EP2924135A1 - Alliage d'aluminium à fermeté moyenne hautement déformable pour la fabrication de produits semi-finis ou de composants de véhicules automobiles - Google Patents

Alliage d'aluminium à fermeté moyenne hautement déformable pour la fabrication de produits semi-finis ou de composants de véhicules automobiles Download PDF

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Publication number
EP2924135A1
EP2924135A1 EP14162348.8A EP14162348A EP2924135A1 EP 2924135 A1 EP2924135 A1 EP 2924135A1 EP 14162348 A EP14162348 A EP 14162348A EP 2924135 A1 EP2924135 A1 EP 2924135A1
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EP
European Patent Office
Prior art keywords
aluminum alloy
components
rolling
strip
finished products
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
EP14162348.8A
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German (de)
English (en)
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EP2924135B1 (fr
Inventor
Dr. Thomas Hentschel
Dr. Simon Jupp
Henk-Jan Brinkmann
Dr. Olaf Engler
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.)
Speira GmbH
Original Assignee
Hydro Aluminium Rolled Products GmbH
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.)
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Publication date
Priority to EP14162348.8A priority Critical patent/EP2924135B1/fr
Application filed by Hydro Aluminium Rolled Products GmbH filed Critical Hydro Aluminium Rolled Products GmbH
Priority to EP17151174.4A priority patent/EP3178952B9/fr
Priority to ES14162348.8T priority patent/ES2655434T3/es
Priority to PT141623488T priority patent/PT2924135T/pt
Priority to RU2016142403A priority patent/RU2655510C2/ru
Priority to JP2016559550A priority patent/JP6279761B2/ja
Priority to KR1020177030782A priority patent/KR20170121336A/ko
Priority to KR1020167030120A priority patent/KR101808812B1/ko
Priority to PCT/EP2015/056733 priority patent/WO2015144888A2/fr
Priority to CA2944061A priority patent/CA2944061C/fr
Priority to CN201580017129.6A priority patent/CN106164311A/zh
Publication of EP2924135A1 publication Critical patent/EP2924135A1/fr
Priority to US15/270,601 priority patent/US10047424B2/en
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Publication of EP2924135B1 publication Critical patent/EP2924135B1/fr
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent

