EP3918102A1 - Procédé de fabrication d'une tôle ou d'un feuillard en un alliage d'aluminium ainsi que tôle, feuillard ou pièce façonnée produit-e par ce procédé - Google Patents

Procédé de fabrication d'une tôle ou d'un feuillard en un alliage d'aluminium ainsi que tôle, feuillard ou pièce façonnée produit-e par ce procédé

Info

Publication number
EP3918102A1
EP3918102A1 EP20706105.2A EP20706105A EP3918102A1 EP 3918102 A1 EP3918102 A1 EP 3918102A1 EP 20706105 A EP20706105 A EP 20706105A EP 3918102 A1 EP3918102 A1 EP 3918102A1
Authority
EP
European Patent Office
Prior art keywords
weight
sheet
strip
rolling
particles
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.)
Pending
Application number
EP20706105.2A
Other languages
German (de)
English (en)
Inventor
Paul EBENBERGER
Werner FRAGNER
Bodo Gerold
Stefan Pogatscher
Lukas STEMPER
Peter J. Uggowitzer
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.)
Amag Rolling GmbH
Original Assignee
Amag Rolling 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.)
Filing date
Publication date
Application filed by Amag Rolling GmbH filed Critical Amag Rolling GmbH
Publication of EP3918102A1 publication Critical patent/EP3918102A1/fr
Pending legal-status Critical Current

Links

Classifications

    • 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
    • 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
    • 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

