  • the presence of manganese improved the weldability by reducing the tendency to crack or quenching sensitivity of the aluminum strip according to the invention.
  • a reduction of the zinc content to a maximum of 0.1% by weight improves in particular the corrosion resistance of the aluminum alloy or of the finished sheet in the respective application.
  • titanium provides grain refining during casting, but should be limited to a maximum of 0.1% by weight to ensure good castability of the aluminum alloy.
  • An aluminum alloy of the type AA6060 has the following alloy constituents in percent by weight: 0 . 35 % ⁇ mg ⁇ 0 . 6 % . 0 . 3 % ⁇ Si ⁇ 0 . 6 % . 0 . 1 % ⁇ Fe ⁇ 0 . 3 % Cu ⁇ 0 . 1 % . Mn ⁇ 0 . 1 % . Cr ⁇ 0 . 05 % . Zn ⁇ 0 . 10 % . Ti ⁇ 0 . 1 % and Residual Al and unavoidable impurities up to a total of 0.15%, individually up to a maximum of 0.05%.
  • the combination of a precisely predetermined magnesium content with a reduced Si content and narrowly specified Fe content in comparison to the first embodiment results in an aluminum alloy in which the formation of Mg 2 Si precipitates after hot rolling can be prevented particularly well by the method according to the invention, so that a sheet with improved elongation and high yield strengths can be provided compared to conventionally produced sheets.
  • the lower upper limits of the alloy components Cu, Mn and Cr additionally reinforce the effect of the method according to the invention. With regard to the effects of the upper limit of Zn and Ti, reference is made to the comments on the first embodiment of the aluminum alloy.
  • An aluminum alloy of type AA6014 has the following alloy constituents in percent by weight: 0 . 4 % ⁇ mg ⁇ 0 . 8th % . 0 . 3 % ⁇ Si ⁇ 0 . 6 % . Fe ⁇ 0 . 35 % Cu ⁇ 0 . 25 % . 0 . 05 % ⁇ Mn ⁇ 0 . 20 % . Cr ⁇ 0 . 20 % . Zn ⁇ 0 . 10 % . 0 . 05 % ⁇ V ⁇ 0 . 20 % . Ti ⁇ 0 . 1 % and Residual Al and unavoidable impurities up to a total of 0.15%, individually up to a maximum of 0.05%.
  • An AA6181 aluminum alloy has the following alloy components in weight percent: 0 . 6 % ⁇ mg ⁇ 1 . 0 % . 0 . 8th % ⁇ Si ⁇ 1 . 2 % . Fe ⁇ 0 . 45 % C ⁇ u ⁇ 0 . 10 % . Mn ⁇ 0 . 15 % . Cr ⁇ 0 . 10 % . Zn ⁇ 0 . 20 % . Ti ⁇ 0 . 1 % and Residual Al and unavoidable impurities up to a total of 0.15%, individually up to a maximum of 0.05%.
  • An AA6111 aluminum alloy has the following alloy components in weight percent: 0 . 5 % ⁇ mg ⁇ 1 . 0 % . 0 . 7 % ⁇ Si ⁇ 1 . 1 % . Fe ⁇ 0 . 40 % 0 . 50 % ⁇ Cu ⁇ 0 . 90 % . 0 . 15 % ⁇ Mn ⁇ 0 . 45 % . Cr ⁇ 0 . 10 % . Zn ⁇ 0 . 15 % . Ti ⁇ 0 . 1 % and Residual Al and unavoidable impurities up to a total of 0.15%, individually up to a maximum of 0.05%. Due to the increased copper content, the AA6111 alloy generally shows higher strength values in the T6 application, but is to be classified as more susceptible to corrosion.
  • All the aluminum alloys shown are specifically adapted to different applications in their alloy components. As already stated, they show particularly high elongation values in the state T4 paired with a particularly pronounced increase in the yield strength, for example after heat aging at 205 ° C./30 min.
  • the above-described object is achieved by an aluminum strip consisting of an AlMgSi alloy in that the aluminum strip in state T4 has an elongation at break A 80 of at least 30% at a yield strength Rp0.2 of 80 to 140 MPa having.
  • the delivery state T4 is usually achieved by solution treatment with quenching and subsequent storage at room temperature for at least three days, since then the properties of the solution-annealed sheet or strip are stable.
  • the combination of breaking elongation A 80 and yield strength Rp0.2 of the aluminum strip according to the invention has not been achieved with previously known AlMgSi alloys.
  • the aluminum strip according to the invention therefore permits maximum degrees of deformation due to the high elongation values with maximum values for the yield strength Rp0.2 in the finished sheet metal or component.
  • the aluminum strip according to the invention preferably has a yield strength Rp0.2 of greater than 185 MPa at an elongation A 80 of at least 15% in the condition T6, that is to say in the use or application state. These values were measured in the aluminum tapes according to the invention in the condition T6, which have undergone a heat aging at 205 ° C / 30 min. After a solution heat treatment and quenching (state T4). Due to the high yield strengths in the state T6 with very good elongation values in the state T4, the aluminum strip according to the invention is suitable, for example, for use in the Motor vehicle construction particularly well suited.
  • the increase in the yield strength from state T4 to state T6 is particularly high in the case of the aluminum strip according to the invention.
  • the aluminum strip according to the invention can therefore be formed very well in the condition T4 and then be put into a high-strength use state (state T6) by heat aging. With the necessary, complex shapes and the required high strength values or yield strengths, for example in motor vehicle construction, good hardenability for the production of complex components is of particular advantage.
  • the aluminum strips have a thickness of 0.5 mm to 12 mm.
  • Aluminum strips with thicknesses of 0.5 mm to 2 mm are preferably used for body parts, for example in the automotive industry, while aluminum bands with larger thicknesses of 2 to 4.5 mm, for example, find in chassis parts in automotive applications.
  • Individual components can also be manufactured in a cold-rolled strip with a thickness of up to 6 mm.
  • aluminum strips with thicknesses of up to 12 mm can be used. These very thick aluminum strips are usually provided only by hot rolling.
  • the aluminum alloy of the aluminum strip is of the alloy type AA6xxx, preferably AA6014, AA6016, AA6060, AA6111 or AA6181.
  • the above object according to a third teaching of the present invention by the use of a sheet produced from an aluminum strip according to the invention as a component, suspension or structural part and sheet metal in automotive, aircraft or rail vehicle, in particular as a component, chassis part, outer or inner panel in the automotive industry, preferably as a body component solved.
  • visible body parts, such as hoods, fenders, etc., as well as outer skin parts of a rail vehicle or aircraft benefit from the high yield strengths Rp0.2 with good surface properties even after forming with high degrees of deformation.
