EP3486343B1 - Alliage d'aluminium durcissable - Google Patents

Alliage d'aluminium durcissable Download PDF

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Publication number
EP3486343B1
EP3486343B1 EP18174637.1A EP18174637A EP3486343B1 EP 3486343 B1 EP3486343 B1 EP 3486343B1 EP 18174637 A EP18174637 A EP 18174637A EP 3486343 B1 EP3486343 B1 EP 3486343B1
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European Patent Office
Prior art keywords
aluminum alloy
aluminum
temperable
sheet
molded part
Prior art date
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Application number
EP18174637.1A
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German (de)
English (en)
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EP3486343A1 (fr
Inventor
Mark Erlwein
Heinz Werner HÖPPEL
Felix Glöckel
Bodo Gerold
Stefan Pogatscher
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
Audi AG
Friedrich Alexander Univeritaet Erlangen Nuernberg FAU
Original Assignee
Amag Rolling GmbH
Audi AG
Friedrich Alexander Univeritaet Erlangen Nuernberg FAU
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Application filed by Amag Rolling GmbH, Audi AG, Friedrich Alexander Univeritaet Erlangen Nuernberg FAU filed Critical Amag Rolling GmbH
Priority to SI201830016T priority Critical patent/SI3486343T1/sl
Priority to US16/192,928 priority patent/US11851736B2/en
Publication of EP3486343A1 publication Critical patent/EP3486343A1/fr
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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
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • 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
    • C22F1/053—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 zinc as the next major constituent