Definitions

  • the invention relates to an aluminum alloy for producing semi-finished products or components of motor vehicles, a method for producing a strip from an aluminum alloy according to the invention, a corresponding aluminum alloy strip or sheet and a structural part of a motor vehicle consisting of an aluminum alloy sheet.
  • Semi-finished products and components for motor vehicles must meet different requirements depending on their place of use and purpose in the motor vehicle.
  • the forming properties of the aluminum alloy or of the strips and metal sheets produced therefrom are decisive.
  • the strength values but also, in particular, the corrosion properties play a significant role.
  • the mechanical properties are primarily determined by the rigidity, which depends above all on the shape of the inner door parts.
  • the tensile strength has a rather minor influence.
  • the materials used for a door inner part must not be too soft either.
  • good formability is particularly important for the introduction of aluminum alloy materials into the motor vehicle sector, since the components and semi-finished products undergo particularly complex forming processes during their production. This particularly relates to components that are manufactured in a one-piece sheet metal shell construction, such.
  • the aim is, for example, to be able to produce semi-finished products or components in one piece from an aluminum alloy and to use as few forming operations as possible. This requires maximizing the forming behavior of the aluminum alloy to be used.
  • the AA5005 aluminum alloy (AlMg1) which is sometimes used for similar applications, does not meet these requirements since it does not have sufficient forming capacity due to solidification during forming.
  • the aluminum alloy to be used should therefore be as resistant to corrosion as possible, in particular in the painted state against intercrystalline corrosion and against filiform corrosion.
  • Filiform corrosion is understood to mean a type of corrosion which occurs in coated components and exhibits a thread-like course. Filiform corrosion occurs at high humidity in the presence of chloride ions.
  • the aluminum alloy AA8006 AlFe1.5Mn 0.5
  • the alloy AA8006 is thus less suitable for coated, in particular painted components such as door inner parts.
  • an aluminum alloy is known as an alternative to the aluminum alloy of the type AA8006, which has the following alloy constituents in% by weight: Fe ⁇ 0 . 8th % . Si ⁇ 0 . 5 % . 0 . 9 % ⁇ Mn ⁇ 1 . 5 % . mg ⁇ 0 . 25 % . Cu ⁇ 0 . 20 % . Cr ⁇ 0 . 05 % . Ti ⁇ 0 . 05 % . V ⁇ 0 . 05 % . Zr ⁇ 0 . 05 % .
  • the present invention is therefore based on the object to provide an aluminum alloy for the production of semi-finished products or components for motor vehicles, which is highly deformable, medium-strength and very resistant to corrosion.
  • a method for producing a strip of a corresponding aluminum alloy, an aluminum strip or sheet, its use and a structural part of a motor vehicle to be proposed.
  • an aluminum alloy for the production of semi-finished products or components of motor vehicles which has the following alloy components in% by weight: 0 . 6 % ⁇ Si ⁇ 0 . 9 % . 0 . 6 % ⁇ Fe ⁇ 1 . 0 % . Cu ⁇ 0 . 1 % . 0 . 6 % ⁇ Mn ⁇ 0 . 9 % . 0 . 5 % ⁇ mg ⁇ 0 . 8th % . Cr ⁇ 0 . 05 % .
  • the present aluminum alloy is based on the recognition that Al-Mg-Si alloys of the alloy type AA6XXX in the as-annealed state have a very good formability. However, they were too soft for the previous applications.
  • the lower limits of the forcibly provided alloying elements of 0.6 wt% for Si, 0.6 wt% for Fe, 0.6 wt% for Mn and 0.5 wt% for Mg ensure that the Aluminum alloy in soft annealed condition can provide sufficient strength.
  • the upper limits of 0.9% by weight for Si, 1.0% by weight for Fe, 0.9% by weight for Mn and 0.8% by weight for Mg prevent the elongation at break from dropping and thus the forming behavior is deteriorated.
  • the alloying elements Cu are limited to a maximum of 0.1% by weight and Cr to a maximum of 0.05% by weight.
  • the combination of the intended alloy components of Si, Fe, Mg and Mn ensures that, on the one hand, the very good forming behavior of the Al-Mg-Si alloys is combined with increased strength, without having too great losses in ductility.
  • the investigations showed that the specified aluminum alloy in annealed condition meets the requirements for formability and in particular for corrosion resistance and is thus suitable for the production of semi-finished products or components in motor vehicles.
  • the aluminum alloy according to the invention falls into the class of the Al-Mg-Si alloys of the alloy type AA6XXX. This allows for improved recyclability of this aluminum alloy when used in the scrap cycle with the in Automotive applications commonly used Al-Mg-Si alloys of alloy type AA6XXX be mixed.
  • the alloy constituents Si, Fe, Mn and Mg have the following proportions in% by weight: 0 . 7 % ⁇ Si ⁇ 0 . 9 % . 0 . 7 % ⁇ Fe ⁇ 1 . 0 % . 0 . 7 % ⁇ Mn ⁇ 0 . 9 % and 0 . 6 % ⁇ mg ⁇ 0 . 8th % ,
  • a further improvement of the aluminum alloy according to the invention with respect to a maximum elongation at break is achieved in that the alloy constituents Si, Fe, Mn and Mg have the following proportions in% by weight: 0 . 7 % ⁇ Si ⁇ 0 . 8th % . 0 . 7 % ⁇ Fe ⁇ 0 . 8th % . 0 . 7 % ⁇ Mn ⁇ 0 . 8th % and 0 . 6 % ⁇ mg ⁇ 0 . 7 % ,
  • the resistance to intergranular corrosion can be further improved in that the Si content of the alloy exceeds the Mg content by a maximum of 0.2% by weight, preferably a maximum of zero , 1 wt .-% exceeds.
  • the elongation at break of the aluminum alloy can be further improved by further reducing the Cr content to a maximum value of 0.01% by weight, preferably to a maximum of 0.001% by weight. It has been shown that chromium has a negative effect on the elongation at break even in very low concentrations.