Definitions

  • the invention relates to a method for producing a sheet or strip from an aluminum alloy and a sheet, strip or molded part produced thereby.
  • Al-Mg-Mn alloys are therefore, for example, only for outer skin parts in body construction where ssf (strech strain free) quality or ffa (low-flow) quality, i.e. freedom or reduction of type A flow figures, is only required suitable to a limited extent.
  • the process should be easy to use and reproducible.
  • the invention solves the problem with respect to the method by the features of claim 1.
  • the sheet or strip is in the process of an aluminum alloy with the composition, namely from 2.0 to 5.5% by weight of magnesium (Mg), from 0.2 to 1.2% by weight of manganese (Mn) , optionally up to 0.45% by weight silicon (Si), optionally up to 0.55% by weight iron (Fe), optionally up to 0.35% by weight chromium (Cr), optionally up to 0.2% by weight % Titanium (Ti), optionally up to 0.2% by weight silver (Ag), optionally up to 4.0% by weight zinc (Zn), optionally up to 0.8% by weight copper (Cu), optionally up to 0.8% by weight of zirconium (Zr), optionally up to 0.3% by weight of niobium (Nb), optionally up to 0.25% by weight of tantalum (Ta), optionally up to 0.05% by weight % Vanadium (V) and the remainder aluminum as well as production-related unavoidable impurities, each with a maximum of 0.05% by weight and a total of
  • the method has the following method steps according to
  • the method can optionally have the following method steps:
  • the sheet or strip cold-rolled to the final thickness has at least one, in particular primary, intermetallic phase with first particles with an average particle size of 5 pm to 10 pm (measured according to the line-cutting method ASTM E1 12) - by the process steps heat treatment.
  • the at least casting and the cold rolling in particular after the intermediate annealing, are coordinated with one another in such a way that the sheet or strip has at least one intermetallic phase with first particles with an average particle size of 5 pm to 10 pm.
  • These first and therefore primary particles are relatively coarse.
  • These particles of the primary phase also have a high stability - also with respect to a subsequent recrystallization annealing or a subsequent heat treatment.
  • a sheet or strip with high strength and formability as well as ssf quality or ffa quality can be produced - and that if the sheet or strip cold-rolled to the final thickness after heat treatment also has an average crystal grain size D of ⁇ 60 pm (measured according to the line cutting method ASTM E1 12) and the average crystal grain size D in mm and the number A of the first particles per mm 2 in the aluminum alloy fulfills the condition V ⁇ * A> 1.8 - for example in that the recrystallization annealing of the heat treatment in this way is carried out.
  • This process is also easy to use and has, for example, water cooling for accelerated cooling, the highest reproducibility to produce a sheet or strip in ssf quality or ffa quality.
  • the number of dislocations in the sheet or strip can be increased further in the process if U * A> 2.
  • VU * A> 2.5 the sheet or strip can meet comparatively high quality standards without flow figures, for example Lüders lines of type A, on the surface of the formed sheet or even with comparatively complex geometries or unfavorable plastic deformations Bands have to be feared.
  • the reproducibility of the method can be further improved if, in the heat treatment, the recrystallization annealing is carried out by holding at a temperature of 300 ° C. (degrees Celsius) or more, in particular up to 600 ° C. This can be further improved if the recrystallization annealing at 450 ° C to 550 ° C follows. In addition, this annealing temperature may be sufficient to prestress the structure sufficiently by accelerated cooling in order to produce those dislocations on the first particles which subsequently do not make it necessary to dislodge Lüders lines.
  • the heated sheet is accelerated at a cooling rate of at least 10 K / s (Kelvin per second), in particular at least 20 K / s or at least 50 K / s, this accelerated cooling to in particular below 180 ° C, especially at room temperature.
  • K / s Kelvin per second
  • the billet is solidified while maintaining a cooling rate (or cooling rate) of ⁇ 2.5 ° C./s. This can be further improved if the cooling rate is ⁇ 2 ° C / s or ⁇ 1 ° C / s or ⁇ 0.75 ° C / s.
  • a possible reduction in the average particle size can be intercepted by subsequent process steps, for example by cold rolling, to ensure an average particle size of 5 pm to 10 pm before the heat treatment.
  • the optional homogenization can be done by holding at 450 ° C to 550 ° C for at least 0.5 h.