Definitions

  • the invention relates to a hardenable aluminum alloy, an aluminum sheet or strip of such an aluminum alloy, a molded part and a method for producing such a molded article and a use of a circuit board.
  • DE 112011 103667 T5 an aluminum alloy containing 1.5 to 4 wt% zinc (Zn), 0.3 to 1.5 wt% magnesium (Mg), and 0 to 0.5 wt% silicon (Si).
  • the aluminum alloys of DE112011103667T5 have a comparatively high precipitation pressure, for example on Mg 2 Si phases, which admittedly increases the strength but disadvantageously does not permit sheet metal forming with a low first yield strength R p0.2 of, for example, at most 160 MPa. Moldings with comparatively complex geometry - as required, for example, in vehicle parts, preferably body parts, in particular the outer skin - are so not be produced.
  • the object of the invention is therefore to provide an aluminum alloy which has not only a high plastic deformability during forming, but also a high heat curing reaction, in particular paint bake response (PBR).
  • PBR paint bake response
  • the aluminum alloy in the alloying elements magnesium (Mg) and silicon (Si) compared to zinc (Zn) can allow Mg 2 Si phases, which increase strength - whereby the aluminum alloy despite a comparatively low thermosetting temperature, for example baking temperature, in the state T6 a second yield strength R p0.2 can reach at least 250 MPa.
  • the aluminum alloy can therefore be distinguished by a comparatively high thermal hardening reaction, in particular paint bake response (PBR).
  • these Mg 2 Si phases also have an increasing strength on an aluminum alloy in state T4 or state T4-FH - which, in particular, does not permit cold forming, in particular sheet metal forming, with a first yield strength R p0.2 of not more than 160 MPa.
  • the aluminum alloy adjusted according to the invention in the alloying elements Mg, Si and Zn as well as the trace elements Sn and / or Cd and / or In can fulfill not only the second yield strength R p0,2 , but also the first yield strength R p0,2 in the condition T4 or Condition T4-FH ensure - even at relatively low hot curing temperature.
  • this aluminum alloy according to the invention in the content limits can ensure a uniform elongation A g similar to an aluminum alloy of the type EN AW 6016, as a result of which excellent plastic deformability can be ensured.
  • the aluminum alloy according to the invention may therefore have a particularly good suitability for a rolled aluminum sheet or strip, which is suitable for a Method for producing a molded part of a vehicle, preferably body part, for example the outer skin, may be suitable.
  • the aluminum alloy may, due to its production, have unavoidable impurities, in each case not more than 0.05% by weight and not more than 0.15% by weight in total.
  • vehicle is understood to mean, for example, a land vehicle, watercraft and / or aircraft.
  • the state T4-FH is achieved by a stabilization annealing treatment by subjecting the aluminum alloy in the state T4 (solution annealing and quenching) to a heat treatment, in particular, a thermal shock.
  • This heat treatment preferably follows the T4 treatment (solution annealing and quenching) -
  • Examples of such a Stabilmaschinesglüh harmony are from the literature (see Friedrich Ostermann: Application Technology Aluminum, 3rd edition, release year 2014, ISBN 987-3-662-43806-0 , Page 138), DE 112011 103667 T5 etc. known - which is often referred to as pre-storage treatment.
  • a first yield strength R p0.2 of at most 160 MPa and a second yield strength R p0.2 of at least 250 MPa of the aluminum alloy can be made reproducible if it has 2.5 to 3.4% by weight Zn. This is especially true when the aluminum alloy has from 2.7 to 3.3 wt% Zn. In addition, it is thus possible to improve the solubility of the trace elements Sn and / or Cd and / or In in the solid solution of the aluminum alloy.
  • High strength in the state T6 despite low bake temperature can be made possible when the aluminum alloy of 0.8 to 1.2 wt .-% Mg, in particular 0.85 to 1.15 wt .-% Mg, has.
  • the aluminum alloy has from 0.35 to 0.7% by weight of Si, in particular from 0.4 to 0.6% by weight of Si.
  • tin (Sn) and / or indium (In) and / or cadmium (Cd) in the aluminum alloy Proportion of over 40, in particular over 80, to less than 400, in particular less than 200, atomic ppm.
  • tin (Sn) and / or indium (In) and / or cadmium (Cd) in the aluminum alloy have a content of 100 atomic ppm.
  • the aluminum alloy has from 0.15 to 0.35% by weight of copper (Cu) and / or from 0.1 to 0.3% by weight of silver (Ag) and / or from 0.05 to 0.25% by weight % Iron (Fe) and / or from 0.05 to 0.12% by weight manganese (Mn) and / or from 0.05 to 0.15% by weight titanium (Ti) and / or from 0 , 02 to 0.2 wt .-% tin (Sn) and / or indium (In) and / or cadmium (Cd), is an adverse effect on the tuning of the aluminum alloy in the alloying elements Mg, Si and Zn and the trace elements Sn , Cd and / or in not to be feared.