  • FIG. 1 shows in the only one FIG. 1 a schematic flow diagram of an embodiment of the inventive method for producing a tape from an AlMgSi aluminum alloy comprising the steps of a) producing and homogenizing the rolling ingot, b) hot rolling, c) cold rolling and d) quenching solution annealing.
  • an aluminum alloy ingot 1 having the following alloy components by weight is poured: 0 . 35 % ⁇ mg ⁇ 0 . 6 % . 0 . 3 % ⁇ Si ⁇ 0 . 6 % . 0 . 1 % ⁇ Fe ⁇ 0 . 3 % Cu ⁇ 0 . 1 % . Mn ⁇ 0 . 1 % . Cr ⁇ 0 . 05 % . Zn ⁇ 0 . 1 % . Ti ⁇ 0 . 1 % and Residual Al and unavoidable impurities up to a total of 0.15%, individually up to a maximum of 0.05%.
  • the ingot produced in this way is homogenized in a furnace 2 for 8 hours at a homogenization temperature of about 550 ° C., so that the alloyed components alloyed in are present in a particularly homogeneous distribution in the rolling ingot.
  • Fig. 1a The ingot produced in this way is homogenized in a furnace 2 for 8 hours at a homogenization temperature of about 550 ° C., so that the alloyed components alloyed in are present in a particularly homogeneous distribution in the rolling ingot.
  • Fig. 1a The ingot produced in this way is homogenized in a furnace 2 for 8 hours at a homogenization temperature of about 550 ° C.
  • the hot strip 4 after leaving the hot rolling mill 3 and before the penultimate hot rolling pass, the hot strip 4 preferably has a temperature of at least 400 ° C.
  • the work rolls of the hot rolling stand 3 are subjected to emulsion and cool the hot strip 4 further down. After the last rolling pass, the hot strip 4 at the outlet of the sinker cooler 5 'in the present embodiment, only a temperature of 95 ° C and will then be wound on the take-up reel 6.
  • the hot strip 4 has a temperature of at most 130 ° C or at most 100 ° C immediately at the outlet of the last hot rolling pass or optionally in the last two hot rolling passes using the sinker 5 and the work rolls of the hot rolling mill 3 to a temperature below 130 ° C or below 100 ° C, the hot strip 4 has a frozen crystal structure state, since no additional energy in the form of heat is available for subsequent precipitation operations.
  • the hot strip with a thickness of 3 to 12 mm, preferably 3.5 to 8 mm is wound on the take-up reel 6.
  • the coiling temperature in the present embodiment is less than 95 ° C.
  • the hot strip 4 has a very favorable for further processing crystal state and can be unwound from the unwinding reel 7, for example, fed to a cold rolling mill 9 and rewound on a take-up reel 8, Fig. 1c ).
  • the resulting cold-rolled strip 11 is wound up. Subsequently, it is supplied to a solution annealing and quenching 10, Fig. 1d ). For this purpose, it is again unwound from the coil 12, solution-annealed in an oven 10 and quenched again wound into a coil 13.
  • the aluminum strip can then be delivered after a cold aging at room temperature in the state T4 with maximum formability. Alternatively (not shown), the aluminum strip 11 can be singulated into individual sheets, which are present after a cold aging in the state T4.
  • the aluminum strip or the aluminum sheet is brought by cold aging at 100 ° C to 220 ° C in order to achieve maximum values for the yield strength. For example, a hot aging at 205 ° C / 30 min. Performed.
  • the aluminum strips produced according to the illustrated embodiment for example, after cold rolling a thickness of 0.5 to 4.5 mm.
  • Tape thicknesses of 0.5 to 2 mm are commonly used for car body applications or tape thicknesses of 2.0 mm to 4.5 mm for chassis parts in the automotive industry.
  • the improved elongation values in the manufacture of the components are of decisive advantage, since in most cases strong deformation of the sheets is carried out and nevertheless high strengths in the operating condition (T6) of the end product are required.
  • Table 1 shows the alloy compositions of aluminum alloys from which aluminum tapes have been produced conventionally or according to the invention.
  • the aluminum strips contain aluminum and impurities as a residual proportion, individually not more than 0.05% by weight and in total not more than 0.15% by weight.
  • Table 1 rehearse Si% by weight Fe% by weight Cu% by weight Mn% by weight Mg% by weight Cr% by weight Zn% by weight Ti% by weight 409 1.29 0.17 0.001 0.057 0.29 ⁇ 0.0005 ⁇ 0.001 0.02 410 1.30 0.17 0.001 0.056 0.29 ⁇ 0.0005 ⁇ 0.001 0.0172 491-1 1.39 0.18 0,002 0.062 0.30 0.0006 0.01 0.0158 491-11 1.40 0.18 0,002 0.063 0.31 0.0006 0.0104 0.0147
  • the belts 409 and 410 were made by a process according to the invention in which the hot strip was cooled and wound up within the last two hot rolling passes from about 400 ° C to 95 ° C using a sinker cooler and the hot rolls themselves. Table 2 shows the measured values of these samples as "Inv.” characterized. Subsequently, a cold rolling to a final thickness of 1.04 mm.
  • Samples 491-1 and 491-11 were made with conventional hot rolling and cold rolling and with a "conv.” characterized.
  • Table 2 rehearse T4 T6 205 ° C / 30 min. thickness (mm) Rp0.2 (MPa) R m (MPa) A 80 (%) Rp0.2 (MPa) R m (MPa) A 80 (%) ⁇ Rp0,2 (MPa) 409 Inv. 1.04 100 220 31.3 187 251 16.2 87 410 Inv. 1.04 98 217 30.3 195 256 15.5 97 491-1 Conv. 1.04 92 202 27.8 180 235 14.7 88 491-11 Conv. 1.04 88 196 27.4 179 232 14.3 91
  • the samples were subjected to solution annealing with subsequent quenching and subsequent cold aging at room temperature.
  • the T6 state was achieved by hot aging at 205 ° C for 30 minutes.
  • the measured values could be verified in state T4 by measurements on other bands.
  • the aluminum alloy of Samples A and B had the following composition: 0 . 25 % ⁇ mg ⁇ 0 . 6 % . 1 . 0 % ⁇ Si ⁇ 1 . 5 % . Fe ⁇ 0 . 5 % . Cu ⁇ 0 . 2 % . Mn ⁇ 0 . 2 % . Cr ⁇ 0 . 1 % . Zn ⁇ 0 . 1 % . Ti ⁇ 0 . 1 % and residual Al and unavoidable impurities in the sum total of 0.15%, individually a maximum of 0.05%.
  • Samples A and B were wound to 95 ° C using the quenching process of the present invention within the last two hot rolling passes and then cold rolled to a final thickness of 1.0 mm and 3.0 mm, respectively.
  • samples A and B were solution annealed and cold-aged after quenching.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)
EP09164221.5A 2009-06-30 2009-06-30 Bande AIMgSi pour applications ayant des exigences de déformation élevées Active EP2270249B2 (fr)

