EP0259232B2 - Gut bearbeitbare und schweissbare Aluminiumlegierung und Verfahren zu ihrer Herstellung - Google Patents

Gut bearbeitbare und schweissbare Aluminiumlegierung und Verfahren zu ihrer Herstellung Download PDF

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Publication number
EP0259232B2
EP0259232B2 EP87420190A EP87420190A EP0259232B2 EP 0259232 B2 EP0259232 B2 EP 0259232B2 EP 87420190 A EP87420190 A EP 87420190A EP 87420190 A EP87420190 A EP 87420190A EP 0259232 B2 EP0259232 B2 EP 0259232B2
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EP
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Prior art keywords
alloy
solution treatment
carried out
delimited
homogenisation
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Expired - Lifetime
Application number
EP87420190A
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English (en)
French (fr)
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EP0259232B1 (de
EP0259232A1 (de
Inventor
Didier Constant
Gilbert Gutmann
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.)
Constellium Issoire SAS
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Pechiney Rhenalu SAS
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Application filed by Pechiney Rhenalu SAS filed Critical Pechiney Rhenalu SAS
Priority to AT87420190T priority Critical patent/ATE64763T1/de
Publication of EP0259232A1 publication Critical patent/EP0259232A1/de
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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
    • 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 weldable boilermaking aluminum alloy containing essentially Si, Mg and Cu and its manufacturing process.
  • Alloys of the 6000 series according to the nomenclature of the Aluminum Association have been developed mainly in the form of profiles, although some of these allallies such as 6061 or 6082, are commonly found in the form of sheets or strips, intended for stamping.
  • Patent application FR 2 375 332 describes a process in which an alloy rich in Si is treated with so as to obtain a fine sub-micron precipitation (0.1 to 0.5 ⁇ m) of Si in supersaturation; this size is intermediate between the eutectic phases present in the alloy and that of the hardening phases usually observed in Al-Si-Mg-Cu alloys.
  • French patent application FR 2 360 684 describes an Al-Si-Mg-Cu alloy containing at least one of the elements which inhibit recrystallization from the Mn, Cr, Zr group.
  • the alloy comprises (in% by weight) contents of Si and Mg defined by the trapezoid of coordinates: Yes Mg AT) 0.5 0.1 B) 0.5 0.2 VS) 1.3 0.5 D) 1.3 0.1 Cu 0.1 - 1.5 Mn 0 - 0.15 Fe 0 - 0.35 others each ⁇ 0.05 total other ⁇ 0.15
  • the maximum Si / Mg ratio (BC side of the trapezoid) remains equal to or greater than 2.6 approximately so as to limit the precipitation of Mg 2 Si during solidification as much as possible.
  • the fine precipitation Mg 2 Si present in the alloy results only from the heat treatments undergone.
  • the secondary elements are limited for the following reasons: As explained above, the presence of Mn is not desirable; however it was admitted up to 0.15% maximum due to possible contamination in this element, due to recycling of waste. It should be noted that the alloy does not contains no intentional additions of Cr and / or Zr.
  • the Ti associated with B controls, as is known, the fineness of the primary crystallization of the products rough casting (plates, strips, billets, etc ...) and allows homogenizations and solutions more short, in particular with regard to the processing of flat products (sheets, strips).
  • the contents effective are Ti ⁇ 0.1% and B ⁇ 0.05%.
  • the Fe content is limited to 0.35% to avoid the formation of coarse primary compounds containing Fe (AlMnFeSi type).
  • Another preferred composition of the alloy according to the invention corresponds to the contents of Si and Mg, delimited by the trapezoid A'B'C'D 'of Fig. 1 with Cu: 0.1-0.25 and Mn ⁇ 0.15, the limits of the others elements being the same.