  • Copper (Cu), iron (Fe) and / or silver (Ag) can further increase the strength of the aluminum alloy - in particular Fe can be distinguished in this respect.
  • Manganese (Mn) can to a certain extent bind Fe in the aluminum alloy and thus reduce negative effects of iron on the plastic deformability of the aluminum alloy.
  • Titanium (Ti) can contribute to grain refining and further increase plastic deformability and strength.
  • the strength of the aluminum alloy can be increased without adversely affecting the tuning of the aluminum alloy in the alloying elements Mg, Si and Zn and the trace elements Sn , Cd and / or in to fear.
  • the curable aluminum alloy according to the invention may be particularly suitable for an aluminum sheet or strip - for example, in order to produce a molded part of a vehicle, preferably a body part, for example the outer skin.
  • An aluminum sheet or strip with a thickness of 0.5 to 4 mm, in particular from 1 to 3 mm, may be particularly suitable for the production of a molded part of a vehicle.
  • a molded part in particular a vehicle part, preferably a body part, is produced from an aluminum sheet or strip according to the invention, this can be ensured after hot curing, for example a stoving cycle, preferably paint stoving cycle, maximum yield strength Rp0.2 and ductility.
  • a stoving cycle preferably paint stoving cycle, maximum yield strength Rp0.2 and ductility.
  • under-forming methods for example, deep-drawing, stretch-forming, pressing, etc.
  • Under forming process is a cold or warm or warm forming etc. to understand.
  • a cold forming preferably cold sheet forming
  • a burn-in cycle such as paint bake cycle, may be heat treatment in a bake-hardening process, eg, KTL process.
  • the temperature, in particular stoving temperature, during hot curing is preferably at most 165 degrees Celsius.
  • inventive advantages in high ductility for complex geometry and high yield strength R p0,2 of at least 250 MPa, for example after a baking cycle with low baking temperature may prove to be particularly advantageous when a board of the aluminum sheet or strip according to the invention, in particular cold , Forming, in particular sheet metal forming, and hot curing, in particular firing, preferably paint baking, to a molded part, in particular vehicle part, preferably body part, for example the outer skin, is used in a vehicle.
  • rolled semifinished products namely thin sheets of various aluminum alloys were produced - after a week of storage at room temperature
  • these thin sheets in the T4-FH state are shaped into a molded part, namely the body part of the outer skin, by cold sheet forming.
  • these moldings were subjected to cathodic dip painting (CDC) with a bake cycle at a bake temperature of 165 degrees Celsius.
  • Table 1 Overview of the investigated alloys in% by weight. alloys Zn mg Si sn Cu Mn Cr Ag Fe Ti 1 2 1 0.3 ⁇ 0.05 ⁇ 0.05 ⁇ 0.05 ⁇ 0.05 ⁇ 0.1 ⁇ 0.1 2 3 1 0.5 0.04 ⁇ 0.05 ⁇ 0.05 ⁇ 0.05 ⁇ 0.1 ⁇ 0.1 3 3 1 0.5 0.04 0.17 0.08 ⁇ 0.05 ⁇ 0.05 0.16 0.07 4 3 1 0.5 0.04 0.17 0.08 ⁇ 0.05 0.15 0.16 0.07
  • Mg magnesium
  • the first yield strength R p0.2 and the uniform elongation A g of the aluminum alloy in the T4-FH state were determined.
  • the second yield strength R p0.2 and also the uniform elongation A g of the aluminum alloy in the condition T6 were determined.
  • Table 2 Mechanical characteristics of the alloys investigated. alloys T4 FH T6 R p0.2 [MPa] A g [%] R p0.2 [MPa] A g [%] 1 120 20 210 17 2 150 19 245 15 3 150 19 250 15 4 160 18 265 14
  • the aluminum alloys 2, 3 and 4 according to the invention meet the required first yield strength R p0.2 of 150 MPa as below 160 MPa and the required second yield strength R p0.2 in the range of 250 MPA - even with a comparatively low stoving temperature of 165 degrees Celsius to reach the T6 condition.
  • the aluminum alloy 4 with silver in the state T6 has an increased yield strength R p0.2 with negligibly reduced uniform elongation A g .
  • the aluminum alloys 2, 3 and 4 according to the invention are distinguished by an alloy which is particularly adjusted in the alloying elements Mg, Si and Zn and the trace elements Sn, Cd and / or In.
  • the alloying elements can advantageously act on the heat-hardening of the aluminum alloy in order to ensure all required yield strengths R p0.2 in the state T4 or T4-FH and in T6 - the latter second yield strengths R p0.2 in the state T6 even when a low heat setting temperature is used , resulting in a high paint bake response (PBR).
  • PBR paint bake response
  • all inventive aluminum alloys 2, 3 and 4 in state T4-FH show a high uniform elongation A g during forming, in particular cold sheet forming, which allows complex geometries on the molded part.
  • the uniform elongation A g of the aluminum alloys 2, 3 and 4 according to the invention in the T6 state is also high, which ensures high ductility on the molded part.
  • the aluminum alloys 2, 3 and 4 according to the invention also have a particularly good suitability for molded parts of the body.

