EP3848476A1 - Blech oder band aus einer aushärtbaren aluminiumlegierung, ein daraus gefertigtes fahrzeugteil, eine verwendung und ein verfahren zur herstellung des blechs oder bands - Google Patents

Blech oder band aus einer aushärtbaren aluminiumlegierung, ein daraus gefertigtes fahrzeugteil, eine verwendung und ein verfahren zur herstellung des blechs oder bands Download PDF

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Publication number
EP3848476A1
EP3848476A1 EP20190782.1A EP20190782A EP3848476A1 EP 3848476 A1 EP3848476 A1 EP 3848476A1 EP 20190782 A EP20190782 A EP 20190782A EP 3848476 A1 EP3848476 A1 EP 3848476A1
Authority
EP
European Patent Office
Prior art keywords
strip
sheet
weight
aluminum alloy
gpi
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
EP20190782.1A
Other languages
German (de)
English (en)
French (fr)
Inventor
Stefan Pogatscher
Lukas STEMPER
Ramona Tosone
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
Priority to CA3166639A priority Critical patent/CA3166639A1/en
Priority to IL294402A priority patent/IL294402A/en
Priority to CN202180008190.XA priority patent/CN115151667A/zh
Priority to AU2021206534A priority patent/AU2021206534A1/en
Priority to PCT/EP2021/050203 priority patent/WO2021140163A1/de
Priority to JP2022537081A priority patent/JP2023509367A/ja
Priority to US17/791,147 priority patent/US20230042050A1/en
Priority to BR112022013432A priority patent/BR112022013432A2/pt
Priority to MX2022008360A priority patent/MX2022008360A/es
Publication of EP3848476A1 publication Critical patent/EP3848476A1/de
Pending legal-status Critical Current