  • Hot rolling can take place at 280 ° C to 550 ° C.
  • the cold rolling to the final thickness can take place with a rolling degree of 10% to 65%, in particular from 20% to 50%.
  • the cold rolling is carried out after the intermediate annealing with a rolling degree of 10% to 65%, in particular from 20% to 50%, in order to improve the reproducibility of the average particle size from 5 pm to 10 pm.
  • the optional intermediate annealing can be done by holding at 300 ° C to 500 ° C.
  • the optional stabilization can be carried out by holding at 80 ° C to 120 ° C for at least 0.5 h.
  • An average particle size of 5 pm to 10 pm before the heat treatment can be ensured in particular if the product of the degree of rolling in% after the intermediate annealing and the cooling rate in ° C./s fulfills the condition 10 ⁇ degree of rolling * cooling rate ⁇ 50, in particular 20 ⁇ degree of rolling * Cooling rate ⁇ 45, fulfilled.
  • the intermetallic phase has an Al-Mn base, those dislocations can be created in the aluminum alloy, based on which flow figures can be avoided in a particularly stable manner.
  • the intermetallic phase is preferably of the type Ali3 (Mn, Fe) 6 or of the type AhsFeM S or of the type Ali2Mn or of the type AIbMh. These first particles of the primary phase are a particularly stable phase. It is also conceivable that the primary phase forms the intermetallic phase in order to create a sufficient number of dislocations in cooperation with the heat treatment of the sheet or strip.
  • the aluminum alloy (with an Al-Mg-Mn base) is 4.0 to 5.0% by weight magnesium (Mg) and / or from 0.2 to 0.5% by weight of manganese (Mn).
  • Mg magnesium
  • Mn manganese
  • the aluminum alloy additionally contains 2.0 to 4.0% by weight of zinc (Zn) (Al-Mg-Zn base).
  • this aluminum alloy can also contain up to 0.8% by weight of copper (Cu).
  • the invention achieves the stated object with regard to the sheet or strip by the features of claim 8.
  • the average crystal grain size D according to the invention of ⁇ 60 pm leads to the fact that the comparatively fine crystal grain of the sheet or strip enables high strength and formability.
  • the first particles present in the sheet or strip have a limited average particle size of 5 pm to 10 pm, the average crystal grain size D in mm and the number A of first particles in the aluminum alloy per mm 2 fulfills the condition U * A> 1.8.
  • a sheet or strip made of an aluminum alloy preferably with an Al-Mg base (or Mg as one of the main alloying elements) in ssf quality or ffa quality is created, which is also characterized by sufficient strength and formability, for example for outer skin parts in the bodywork.
  • the number of dislocations in the sheet or strip can be increased further if VH * A> 2.
  • ⁇ * A> 2.5 the sheet or strip can meet comparatively high quality standards without flowing elements, for example Lüders lines of type A, on the surface of the formed part, even with comparatively complex geometries or unfavorable plastic deformations Sheet or band must be feared.
  • a sufficient number of dislocations to avoid flow figures on the formed sheet or band can result if the crystal structure on each first particles has more than 200, in particular more than 400, dislocations. This can be achieved if the sheet or strip has been heat-treated by heating and then accelerated cooling such that the crystal structure has more than 200, in particular more than 400, dislocations for each first particle.
  • the number A of the first particles is preferably> 10 particles / mm 2 , which can enable a sufficient distribution of the dislocations in the sheet or strip in order to avoid flow figures. This is particularly the case if the number A of the first particles is> 25 particles / mm 2 , preferably> 35 particles / mm 2 .
  • the intermetallic phase has an Al-Mn base, those dislocations can be created in the aluminum alloy that can be used to avoid stable flow figures.
  • the intermetallic phase is preferably of the type Ali3 (Mn, Fe) 6 or of the type AhsFeM S or of the type Ali2Mn or of the type AteMn. These first parts of the primary phase are a particularly stable phase. It is also conceivable that the primary phase forms the intermetallic phase in order to create a sufficient number of dislocations through the subsequent heat treatment of the sheet or strip.
  • the aluminum alloy contains 4.0 to 5.0% by weight of magnesium (Mg) and / or 0.2 to 0.5% by weight of manganese (Mn).
  • the aluminum alloy additionally contains 2.0 to 4.0% by weight of zinc (Zn) (with an Al-Mg-Zn base).
  • This aluminum alloy can optionally have up to 0.8% by weight of copper (Cu).