Priority Applications (12)

Application Number Priority Date Filing Date Title
EP09164221.5A EP2270249B2 (fr) 2009-06-30 2009-06-30 Bande AIMgSi pour applications ayant des exigences de déformation élevées
ES09164221T ES2426226T3 (es) 2009-06-30 2009-06-30 Banda de AlMgSi para aplicaciones con altos requisitos de conformación
CN201080029594.9A CN102498229B (zh) 2009-06-30 2010-05-21 用于高变形要求的铝镁硅带材
PCT/EP2010/057071 WO2011000635A1 (fr) 2009-06-30 2010-05-21 Bande en almgsi pour applications à exigences élevées de déformation
RU2012102976/02A RU2516214C2 (ru) 2009-06-30 2010-05-21 Al-Mg-Si-ПОЛОСА ДЛЯ ПРИМЕНЕНИЙ С ВЫСОКИМИ ТРЕБОВАНИЯМИ К ФОРМУЕМОСТИ
JP2012518057A JP5981842B2 (ja) 2009-06-30 2010-05-21 高い成形性要求を有する用途のためのＡｌＭｇＳｉストリップ
EP10723562.4A EP2449145B1 (fr) 2009-06-30 2010-05-21 Bande AIMgSi pour applications ayant des exigences de déformation élevées
CA2766327A CA2766327C (fr) 2009-06-30 2010-05-21 Bande en almgsi pour applications a exigences elevees de deformation
ES10723562T ES2746846T3 (es) 2009-06-30 2010-05-21 Banda de AlMgSi para aplicaciones con altos requerimientos de conformación
KR1020127001479A KR101401060B1 (ko) 2009-06-30 2010-05-21 높은 소성 요구에 적용하기 위한 ａｌｍｇｓｉ 스트립
US13/340,225 US10047422B2 (en) 2009-06-30 2011-12-29 AlMgSi strip for applications having high formability requirements
US14/928,122 US10612115B2 (en) 2009-06-30 2015-10-30 AlMgSi strip for applications having high formability requirements