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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
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22F1/047—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 a sheet metal or strip made of a hardenable aluminum alloy, a vehicle part made therefrom, its use and a method for producing the sheet metal or strip.
  • the invention has therefore set itself the task of making available an Al-Mg-aluminum alloy which has a high temperature-hardening reaction, in particular a lacquer stoving reaction (PBR).
  • PBR lacquer stoving reaction
  • this Al-Mg-aluminum alloy should be able to achieve comparatively high strengths.
  • the invention solves the problem set according to the features of claim 1.
  • Mg magnesium
  • Zn zinc
  • a degree of sheet metal deformation of 2% with a paint baking reaction at 185 ° C for 20 minutes an R p0.2 gain in strength of well over 150 MPa could be achieved - which is unknown even from PBR-optimized 6xxx alloys.
  • this Al-Mg-Zn alloy reacts in the T4-FH condition, namely the solution-annealed, accelerated cooled (preferably quenched), stabilization annealed and cold-age-aged Al-Mg-Zn alloy, particularly rapidly hardening to a paint baking process - for example through a preferred formation of stable precursors of the T phase (Mg 32 (Al, Zn) 49 or Mg 3 Zn 3 Al 2 ) during the stabilization annealing treatment, which develop in the course of the paint-bake cycle into precipitations with a strong hardening effect and thus cause a particularly strong paint bake response (PBR).
  • T phase Mg 32 (Al, Zn) 49 or Mg 3 Zn 3 Al 2
  • the formation of the same phases or clusters in the size range from 1 to 10 nm suppresses the precipitation of S-phase and ⁇ -phase due to the comparatively high Zn content.
  • these phases or clusters produced enable a significant increase in strength in the course of a post-curing reaction, for example a paint baking reaction at 185 ° C. for 20 minutes.
  • this aluminum alloy according to the invention in the T4-FH state is energy-efficient in utilizing the available thermal energies in subsequent production steps due to the comparatively high artificial hardening reaction.
  • the sheet or strip can have one or more elements: from 0 to 0.8% by weight of copper (Cu) and / or from 0 to 0.2% by weight of silver (Ag) and / or from 0 to 1 , 0 wt .-% manganese (Mn) and / or from 0 to 0.45 wt .-% silicon (Si) and / or from 0 to 0.55 wt .-% iron (Fe) and / or from 0 to 0.35% by weight chromium (Cr) and / or from 0 to 0.2% by weight titanium (Ti) and / or from 0 to 0.8% by weight zirconium (Zr) and / or from 0 to 1.0% by weight of hafnium (Hf) and / or from 0 to 0.3% by weight of niobium (Cu) and / or from 0 to 0.2% by weight of silver (Ag) and / or from 0 to 1 , 0 wt .-% manganese
  • a vehicle is to be understood as meaning a land, water and / or air vehicle, for example.
  • a heat treatment for example a thermal shock
  • T4 treatment solution annealed with cold aging or cold aging
  • a high PBR can be made possible if the aluminum alloy contains from 3.0 to 4.0% by weight of Zn, in particular from 3.3 to 3.7% by weight of Zn - in particular because, in combination with magnesium, a comparatively very favorable curing potential can be set.
  • the alloy in the T4-FH condition has a comparatively high yield strength compared to a Zn-free alloy, which is significantly increased after subsequent reshaping and enamel baking.
  • the above can be further improved when the aluminum alloy contains from 4.5 to 5.0% by weight of Mg.
  • Mg contains from 4.5 to 5.0% by weight of Mg.
  • PBR hardening potential
  • the aluminum alloy has 0.3 to 0.6% by weight, in particular 0.4 to 0.6% by weight, for example 0.5 to 0.6% by weight, Cu.
  • the aluminum alloy can preferably contain from 0.1 to 0.3% by weight of silver (Ag).
  • Ag silver
  • This proposed Ag content leads - similar to Cu - to an additional higher precipitation density in the course of the stabilization annealing treatment - and enables a further increase in the PBR.
  • the aluminum alloy can preferably contain from 0.05 to 0.25% by weight of iron (Fe) in order to permit an increased proportion of secondary aluminum in the alloy.
  • the aluminum alloy can preferably contain from 0.3 to 1.0% by weight of manganese (Mn).
  • the aluminum alloy preferably has from 0.3 to 0.5% by weight of manganese (Mn).
  • Mn manganese
  • the aluminum alloy can preferably contain from 0.05 to 0.15% by weight of titanium (Ti) in order, for example, to adjust the grain size in a controlled manner.
  • a sheet metal or strip according to the invention with a thickness of 0.5 to 4 mm, in particular 0.8 to 2.5 mm, can also be especially suitable for the production of molded parts of a vehicle, for example a motor vehicle.