  • the sheet or strip according to the invention can also be particularly suitable for the production of a molded part, in particular a vehicle part, preferably a body part, by sheet metal forming.
  • a plate is preferably produced from the sheet or strip in order to be able to carry out a sheet metal forming process.
  • the average crystal grain size and the average particle size are measured according to the line cut method ASTM E 1 12.
  • the aluminum alloy preferably has an Al-Mg base.
  • the sheet or strip can have an average crystal grain size D of ⁇ 50 gm
  • cooling rate (or cooling rate) ⁇ 2.4 ° C / s, ⁇ 2.3 ° C / s,
  • the strip can be separated into a split strip or into metal sheets or can also be cut off from the metal sheet or strip in order to reshape these semi-finished products, for example to reshape them.
  • Forming can be deep drawing, roll profiling, etc.
  • the aluminum alloy can be of the type, for example, EN AW-5083 or EN AW-5086 or EN AW-5182 or EN AW-5454 or EN AW- 5457 or EN AW-5754.
  • cold-rolled semi-finished products for example, thin sheets made of an aluminum alloy with an Al-Mg-Mn base and thin sheets made of an aluminum alloy with an Al-Mg-Zn-Mn base were produced.
  • Table 1 A wide variety of aluminum alloys and the remainder aluminum and production-related unavoidable impurities, each with a maximum of 0.05% by weight and a total of at most 0.15% by weight, were used.
  • a thin sheet A1 with a sheet thickness of 1.2 mm was made from an alloy of type AA5182 (Al-Mg-Mn base) with the chemical composition C1.
  • the manufacture of the ingot was solidified with a comparatively reduced cooling rate (or cooling rate), the rolling steps for hot and cold rolling were carried out according to the standard scheme.
  • the last rolling pass during cold rolling was 63% (from 3.25 mm to 1.2 mm) and the final heat treatment was carried out at 500 ° C. with subsequent water quenching.
  • the average crystal grain size or final grain size of the thin sheet A1 was 15 gm (measured according to the line cutting method ASTM E1 12) and in the primary intermetallic phase there were 44, an average particle size of 5 pm to 10 pm (measured according to the line cutting method ASTM E 1 12 ) having first particles per mm 2 . These primary particles were also formed comparatively roughly. In addition, with the product of the cooling rate after the intermediate annealing and the degree of rolling of 44, the condition 10 ⁇ degree of rolling * cooling rate ⁇ 50 is met.
  • VD * A> 1, 8 The criterion (VD * A> 1, 8) is met with a VD * A value of 5.4.
  • a tensile test showed no lines of Lüders on the surface of the sheet A1.
  • the intermetallic phase according to the invention with the first particles could therefore provide a sufficient number of dislocations to prevent Lüders lines from being formed.
  • a sheet A2 with a sheet thickness of 1.2 mm was made from an alloy of type AA5182 with the chemical composition C2.
  • the rolling ingot was solidified at a cooling rate (or cooling rate) of 1.8 ° C./s, and the rolling steps during hot and cold rolling were carried out according to the standard scheme.
  • the last rolling pass during cold rolling was 15% (from 1.41 mm to 1.2 mm), the final heat treatment was carried out at 500 ° C with subsequent water quenching.
  • the condition 10 ⁇ degree of rolling * cooling rate ⁇ 50 is met.
  • the average crystal grain size or final grain size of the thin sheet A1 after the heat treatment was found to be 35 pm and in the primary intermetallic phase there were 12 first particles per mm 2 having an average particle size of 5 pm to 10 pm.
  • the criterion (VD * A> 1, 8) is met with a VD * A value of 2.24.
  • a tensile test showed no lines of Lüders on the surface of the sheet A2.
  • the intermetallic phase according to the invention with the first or primary part was therefore able to provide a sufficient number of dislocations to prevent Lüder lines during the forming.
  • Example 3 Example 3:
  • a thin sheet A3 with a sheet thickness of 1.2 mm was made from an alloy of type AA5182 with the chemical composition C3.
  • the rolling bar was solidified at a cooling rate (or cooling rate) of 1.8 ° C./s, and the rolling steps during hot and cold rolling were carried out according to the standard scheme.
  • the last rolling pass during cold rolling was 18% (from 1.46 mm to 1.2 mm), the final heat treatment was carried out at 500 ° C with subsequent water quenching.
  • the average crystal grain size or final grain size was 29 pm and in the primary intermetallic phase there were 14 first particles per mm 2 with an average particle size of 5 pm to 10 pm.
  • the condition 10 ⁇ degree of rolling * cooling rate ⁇ 50 is met.
  • VD * A> 1, 8 The criterion (VD * A> 1, 8) is met with a VD * A value of 2.38.