  • a similar effect also has the reduction of the Cu contents to a maximum of 0.05 wt .-%, preferably at most 0.01 wt .-%, at the same time the tendency to filiform corrosion or intergranular corrosion by reducing the Cu contents generally returns.
  • the hot rolling temperatures allow good recrystallization during hot rolling, so that the structure is as fine as possible after hot rolling.
  • this fine-grained structure is merely stretched and recrystallized again in the final soft annealing.
  • the cold rolling produces a particularly high number of dislocations in the microstructure, which produces a very fine-grained, thoroughly recrystallised microstructure in the final soft annealing.
  • the Abwalzgrad to final thickness before the final annealing must have at least 50%, preferably at least 70% to the desired final thickness.
  • a further positive influence on the fine grain of the structure can be achieved that according to a further embodiment of the method according to the invention, the homogenization is carried out in two stages, the ingot is first heated to 550 ° C to 600 ° C for at least 0.5 h and then the Rolling bar at 450 ° C to 550 ° for at least 0.5 h, preferably at least 2 h is maintained. Subsequently, the rolling ingot is hot rolled.
  • the corrosion properties can be improved by milling the billet after casting or after homogenization on the top and bottom, in order to exclude impurities from the top and bottom of the rolling billet, which can adversely affect the corrosion resistance.
  • the method according to the invention at least one intermediate annealing after a first cold rolling in a Temperature of 300 ° C to 400 ° C, preferably at a temperature of 330 ° C to 370 ° C for at least 0.5 h, wherein before and after the intermediate annealing the Abwalzgrad is at least 50%, preferably at least 70%. Due to the selected degrees of finish before the intermediate annealing or after the intermediate annealing, it is achieved that the microstructure is thoroughly recrystallized during the intermediate annealing.
  • the intermediate annealing time is at least 0.5 h, preferably at least 2 h.
  • the above object is achieved by an aluminum alloy strip or sheet made of an aluminum alloy according to the invention, wherein the strip has a thickness of 0.2 mm to 5 mm and in the annealed state, a yield strength R p0.2 of at least 45 MPa and an equi- elongation Ag of at least 23% and an elongation at break A 80mm of not less than 35%.
  • the conditions are given that the aluminum alloy strip or sheet can be used for components in the motor vehicle, which in addition to very good forming properties and a very good Have resistance to intergranular corrosion or filiform corrosion. This is especially true for painted or coated components.
  • the use of the aluminum alloy strip according to the invention for the production of semi-finished products or components of a motor vehicle, in particular structural parts of a motor vehicle solves the above-mentioned Task.
  • structural parts can be produced with very large degrees of deformation and assume very complex shapes without requiring particularly complicated forming operations.
  • these are also particularly resistant to corrosion in lacquered form, in particular against intergranular corrosion and filiform corrosion.
  • the object indicated is achieved by a structural part of a motor vehicle, in particular a door inner part of a motor vehicle having at least one deformed sheet of an aluminum alloy according to the invention.
  • the aluminum alloy according to the invention not only provides the required forming properties in the as-annealed state, but at the same time also ensures the necessary corrosion resistance and strength of the structural parts.
  • the structural part according to the invention is produced from a strip which has been produced by the method according to the invention. It has been shown that with the method according to the invention, the forming properties as well as the strength properties of the structural part can be achieved in a process-reliable manner, so that an economic production of the structural parts which meet the conditions mentioned, is possible.
  • a first embodiment in a schematic flow diagram now shows Fig. 1 ,
  • the rolling ingot is cast, for example in the DC continuous casting process or in the strip casting process.
  • the bar is then heated to a temperature of 500 ° C to 600 ° C and held for at least 0.5 h, preferably at least 2 h at this temperature for homogenization.
  • the so homogenized ingot is then hot rolled at a temperature of 280 ° C to 500 ° C, preferably 300 ° C to 400 ° C to a final thickness of 3 to 12 mm.
  • step 8 a cold rolling to final thickness, followed by a recrystallizing final soft annealing according to step 10 followed.
  • the degree of rolling must be at least 50%, preferably at least 70%, in order to produce a sufficiently fine-grained microstructure in the final soft annealing.
  • the final soft annealing at which the strip recrystallizes again, takes place in the chamber furnace at 300 ° C. to 400 ° C., preferably at 330 ° C. to 370 ° C. in step 10.
  • the alloy components according to the invention of Mg, Si, Fe and Mn, the use is a continuous furnace for the production of the aluminum alloy strip according to the invention is not possible because other structures would be provided due to the different heating and cooling rates.
  • milling may also be performed according to step 12 of the top and bottom of the rolling billet to minimize the impact of contaminants at the edges of the billets in the ingot fabrication on the finished product. In particular, this has a positive influence on the corrosion resistance of the components.