  • the hot transformation is carried out by any known means (rolling, spinning, forging, etc.) However, this must then be carried out so as to avoid coarse recrystallizations in progress of operation.
  • the temperature at the end of hot transformation to avoid these recrystallizations, must be imperatively between 270 ° and 340 ° C.
  • the alloy After possible cold transformation, the alloy is put into a complete solution. This takes place in the temperature range between 540 and 580 ° C, preferably between 550 and 570 ° C, targeting the temperature of 560 ° C.
  • the processing time varies from a few seconds to a few minutes, without being able to exceed a hour.
  • the sheets and strips thus obtained have good isotropy and grain size average not exceeding 60 ⁇ m.
  • the quenching must be rapid and depends on the thickness of the product. For sheets and strips, it is generally performed in calm or pulsed air.
  • the parts undergo hardening, under the usual conditions; the hardening is due to the precipitation of the Mg 2 Si phase and of the complex AlCuMg, AlCuMg Si phases. Tempering is typically carried out between 8 to 12 h at 165 ° C.
  • FIG. 1 represents the domain of composition of the elements Si and Mg of the alloy
  • FIG. 2 represents the domain of dissolving or homogenizing an alloy according to the invention, on a vertical section of the state diagram Al, Mg, Si at 0.2% Mg.
  • Dissolution (or homogenization) must be carried out in the single-phase field and in particular under the temperature conditions represented by the rectangle FGHI for the general range and F'G'H'I 'for the preferred range. It is obvious from these curves that for high Si contents, the treatment is delicate, since a small variation with respect to the set temperature leads either to a precipitation of Si if the temperature drops, or to a "burning" of the metal if the temperature rises.
  • This heat treatment therefore requires a precise industrial tool.
  • the dissolution of these was carried out in a passage oven at a speed of 20 m / min, the temperature holding time of 560 ° C. being of the order of 1 minute and the rate of rise in temperature of the order of 25 ° C / sec.
  • the anisotropy was estimated by making buckets and measuring the rate of the horns according to the standard AFNOR NF-A-50-301. This value is equal to 7%.
  • the grain size measured by metallography is 40 ⁇ m.
  • Sheets cut from the dissolved metal were finished by shaping parts automotive body, in this case a front cover.
  • the mechanical characteristics obtained as a function of the local hardening rate are as follows: Work hardening rate (%) Rp0.2 (MPa) Rm (MPa) AT % 0 225 285 15 5 250 290 10 10 265 295 8
  • the assembly was then brought, in an oven, to 165 ° C for 10 h.
  • the shear strength of the welded joints thus obtained is of the order of 280 MPa. We can see the good properties obtained after welding and tempering.
  • the alloy according to the invention has the following advantages: This alloy is delivered in T4 state to transformers. In this state, the alloy is ductile and lends itself well to deformation, its maturation at ambient temperature being very low. The cold-deformed part acquires better resistance characteristics by work hardening, at least locally in the most deformed zones; the softening due to annealing during the welding operation is partially offset by the structural hardening during the final tempering (T6).
  • the metal only undergoes after quenching the finishing operations (such as as dressing, leveling, etc.) strictly necessary.
  • the alloys according to the invention are mainly used in the fields of automobile bodywork and box.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)
  • Arc Welding In General (AREA)
  • Mold Materials And Core Materials (AREA)
  • Heat Treatment Of Steel (AREA)
  • Filtering Materials (AREA)
  • Heat Treatment Of Articles (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)