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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)
  • Laminated Bodies (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)

Claims (14)

  1. Alliage d'aluminium durcissable comprenant de 2,5 à 3,5 % en poids de zinc (Zn), de 0,5 à 1,5 % en poids de magnésium (Mg), de 0,2 à 0,8 % en poids de silicium (Si), de 0,005 à 0,2 % en poids d'étain (Sn) et/ou d'indium (In) et/ou de cadmium (Cd),
    facultativement jusqu'à 0,35 % en poids de cuivre (Cu), jusqu'à 0,3 % en poids d'argent (Ag), jusqu'à 0,25 % en poids de fer (Fe), jusqu'à 0,12 % en poids de manganèse (Mn), jusqu'à 0,15 % en poids de titane (Ti)
    et de l'aluminium pour le reste, ainsi que les impuretés inévitables dans le processus de fabrication, la teneur en magnésium (Mg) et en silicium (Si) satisfaisant la relation ordinale 0,4 % en poids Si − 0,15 < % en poids Mg < 0,7 % en poids Si − 0,2 .
    Figure imgb0003
  2. Alliage d'aluminium durcissable selon la revendication 1, caractérisé en ce qu'il contient de 2,5 à 3,4 % en poids de zinc, en particulier de 2,7 à 3,3 % en poids de zinc.
  3. Alliage d'aluminium durcissable selon la revendication 1 ou 2, caractérisé en ce que qu'il contient de 0,8 à 1,2 % en poids de magnésium, en particulier de 0,85 à 1,15 % en poids de magnésium.
  4. Alliage d'aluminium durcissable selon la revendication 1, 2 ou 3, caractérisé en ce que qu'il contient de 0,35 à 0,7 % en poids de silicium, en particulier de 0,4 à 0,6 % en poids de silicium.
  5. Alliage d'aluminium durcissable selon l'une des revendications 1 à 4, caractérisé en ce que l'étain (Sn) et/ou l'indium (In) et/ou le cadmium (Cd) représentent dans l'alliage d'aluminium une part de 40 ppm atomiques, en particulier plus de 80 à moins de 400, en particulier moins de 200, par exemple 100 ppm atomiques.
  6. Alliage d'aluminium durcissable selon l'une des revendications 1 à 5, caractérisé en ce que qu'il contient de 0,15 à 0,35 % en poids de cuivre (Cu) et/ou de 0,1 à 0,3 % en poids d'argent (Ag) et/ou de 0,05 à 0,25 % en poids de fer (Fe) et/ou de 0,05 à 0,12 % en poids de manganèse (Mn) et/ou de 0,05 à 0,15 % en poids de titane (Ti) et/ou de 0,02 à 0,2 % en poids d'étain (Sn) et/ou d'indium (In) et/ou de cadmium (Cd).
  7. Alliage d'aluminium durcissable selon la revendication 6, caractérisé en ce que qu'il contient de 0,25 à 0,35 % en poids de cuivre (Cu).
  8. Tôle ou feuillard d'aluminium fait d'un alliage d'aluminium durcissable selon l'une des revendications 1 à 7.
  9. Tôle ou feuillard d'aluminium selon la revendication 8 dans l'état T4 ou dans l'état T4 avec un recuit de stabilisation (T4-FH).
  10. Tôle ou feuillard d'aluminium selon la revendication 8 ou 9 ayant une épaisseur de 0,5 à 4 mm, en particulier de 1 à 3 mm.
  11. Pièce mise en forme, en particulier pièce de véhicule, de préférence pièce de carrosserie, fabriquée à partir d'une tôle ou d'un feuillard d'aluminium selon l'une des revendications 8 à 10.
  12. Procédé pour la fabrication d'une pièce mise en forme, en particulier pièce de véhicule, de préférence pièce de carrosserie, dans laquelle un flan est fabriqué à partir de la tôle ou du feuillard d'aluminium selon l'une des revendications 8 à 10, la pièce mise en forme est produite à partir du flan par un procédé de déformation, en particulier à froid, en particulier un procédé de déformation de la tôle, et la pièce mise en forme est ensuite soumise à un durcissement à chaud, en particulier un cycle de cuisson, de préférence un cycle de cuisson de peinture.
  13. Procédé selon la revendication 12, que la pièce mise en forme est soumise à un durcissement à chaud à une température, en particulier une température de cuisson, de 165 degrés Celsius au maximum.
  14. Utilisation d'un flan d'une tôle ou d'un feuillard d'aluminium selon l'une des revendications 8 à 10 pour le formage, en particulier à froid, en particulier le formage de tôle, et le durcissement à chaud, en particulier la cuisson, de préférence la cuisson de peinture, pour produire une pièce mise en forme, en particulier une pièce de véhicule, de préférence une pièce de carrosserie, par exemple une enveloppe extérieure, dans un véhicule.
EP18174637.1A 2017-11-16 2018-05-28 Alliage d'aluminium durcissable Active EP3486343B1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
SI201830016T SI3486343T1 (sl) 2017-11-16 2018-05-28 Strdljiva aluminijeva zlitina
US16/192,928 US11851736B2 (en) 2017-11-16 2018-11-16 Hardenable aluminum alloy

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP17202190 2017-11-16

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EP3486343A1 EP3486343A1 (fr) 2019-05-22
EP3486343B1 true EP3486343B1 (fr) 2019-08-28

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US (1) US11851736B2 (fr)
EP (1) EP3486343B1 (fr)
ES (1) ES2760449T3 (fr)
HU (1) HUE047147T2 (fr)
SI (1) SI3486343T1 (fr)

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4794862B2 (ja) * 2004-01-07 2011-10-19 新日本製鐵株式会社 塗装焼付け硬化性に優れた６０００系アルミニウム合金板の製造方法
DE112011103667T5 (de) 2010-11-05 2013-08-01 Aleris Aluminum Duffel Bvba Automobil-Formteil aus einem Aluminiumlegierungsprodukt und Verfahren zu seiner Herstellung
CN103789583B (zh) * 2014-01-22 2016-06-08 北京科技大学 快速时效响应型Al-Mg-Si-Cu-Zn系合金及其制备方法
CN103757507B (zh) * 2014-02-25 2016-04-27 北京科技大学 一种汽车车身外板用高烤漆硬化铝合金材料及其制备方法

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* Cited by examiner, † Cited by third party
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Publication number Publication date
US11851736B2 (en) 2023-12-26
HUE047147T2 (hu) 2020-04-28
EP3486343A1 (fr) 2019-05-22
SI3486343T1 (sl) 2020-02-28
US20190144977A1 (en) 2019-05-16
ES2760449T3 (es) 2020-05-14

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