  • a tensile test showed no lines of Lüders on the surface of the sheet A3.
  • the intermetallic phase according to the invention with the first or primary particles could therefore ensure a sufficient number of dislocations in order to prevent Lüders lines from being formed.
  • Two fine sheets A4.1 and A4.2 with a sheet thickness of 1.2 mm were produced from an alloy of type AA5182 with the chemical composition C4.
  • the rolling bar was solidified at a cooling rate (or cooling rate) of 1.8 ° C / s and the rolling steps in hot and cold rolling were carried out according to the standard scheme.
  • the last rolling pass during cold rolling was 25% (from 1.60 mm to 1.2 mm).
  • the final heat treatment was carried out on sheet A4.1 at 500 ° C with subsequent water quenching.
  • the A4.2 thin sheet was finally heat-treated at 370 ° C with subsequent cooling in still air.
  • the mean crystal grain size or final grain size of both thin sheets A4.1 and A4.2 was 32 pm and in their primary intermetallic phase there were 12, one average particle size of 5 gm to 10 gm, the first particles per mm 2 . With a VD * A value of 2, 14, the criterion (VD * A> 1, 8) is met by both thin sheets A4.1 and A4.2.
  • Lüders lines appear on thin sheet A4.2 after deep drawing.
  • slower cooling in still air did not allow a sufficient number of dislocations to form on the sheet A4.2 to prevent lines of wear and tear. That accelerated water cooling of the sheet A4.1 therefore meant that the intermetallic phase with the first or primary particles could provide a sufficient number of dislocations to prevent Lüders lines from being formed.
  • a sheet A5 with a sheet thickness of 1.2 mm was produced from an alloy of type AA5182 with the chemical composition C4.
  • the rolling ingot was solidified at a cooling rate (or cooling rate) of 1.8 ° C./s, and the rolling steps during hot and cold rolling were carried out according to the standard scheme.
  • the last rolling pass during cold rolling was 63% (from 3.25 mm to 1.2 mm), the final heat treatment was carried out at 500 ° C with subsequent water quenching.
  • the average crystal grain size or final grain size was 10 pm and in the primary intermetallic phase there were 12 first particles per mm 2 , which had an average particle size of 5 pm to 10 pm.
  • a sheet A6.1 with a sheet thickness of 1.2 mm was made from an alloy with an Al-Mg-Zn-Mn base of chemical composition D1.
  • the ingot was solidified at a cooling rate (or cooling rate) of 1.8 ° C / s and the rolling steps during hot and cold rolling were carried out according to the standard scheme.
  • the last rolling pass during cold rolling was 18% (from 1.46 mm to 1.2 mm).
  • the final heat treatment was carried out at 500 ° C with subsequent water quenching. After the accelerated cooling, stabilization was carried out at 100 ° C for 3 h (hours).
  • the average crystal grain size or final grain size was 28 gm and in the primary intermetallic phase there were 14 first particles per mm 2 , which had an average particle size of 5 pm to 10 pm.
  • VD * A value of 2.34 the criterion (VD * A> 1, 8) is met.
  • VD * A the criterion (VD * A> 1, 8) is met.
  • the condition 10 ⁇ degree of rolling * cooling rate ⁇ 50 is met.
  • a tensile test showed no lines of Lüders on the surface of the sheet A6.1.
  • the intermetallic phase according to the invention with the first or primary particles could therefore ensure a sufficient number of dislocations in order to prevent Lüders lines from being formed.
  • Embodiment 6.2
  • a sheet A6.2 with a sheet thickness of 1.2 mm was made from an alloy with an Al-Mg-Zn-Mn base of chemical composition D1.
  • the ingot was solidified at a cooling rate (or cooling rate) of 1.8 ° C / s and the rolling steps during hot and cold rolling were carried out according to the standard scheme.
  • the last rolling pass during cold rolling was 63% (from 3.25 mm to 1.2 mm), the final heat treatment was carried out at 500 ° C. with subsequent water quenching.
  • the average crystal grain size or final grain size was 10 pm and in the primary intermetallic phase there were 14 first particles per mm 2 having an average particle size of 5 pm to 10 pm.
  • VD * A value of 1.4 the criterion for freedom from liability (VD * A> 1.8) is not Fulfills.
  • VD * A the condition 10 ⁇ degree of rolling * cooling rate ⁇ 50 is not met.
  • lines of Lüders were found. The intermetallic phase with the first or primary particles could therefore not ensure a sufficiently high number of dislocations to prevent Lüders lines from being formed.
  • All of the exemplary embodiments according to the invention namely A1, A2, A3, A4.1 and A6.1, have in common that their crystal structure has more than 200, in particular more than 400, dislocations on each first particle.