  • Fig. 2 now shows another flowchart which shows the step 16 of the homogenization as an alternative to step 4.
  • the homogenization has an influence on the fine grain of the desired end structure of the strip or finished component.
  • the homogenization is carried out in several stages. So instead of step 4 in Fig. 1 in Fig. 2 a Homogenticians Republic 16 performed.
  • the homogenization step 16 initially has a first homogenization phase, step 18, in which the milled or unmilled roll ingot is heated to a temperature of 550 ° C. to 600 ° C. for at least 0.5 h, preferably at least 2 h.
  • step 20 the so heated ingot is cooled to a temperature of 450 ° C to 550 ° C and held at this temperature for at least 0.5 h, preferably at least 2 h, which in Fig. 2 is shown in step 22.
  • the ingot may also be cooled to room temperature in a step 24 and heated in a subsequent step 26 to the temperature for the second homogenization. This is necessary, for example, if the rolling ingot has to be stored between the homogenization step.
  • this phase can be used at room temperature to mill the ingot at the top and bottom, step 28.
  • the hot rolling is carried out as in Fig. 1 represented with the parameters specified there. It has been shown that the multi-stage homogenization, in particular the two-stage homogenization leads to a finer structure in the final product.
  • Variants 1 to 4 and 9 and 10 are comparative examples which do not correspond to the aluminum alloy according to the invention.
  • embodiments 5 to 8 correspond to the aluminum alloy compositions claimed according to the invention.
  • both the yield strength R p0.2 , the tensile strength R m , the uniform elongation Ag, the elongation at break A were measured 80 mm, and the draft SZ 32 obtained in the ironing was measured in millimeters.
  • the values for the yield strength R p0.2 and the tensile strength R m were measured in the tensile test perpendicular to the rolling direction of the sheet according to DIN EN ISO 6892-1: 2009.
  • the uniform elongation Ag and the elongation at break A were measured 80 mm in each case perpendicular to the rolling direction of the sheet with a flat tensile specimen according to DIN EN ISO 6892-1: 2009, Annex B, Form 2.
  • the forming behavior can also be used in a Stretch drawing test SZ 32 can be measured by a cupping test according to Erikson (DIN EN ISO 20482), in which a test piece is pressed against the sheet, so that a cold deformation occurs. During cold working, the force as well as the punch travel of the test specimen are measured until there is a load drop, which causes the formation of a crack.
  • the cupping test was carried out with a punch head diameter of 32 mm and die diameter of 35.4 mm coordinated with the sheet metal blanket with the aid of a Teflon drawing film to reduce friction. The overview of the results is shown in Table 2.
  • V comparative R p0,2 R m A g A 80mm SZ32 (E): Invention N / mm 2 N / mm 2 % % mm 1 V 65 145 19.6 26.5 15.8 2 V 52 131 21.9 30.3 16.2 3 V 60 135 22.7 30.3 16.4 4 V 51 122 22.3 33.5 15.6 5 e 48 112 23.1 35.3 16.0 6 e 47 118 23.5 35.0 16.5 7 e 50 120 23.4 36.2 16.1 8th e 47 112 23.8 36.6 15.0 9 V 41 98 23.6 37.9 16.5 10 V 41 102 24.2 38.0 16.3
  • the exemplary embodiments show that excessive reduction of the contents Si, Fe, Mn, Mg with an increase in the contents of Cu and Cr results in the yield limit values above 45 MPa remains, but the elongation at break drops significantly to about 30%. This effect can also be demonstrated if the Mn content alone is 1.0%, for example, which already pushes the breaking elongation A 80 mm below 35%, variant 4.
  • the variants 9 and 10 show the effect of reduced contents of Si, Fe, Mn and Mg. Comparative Examples 9 and 10 show a very good elongation at break A 80mm with more than 35%, however, the yield strength with 41 MPa is below that of the inventive embodiments 5 to 8.
  • the embodiments according to the invention showed a very good forming behavior, especially in the case of strong deformations, which can be deduced from the very good stretch drawing results SZ 32 and the high elongation values both in the uniform expansion Ag and in the elongation at break A 80 mm . From this it can be seen that overall the interaction of the alloy contents Si, Fe, Mn, Mg is important, whereby the components Cr and Cu have to be kept particularly low, preferably the Cu content is ⁇ 0.05% by weight, preferably ⁇ 0.01 wt .-% and the chromium content ⁇ 0.01 wt .-%, preferably ⁇ 0.001 wt .-%.
  • Coupled with the very good corrosion resistance of the embodiments can be provided for vehicles semi-finished products and components, in particular structural components such as door inner parts, which not only ensures the specifications of the field of application in terms of mechanical and chemical properties, but can be economically produced by a few forming operations.
  • the aluminum alloy strips according to the invention are therefore ideally suited, for example, structural parts of a motor vehicle, such as in Fig. 3 to provide shown door inner parts 30 and to be used for their preparation.
  • the door inner part is made of a sheet metal of an aluminum alloy according to the invention with a thickness of 1.5 mm, which provides only by forming operations, but without joining operations a window frame.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)
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  • Heat Treatment Of Sheet Steel (AREA)
EP14162348.8A 2014-03-28 2014-03-28 Procédé pour la fabrication d'une bande d'un alliage d'aluminium à fermeté moyenne hautement déformable pour la fabrication de produits semi-finis ou de composants de véhicules automobiles Active EP2924135B1 (fr)