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP09164221.5A EP2270249B2 (fr) 2009-06-30 2009-06-30 Bande AIMgSi pour applications ayant des exigences de déformation élevées

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EP2270249A1 true EP2270249A1 (fr) 2011-01-05
EP2270249B1 EP2270249B1 (fr) 2013-05-29
EP2270249B2 EP2270249B2 (fr) 2020-05-27

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EP09164221.5A Active EP2270249B2 (fr) 2009-06-30 2009-06-30 Bande AIMgSi pour applications ayant des exigences de déformation élevées
EP10723562.4A Revoked EP2449145B1 (fr) 2009-06-30 2010-05-21 Bande AIMgSi pour applications ayant des exigences de déformation élevées

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US (2) US10047422B2 (fr)
EP (2) EP2270249B2 (fr)
JP (1) JP5981842B2 (fr)
KR (1) KR101401060B1 (fr)
CN (1) CN102498229B (fr)
CA (1) CA2766327C (fr)
ES (2) ES2426226T3 (fr)
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EP2570509A1 (fr) 2011-09-15 2013-03-20 Hydro Aluminium Rolled Products GmbH Procédé de fabrication pour une bande d'aluminium AlMgSi
EP2570257A1 (fr) 2011-09-15 2013-03-20 Hydro Aluminium Rolled Products GmbH Matière première composite en aluminium dotée d'une couche d'alliage centrale AIMgSi
EP3060358B1 (fr) 2013-10-25 2017-11-15 SMS group GmbH Train de laminage à chaud de bandes d'aluminium et procédé de laminage à chaud d'une bande d'aluminium
EP3622096B1 (fr) 2017-05-11 2021-09-22 Aleris Aluminum Duffel BVBA Procédé de fabrication d'un produit en feuille laminé en alliage al-si-mg ayant une excellente formabilité