  • the aluminum alloy of the sheet or strip has a density of Guinier-Preston I zones (GPI zones) of at least 0.25 ⁇ 10 23 GPI zones / m 3 with at least 700 atoms per GPI zone, measured using Felfer's evaluation method (cf. P.
  • the aluminum alloy of the sheet or strip has a density of Guinier-Preston I zones (GPI zones) of at most 5.0 ⁇ 10 23 GPI zones / m 3 with at least 700 atoms per GPI zone .
  • the sheet metal or strip according to the invention can be suitable for a vehicle part, preferably a body part.
  • the stabilization annealing treatment is preferably carried out at 95 ° C. (degrees Celsius) to 125 ° C. for at least 20 minutes (minutes) and a maximum of 10 hours (hours) in order to get through this Temperature control to prepare the sheet or strip reproducibly for a comparatively high artificial curing reaction, in particular paint bake response (PBR).
  • This artificial hardening reaction for example PBR, can be increased further if the stabilization annealing treatment is carried out at 100 ° C. to 120 ° C. and / or for at least 2 h and a maximum of 4 h.
  • the solution heat treatment is carried out at 450 ° C. to 500 ° C., in particular at 460 ° C. to 490 ° C. Recrystallization can also occur in the course of the solution treatment.
  • the accelerated cooling takes place with a cooling rate of the sheet or strip of at least 10 ° C / s.
  • the accelerated cooling is preferably carried out at a cooling rate of at least 20 ° C./s.
  • under certified cooling is a faster cooling than cooling at room temperature and still air (cf. Friedrich Ostermann, Application Technology Aluminum, 3rd edition, published in 2014: Cooling after solution annealing en).
  • the hot rolling is preferably carried out at a temperature of the sheet or strip of 310 ° C. to a maximum of 440 ° C. in order, for example, to reliably avoid edge cracks and crocodiling during hot rolling.
  • the method according to the invention can therefore be particularly process-reliable.
  • the advantages according to the invention with regard to high deformability for complex geometry and high yield point R p0.2 can turn out to be particularly advantageous if the aluminum sheet or strip in question is used for, in particular cold forming, in particular sheet metal forming, and subsequent hot curing, in particular stoving, preferably lacquer stoving, to form a molded part, in particular a vehicle part, preferably a body part, for example the outer skin, in a vehicle.
  • Advantageous process conditions can result if the varnish is baked at 150 ° C. to 200 ° C. for at least 10 and a maximum of 30 minutes, in particular at 170 ° C. to 190 ° C. for at least 15 and a maximum of 25 minutes.
  • Alloy 1 is a known AA5182 alloy as a reference alloy.
  • Alloys 2 to 4 represent alloys according to the invention and contain balanced contents of Zn, Zn + Cu or Zn + Cu + Ag. The remainder of all alloys is aluminum and impurities that are unavoidable due to the manufacturing process, each with a maximum of 0.05% by weight and a total of 0.15% by weight. If necessary, alloys 1 to 4 can also contain 0.1% by weight of chromium (Cr).
  • the alloys listed in Table 1 were examined with regard to their mechanical properties R p0.2 and elongation at break A by means of a tensile test. The tests were carried out in the T4-FH condition as well as after the paint baking cycle (PB) with a previous 2% reshaping. In addition, the density of Guinier Preston I zones (GPI zones) with at least 700 atoms per GPI zone was measured using the Felfer evaluation method using atomic probe tomography (atomic probe of the LEAP 3000HR type) as already described above . Table 2: Characteristic values of the alloys examined.
  • the aluminum alloys 2 to 4 according to the invention achieve an unexpectedly high paint bake response (PBR) of up to 195 MPa compared to alloy 1 without the formability (or elongation) in the T4-FH state to deteriorate significantly.
  • PBR paint bake response
  • the alloys according to the invention, in combination with the production method according to the invention are particularly suitable for molded parts of a body.
  • alloys according to the invention show a delayed onset of the PLC effect and thus a reduction in flow figures of type B.
  • alloys 2 to 4 in the T4-FH state have an increasing density of Guinier-Preston I zones (GPI zones) with at least 700 atoms per GPI zone
  • this density increasing Guinier-Preston I zones (GPI zones) with at least 700 atoms per GPI zone is designated in Table 2 as GPI zone density *.
  • GPI zone density * of 1.6 ⁇ 10 23 GPI zones / m 3 already showed a surprisingly high R p0.2 gain in strength after the PB of over 400 MPa, as can be seen in alloy 3, which in Alloy 4 turns out to be even higher.
  • a maximum density of Guinier-Preston I zones of 5 ⁇ 10 23 GPI zones / m 3 with at least 700 atoms per GPI zone can be sufficient.