Priority Applications (12)

Application Number Priority Date Filing Date Title
EP17151174.4A EP3178952B9 (fr) 2014-03-28 2014-03-28 Alliage d'aluminium à haute ductilité, semi-rigide destiné à la fabrication de demi-produits ou de pièces pour véhicules automobiles
ES14162348.8T ES2655434T3 (es) 2014-03-28 2014-03-28 Procedimiento para la fabricación de una cinta de una aleación de aluminio altamente conformable y de resistencia media para productos semiacabados o componentes de automóviles
PT141623488T PT2924135T (pt) 2014-03-28 2014-03-28 Processo para a produção de uma banda de uma liga de alumínio de média tenacidade e de grande deformabilidade para produtos semiacabados ou para componentes de veículos automóveis
EP14162348.8A EP2924135B1 (fr) 2014-03-28 2014-03-28 Procédé pour la fabrication d'une bande d'un alliage d'aluminium à fermeté moyenne hautement déformable pour la fabrication de produits semi-finis ou de composants de véhicules automobiles
JP2016559550A JP6279761B2 (ja) 2014-03-28 2015-03-27 自動車の半製品又は部品の製造のための高成形性中強度アルミニウム合金ストリップ又はシート
KR1020177030782A KR20170121336A (ko) 2014-03-28 2015-03-27 차량용 반제품 또는 부품을 제조하기 위한 고성형성의 중강도 알루미늄 합금
RU2016142403A RU2655510C2 (ru) 2014-03-28 2015-03-27 Легко формируемый, среднепрочный алюминиевый сплав для изготовления заготовок или деталей автомобилей
KR1020167030120A KR101808812B1 (ko) 2014-03-28 2015-03-27 차량용 반제품 또는 부품을 제조하기 위한 고성형성의 중강도 알루미늄 합금
PCT/EP2015/056733 WO2015144888A2 (fr) 2014-03-28 2015-03-27 Alliage d'aluminium de résistance mécanique intermédiaire, hautement façonnable pour fabriquer des demi-produits ou des pièces de véhicules automobiles
CA2944061A CA2944061C (fr) 2014-03-28 2015-03-27 Alliage d'aluminium de resistance mecanique intermediaire, hautement faconnable pour fabriquer des demi-produits ou des pieces de vehicules automobiles
CN201580017129.6A CN106164311A (zh) 2014-03-28 2015-03-27 制造汽车的半成品或构件的高成型性、中强度的铝合金
US15/270,601 US10047424B2 (en) 2014-03-28 2016-09-20 Highly formable, medium-strength aluminium alloy for the manufacture of semi-finished products or components of motor vehicles