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DE102013108127A1 (de) 2012-08-23 2014-02-27 Ksm Castings Group Gmbh Al-Gusslegierung
WO2014121785A1 (fr) 2013-02-06 2014-08-14 Ksm Castings Group Gmbh Alliage d'al de fonderie
FR3008427B1 (fr) * 2013-07-11 2015-08-21 Constellium France Tole en alliage d'aluminium pour structure de caisse automobile
EP3497256B1 (fr) * 2016-08-15 2020-07-01 Hydro Aluminium Rolled Products GmbH Alliage d'aluminium pour la protection des piétons contre la collision
CA3093126C (fr) * 2018-05-15 2023-07-18 Novelis Inc. Produits d'alliage d'aluminium a trempe f* et w et procedes de fabrication associes
EP3825428B1 (fr) * 2019-11-25 2022-11-16 AMAG casting GmbH Composant moulé sous pression et procédé de fabrication d'un composant moulé sous pression

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Cited By (11)

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Publication number Priority date Publication date Assignee Title
EP2570509A1 (fr) 2011-09-15 2013-03-20 Hydro Aluminium Rolled Products GmbH Procédé de fabrication pour une bande d'aluminium AlMgSi
EP2570257A1 (fr) 2011-09-15 2013-03-20 Hydro Aluminium Rolled Products GmbH Matière première composite en aluminium dotée d'une couche d'alliage centrale AIMgSi
WO2013037919A1 (fr) 2011-09-15 2013-03-21 Hydro Aluminium Rolled Products Gmbh Procédé de fabrication d'une bande d'aluminium almgsi
WO2013037918A1 (fr) 2011-09-15 2013-03-21 Hydro Aluminium Rolled Products Gmbh Matériau composite d'aluminium comportant une couche centrale en alliage almgsi
KR20150126975A (ko) * 2011-09-15 2015-11-13 하이드로 알루미늄 롤드 프로덕츠 게엠베하 Almgsi 알루미늄 스트립 제조 방법
RU2576976C2 (ru) * 2011-09-15 2016-03-10 Гидро Алюминиум Ролд Продактс Гмбх СПОСОБ ПРОИЗВОДСТВА AlMgSi ПОЛОСЫ
US9796157B2 (en) 2011-09-15 2017-10-24 Hydro Aluminium Rolled Products Gmbh Aluminium composite material with AlMgSi core layer
KR101974624B1 (ko) 2011-09-15 2019-05-02 하이드로 알루미늄 롤드 프로덕츠 게엠베하 Almgsi 알루미늄 스트립 제조 방법
US10471684B2 (en) 2011-09-15 2019-11-12 Hydro Aluminium Rolled Products Gmbh Aluminium composite material with AlMgSi core layer
EP3060358B1 (fr) 2013-10-25 2017-11-15 SMS group GmbH Train de laminage à chaud de bandes d'aluminium et procédé de laminage à chaud d'une bande d'aluminium
EP3622096B1 (fr) 2017-05-11 2021-09-22 Aleris Aluminum Duffel BVBA Procédé de fabrication d'un produit en feuille laminé en alliage al-si-mg ayant une excellente formabilité

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US10612115B2 (en) 2020-04-07
EP2270249B1 (fr) 2013-05-29
WO2011000635A1 (fr) 2011-01-06
CA2766327C (fr) 2016-02-02
KR101401060B1 (ko) 2014-05-29
RU2516214C2 (ru) 2014-05-20
ES2426226T3 (es) 2013-10-22
JP5981842B2 (ja) 2016-08-31
CA2766327A1 (fr) 2011-01-06
CN102498229B (zh) 2014-03-12
ES2746846T3 (es) 2020-03-09
KR20120057607A (ko) 2012-06-05
CN102498229A (zh) 2012-06-13
EP2449145B1 (fr) 2019-08-07
US20160068939A1 (en) 2016-03-10
EP2270249B2 (fr) 2020-05-27
US10047422B2 (en) 2018-08-14
EP2449145A1 (fr) 2012-05-09
US20120222783A1 (en) 2012-09-06
RU2012102976A (ru) 2013-08-10
JP2012531521A (ja) 2012-12-10

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