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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)
  • Laminated Bodies (AREA)
  • Metal Rolling (AREA)
  • Coating With Molten Metal (AREA)
  • Body Structure For Vehicles (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Electroplating Methods And Accessories (AREA)
  • Application Of Or Painting With Fluid Materials (AREA)
  • Bending Of Plates, Rods, And Pipes (AREA)
  • Gasket Seals (AREA)
  • Paints Or Removers (AREA)
  • Preventing Corrosion Or Incrustation Of Metals (AREA)
EP20190782.1A 2020-01-07 2020-08-12 Blech oder band aus einer aushärtbaren aluminiumlegierung, ein daraus gefertigtes fahrzeugteil, eine verwendung und ein verfahren zur herstellung des blechs oder bands Pending EP3848476A1 (de)

Priority Applications (9)

Application Number Priority Date Filing Date Title
CA3166639A CA3166639A1 (en) 2020-01-07 2021-01-07 Sheet or strip made of a hardenable aluminum alloy, a vehicle part made therefrom, a use, and a method for producing the sheet or strip
IL294402A IL294402A (en) 2020-01-07 2021-01-07 A sheet or strip made of a hardenable aluminum alloy, a part of a vehicle made from it, use and method for the production of the sheet or strip
CN202180008190.XA CN115151667A (zh) 2020-01-07 2021-01-07 由能硬化的铝合金制成的板材或带材、由其生产的车辆部件、用途和用于生产板材或带材的方法
AU2021206534A AU2021206534A1 (en) 2020-01-07 2021-01-07 Sheet or strip made of an aluminum alloy which can be hardened, a vehicle part made therefrom, a use, and a method for producing the sheet or strip
PCT/EP2021/050203 WO2021140163A1 (de) 2020-01-07 2021-01-07 Blech oder band aus einer aushärtbaren aluminiumlegierung, ein daraus gefertigtes fahrzeugteil, eine verwendung und ein verfahren zur herstellung des blechs oder bands
JP2022537081A JP2023509367A (ja) 2020-01-07 2021-01-07 析出硬化性アルミニウム合金製の板材または帯材、該板材または帯材から構成された車両部品、該板材または帯材の使用および製造方法
US17/791,147 US20230042050A1 (en) 2020-01-07 2021-01-07 Sheet or strip made of a hardenable aluminum alloy, a vehicle part made therefrom, a use, and a method for producing the sheet or strip
BR112022013432A BR112022013432A2 (pt) 2020-01-07 2021-01-07 Chapa ou tira a partir de uma liga de alumínio endurecível, uma peça de veículo fabricada a partir dessa, uso e processo para a produção da chapa ou tira
MX2022008360A MX2022008360A (es) 2020-01-07 2021-01-07 Chapa o banda de una aleacion de aluminio curable, una pieza de vehiculo fabricada a partir de esta, un uso y un procedimiento para la fabricacion de la chapa o banda.

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP20150632 2020-01-07

Publications (1)

Publication Number Publication Date
EP3848476A1 true EP3848476A1 (de) 2021-07-14

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EP20190782.1A Pending EP3848476A1 (de) 2020-01-07 2020-08-12 Blech oder band aus einer aushärtbaren aluminiumlegierung, ein daraus gefertigtes fahrzeugteil, eine verwendung und ein verfahren zur herstellung des blechs oder bands

Country Status (10)

Country Link
US (1) US20230042050A1 (pt)
EP (1) EP3848476A1 (pt)
JP (1) JP2023509367A (pt)
CN (1) CN115151667A (pt)
AU (1) AU2021206534A1 (pt)
BR (1) BR112022013432A2 (pt)
CA (1) CA3166639A1 (pt)
IL (1) IL294402A (pt)
MX (1) MX2022008360A (pt)
WO (1) WO2021140163A1 (pt)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4332260A1 (de) 2022-09-05 2024-03-06 AMAG rolling GmbH Aushärtbaren aluminiumlegierung, metallband oder -blech aus dieser aluminiumlegierung, verfahren zur herstellung dieses metallbands oder -blechs und dessen verwendung bei einem superplastischen umformen

Citations (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4140556A (en) 1976-04-16 1979-02-20 Sumitomo Light Metal Industries, Ltd. Aluminum alloy sheet
JPS616244A (ja) * 1984-06-21 1986-01-11 Sumitomo Light Metal Ind Ltd 微細結晶粒高強度成形加工用合金とその製造法
JPS61179843A (ja) * 1985-02-04 1986-08-12 Sumitomo Light Metal Ind Ltd メツキ性にすぐれた磁気デイスク用アルミニウム合金
JP2011184795A (ja) * 2010-02-12 2011-09-22 Kobe Steel Ltd 成形性に優れたアルミニウム合金板
DE112011103667T5 (de) 2010-11-05 2013-08-01 Aleris Aluminum Duffel Bvba Automobil-Formteil aus einem Aluminiumlegierungsprodukt und Verfahren zu seiner Herstellung
JP5342201B2 (ja) * 2008-09-26 2013-11-13 株式会社神戸製鋼所 成形性に優れたアルミニウム合金板
US20170081749A1 (en) * 2014-03-17 2017-03-23 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Aluminum alloy sheet for structural components
CN107022725A (zh) * 2017-04-20 2017-08-08 北京科技大学 一种提高时效强化型Al‑Mg‑Zn合金晶间腐蚀性能的热处理工艺
US20170349989A1 (en) 2014-11-11 2017-12-07 Novelis Inc. Multipurpose heat treatable aluminum alloys and related processes and uses
US20180023174A1 (en) * 2015-03-04 2018-01-25 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Aluminum alloy sheet
EP3521466A1 (en) * 2015-10-30 2019-08-07 Novelis Inc. High strength 7xxx aluminum alloys and methods of making the same
CN110541096A (zh) * 2019-09-11 2019-12-06 北京科技大学 一种高强易焊Al-Mg-Zn-Cu合金及其制备方法
EP3690076A1 (de) * 2019-01-30 2020-08-05 Amag Rolling GmbH Verfahren zur herstellung eines blechs oder bands aus einer aluminiumlegierung sowie ein dadurch hergestelltes blech, band oder formteil