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP14162348.8A EP2924135B1 (fr) 2014-03-28 2014-03-28 Procédé pour la fabrication d'une bande d'un alliage d'aluminium à fermeté moyenne hautement déformable pour la fabrication de produits semi-finis ou de composants de véhicules automobiles

Related Child Applications (2)

Application Number Title Priority Date Filing Date
EP17151174.4A Division EP3178952B9 (fr) 2014-03-28 2014-03-28 Alliage d'aluminium à haute ductilité, semi-rigide destiné à la fabrication de demi-produits ou de pièces pour véhicules automobiles
EP17151174.4A Division-Into EP3178952B9 (fr) 2014-03-28 2014-03-28 Alliage d'aluminium à haute ductilité, semi-rigide destiné à la fabrication de demi-produits ou de pièces pour véhicules automobiles

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EP2924135A1 true EP2924135A1 (fr) 2015-09-30
EP2924135B1 EP2924135B1 (fr) 2017-12-13

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EP14162348.8A Active EP2924135B1 (fr) 2014-03-28 2014-03-28 Procédé pour la fabrication d'une bande d'un alliage d'aluminium à fermeté moyenne hautement déformable pour la fabrication de produits semi-finis ou de composants de véhicules automobiles
EP17151174.4A Active EP3178952B9 (fr) 2014-03-28 2014-03-28 Alliage d'aluminium à haute ductilité, semi-rigide destiné à la fabrication de demi-produits ou de pièces pour véhicules automobiles

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EP17151174.4A Active EP3178952B9 (fr) 2014-03-28 2014-03-28 Alliage d'aluminium à haute ductilité, semi-rigide destiné à la fabrication de demi-produits ou de pièces pour véhicules automobiles

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US (1) US10047424B2 (fr)
EP (2) EP2924135B1 (fr)
JP (1) JP6279761B2 (fr)
KR (2) KR20170121336A (fr)
CN (1) CN106164311A (fr)
CA (1) CA2944061C (fr)
ES (1) ES2655434T3 (fr)
PT (1) PT2924135T (fr)
RU (1) RU2655510C2 (fr)
WO (1) WO2015144888A2 (fr)

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Publication number Priority date Publication date Assignee Title
CN116145057B (zh) * 2023-03-20 2025-02-11 山东南山铝业股份有限公司 一种6系铝合金板材均匀化工艺方法及该工艺方法在铝合金板材生产中的应用

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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KR20170121336A (ko) 2017-11-01
PT2924135T (pt) 2018-02-09
JP2017514014A (ja) 2017-06-01
EP3178952B9 (fr) 2021-07-14
WO2015144888A2 (fr) 2015-10-01
CA2944061C (fr) 2019-10-22
RU2655510C2 (ru) 2018-05-28
EP3178952B1 (fr) 2020-07-29
US10047424B2 (en) 2018-08-14
KR101808812B1 (ko) 2017-12-13
ES2655434T3 (es) 2018-02-20
CA2944061A1 (fr) 2015-10-01
US20170009323A1 (en) 2017-01-12
KR20160132119A (ko) 2016-11-16
WO2015144888A3 (fr) 2016-01-07
EP2924135B1 (fr) 2017-12-13
JP6279761B2 (ja) 2018-02-14
RU2016142403A (ru) 2018-04-28
EP3178952A1 (fr) 2017-06-14

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