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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)
  • Continuous Casting (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention concerne un procédé de fabrication d'une tôle ou d'un feuillard en alliage d'aluminium ainsi qu'une tôle, un feuillard ou une pièce façonnée produit-e par ce procédé. Une surface rugueuse et des vermiculures peuvent être évitées si la tôle ou le feuillard laminé-e à froid ayant une composition et une microstructure spéciales est soumis-e à un traitement thermique avec recuit de recristallisation suivi d'un refroidissement accéléré.
EP20706105.2A 2019-01-30 2020-01-30 Procédé de fabrication d'une tôle ou d'un feuillard en un alliage d'aluminium ainsi que tôle, feuillard ou pièce façonnée produit-e par ce procédé Pending EP3918102A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP19154632.4A EP3690076A1 (fr) 2019-01-30 2019-01-30 Procédé de fabrication d'une tôle ou d'une bande d'un alliage d'aluminium ainsi que tôle, bande ou pièce moulée fabriqués selon ledit procédé
PCT/EP2020/052375 WO2020157246A1 (fr) 2019-01-30 2020-01-30 Procédé de fabrication d'une tôle ou d'un feuillard en un alliage d'aluminium ainsi que tôle, feuillard ou pièce façonnée produit-e par ce procédé

Publications (1)

Publication Number Publication Date
EP3918102A1 true EP3918102A1 (fr) 2021-12-08

Family

ID=65268872

Family Applications (2)

Application Number Title Priority Date Filing Date
EP19154632.4A Withdrawn EP3690076A1 (fr) 2019-01-30 2019-01-30 Procédé de fabrication d'une tôle ou d'une bande d'un alliage d'aluminium ainsi que tôle, bande ou pièce moulée fabriqués selon ledit procédé
EP20706105.2A Pending EP3918102A1 (fr) 2019-01-30 2020-01-30 Procédé de fabrication d'une tôle ou d'un feuillard en un alliage d'aluminium ainsi que tôle, feuillard ou pièce façonnée produit-e par ce procédé

Family Applications Before (1)

Application Number Title Priority Date Filing Date
EP19154632.4A Withdrawn EP3690076A1 (fr) 2019-01-30 2019-01-30 Procédé de fabrication d'une tôle ou d'une bande d'un alliage d'aluminium ainsi que tôle, bande ou pièce moulée fabriqués selon ledit procédé

Country Status (7)

Country Link
US (1) US20220127708A1 (fr)
EP (2) EP3690076A1 (fr)
JP (1) JP2022519238A (fr)
CN (1) CN113474479B (fr)
CA (1) CA3128294A1 (fr)
MX (1) MX2021009093A (fr)
WO (1) WO2020157246A1 (fr)

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3848476A1 (fr) * 2020-01-07 2021-07-14 AMAG rolling GmbH Tôle ou bande en alliage d'aluminium durcissable, pièce de véhicule fabriquée à partir de celle-ci, utilisation et procédé de fabrication de tôle ou de bande
WO2024129624A1 (fr) * 2022-12-12 2024-06-20 Arconic Technologies, Llc Nouveaux alliages d'aluminium 5xxx et leurs procédés de fabrication

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CH638243A5 (de) * 1978-07-05 1983-09-15 Alusuisse Verfahren zur herstellung von magnesium- und zinkhaltigen aluminium-legierungs-blechen.
JPH0668146B2 (ja) * 1986-09-09 1994-08-31 スカイアルミニウム株式会社 アルミニウム合金圧延板の製造方法
NL9100565A (nl) 1991-04-02 1992-11-02 Hoogovens Aluminium Nv Aluminium plaat en werkwijze voor het vervaardigen daarvan.
DE10231422A1 (de) 2001-08-13 2003-02-27 Corus Aluminium Nv Aluminium-Magnesium-Legierungserzeugnis
JP4109600B2 (ja) * 2003-10-10 2008-07-02 株式会社神戸製鋼所 アルミニウム合金板およびその製造方法
SE530437C2 (sv) * 2006-10-13 2008-06-03 Sapa Heat Transfer Ab Rankmaterial med hög hållfasthet och högt saggingmotstånd
KR101911037B1 (ko) * 2015-06-25 2018-10-23 하이드로 알루미늄 롤드 프로덕츠 게엠베하 고강도이며 용이하게 성형 가능한 almg-스트립 및 그 제조 방법
CN106834825B (zh) * 2016-11-16 2018-08-31 广西南南铝加工有限公司 5182铝合金

Also Published As

Publication number Publication date
CN113474479A (zh) 2021-10-01
JP2022519238A (ja) 2022-03-22
EP3690076A1 (fr) 2020-08-05
CN113474479B (zh) 2023-06-06
US20220127708A1 (en) 2022-04-28
CA3128294A1 (fr) 2020-08-06
MX2021009093A (es) 2021-10-22
WO2020157246A1 (fr) 2020-08-06

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