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CN104625571A (zh) * 2015-01-06 2015-05-20 湖南科技大学 一种时效强化铝合金的切削加工方法
CN104862551B (zh) * 2015-05-21 2017-09-29 北京科技大学 Al‑Mg‑Cu‑Zn系铝合金及铝合金板材制备方法

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4140556A (en) 1976-04-16 1979-02-20 Sumitomo Light Metal Industries, Ltd. Aluminum alloy sheet
JPS616244A (ja) * 1984-06-21 1986-01-11 Sumitomo Light Metal Ind Ltd 微細結晶粒高強度成形加工用合金とその製造法
JPS61179843A (ja) * 1985-02-04 1986-08-12 Sumitomo Light Metal Ind Ltd メツキ性にすぐれた磁気デイスク用アルミニウム合金
JP5342201B2 (ja) * 2008-09-26 2013-11-13 株式会社神戸製鋼所 成形性に優れたアルミニウム合金板
JP2011184795A (ja) * 2010-02-12 2011-09-22 Kobe Steel Ltd 成形性に優れたアルミニウム合金板
DE112011103667T5 (de) 2010-11-05 2013-08-01 Aleris Aluminum Duffel Bvba Automobil-Formteil aus einem Aluminiumlegierungsprodukt und Verfahren zu seiner Herstellung
US20170081749A1 (en) * 2014-03-17 2017-03-23 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Aluminum alloy sheet for structural components
US20170349989A1 (en) 2014-11-11 2017-12-07 Novelis Inc. Multipurpose heat treatable aluminum alloys and related processes and uses
US20180023174A1 (en) * 2015-03-04 2018-01-25 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Aluminum alloy sheet
EP3521466A1 (en) * 2015-10-30 2019-08-07 Novelis Inc. High strength 7xxx aluminum alloys and methods of making the same
CN107022725A (zh) * 2017-04-20 2017-08-08 北京科技大学 一种提高时效强化型Al‑Mg‑Zn合金晶间腐蚀性能的热处理工艺
EP3690076A1 (de) * 2019-01-30 2020-08-05 Amag Rolling GmbH Verfahren zur herstellung eines blechs oder bands aus einer aluminiumlegierung sowie ein dadurch hergestelltes blech, band oder formteil
CN110541096A (zh) * 2019-09-11 2019-12-06 北京科技大学 一种高强易焊Al-Mg-Zn-Cu合金及其制备方法

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Title
FRIEDRICH OSTERMANN: "Anwendungstechnologie Aluminium", 2014, pages: 175
P. FELFER ET AL.: "Detecting and extracting clusters in atom probe data: a simple, automated method using Voronoi cells", ULTRAMICROSCOPY, vol. 150, 2015, pages 30 - 36

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4332260A1 (de) 2022-09-05 2024-03-06 AMAG rolling GmbH Aushärtbaren aluminiumlegierung, metallband oder -blech aus dieser aluminiumlegierung, verfahren zur herstellung dieses metallbands oder -blechs und dessen verwendung bei einem superplastischen umformen

Also Published As

Publication number Publication date
WO2021140163A1 (de) 2021-07-15
MX2022008360A (es) 2022-12-15
CN115151667A (zh) 2022-10-04
AU2021206534A1 (en) 2022-06-30
IL294402A (en) 2022-08-01
JP2023509367A (ja) 2023-03-08
US20230042050A1 (en) 2023-02-09
CA3166639A1 (en) 2021-07-15
BR112022013432A2 (pt) 2022-09-13

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