Claims (9)

  1. Tiefziehbare und schweißbare Aluminiumlegierung,
    dadurch gekennzeichnet,
    daß sie (in Gew.%) Si- und Mg-Gehalte, die durch das Trapez ABCD begrenzt sind, dessen Koordinaten sind: Si Mg A 0,5 0,1 B 0,5 0,2 C 1,3 0,5 D 1,3 0,1 Cu 0,10 - 0,5 Mn 0 - 0,15 Fe 0 - 0,35 Sonstige je ≤ 0,05 Sonstige gesamt ≤ 0,15 Rest: Al enthält.
    und dass sie ist frei von submikronen, wesentlich aus Silizium gebildeten Ausscheidungen.
  2. Legierung nach dem Anspruch 1,
    dadurch gekennzeichnet,
    daß sie (in Gew.%) Si- und Mg-Gehalte, die durch das Trapez A"B"C"D" begrenzt sind, dessen Koordinaten sind: Si Mg A" 0,65 0,18 B" 0,65 0,2 C" 0,95 0,28 D" 0,95 0,2 Cu 0,1 - 0,25 Mn ≤ 0,15 enthält.
  3. Legierung nach dem Anspruch 1,
    dadurch gekennzeichnet,
    daß sie (in Gew.%) Si und Mg-Gehalte, die durch das in der Figur 1 dargestellte Trapez A'B'C'D' begrenzt sind, sowie Cu 0.1 - 0.25 enthält.
  4. Legierung nach einem der Ansprüche 1 bis 3,
    dadurch gekennzeichnet,
    daß die mittlere Korngröße unter 80 µm ist.
  5. Legierung nach einem der Ansprüche 1 bis 4,
    dadurch gekennzeichnet,
    daß die mittlere Korngröße unter 60 µm ist.
  6. Verfahren zur Herstellung der Erzeugnisse nach einem der Ansprüche 1 bis 5, das den Strangguß oder halbkontinuierlichen Guß von Rohlingen, eine eventuelle Homogenisierung, eine Warmverformung, eine eventuelle Kaltverformung, ein im einphasigen Bereich erfolgtes Lösungsglühen, ein Abschrecken, eine Kaltformgebung und schließlich ein Anlassen umfaßt,
    dadurch gekennzeichnet,
    daß die Endwarmverformung zwischen 270 und 340 °C stattfindet.
  7. Verfahren nach dem Anspruch 6,
    dadurch gekennzeichnet,
    daß die Homogenisierung oder das vollständige Lösungsglühen zwischen 540 und 580 °C durchgeführt werden.
  8. Verfahren nach dem Anspruch 7,
    dadurch gekennzeichnet,
    daß die Homogenisierung oder das Lösungsglühen zwischen 550 und 570 °C stattfinden,
  9. Verfahren nach einem der Ansprüche 7 oder 8,
    dadurch gekennzeichnet,
    daß dem Lösungsglühen ein Temperaturanstieg mit einer Geschwindigkeit über 10 ° Cs vorausgeht
EP87420190A 1986-07-07 1987-07-02 Gut bearbeitbare und schweissbare Aluminiumlegierung und Verfahren zu ihrer Herstellung Expired - Lifetime EP0259232B2 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT87420190T ATE64763T1 (de) 1986-07-07 1987-07-02 Gut bearbeitbare und schweissbare aluminiumlegierung und verfahren zu ihrer herstellung.

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR8610028 1986-07-07
FR8610028A FR2601040B1 (fr) 1986-07-07 1986-07-07 Alliage d'aluminium chaudronnable et soudable et son procede de fabrication
CA000552025A CA1340260C (fr) 1986-07-07 1987-11-17 Alliage d'aluminium chaudronnable et soudable et son procede de fabrication

Publications (3)

Publication Number Publication Date
EP0259232A1 EP0259232A1 (de) 1988-03-09
EP0259232B1 EP0259232B1 (de) 1991-06-26
EP0259232B2 true EP0259232B2 (de) 1998-01-28

Family

ID=25671592

Family Applications (1)

Application Number Title Priority Date Filing Date
EP87420190A Expired - Lifetime EP0259232B2 (de) 1986-07-07 1987-07-02 Gut bearbeitbare und schweissbare Aluminiumlegierung und Verfahren zu ihrer Herstellung

Country Status (7)

Country Link
US (1) US4814022A (de)
EP (1) EP0259232B2 (de)
CA (1) CA1340260C (de)
DE (1) DE3771017D1 (de)
ES (1) ES2022918T5 (de)
FR (1) FR2601040B1 (de)
GR (2) GR3002191T3 (de)

Families Citing this family (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB9318041D0 (en) * 1993-08-31 1993-10-20 Alcan Int Ltd Extrudable a1-mg-si alloys
FR2713664B1 (fr) * 1993-11-17 1996-05-24 Pechiney Rhenalu Alliage type Al-Si-Mg à ductilité et emboutissabilité améliorées et procédé d'obtention.
US5525169A (en) * 1994-05-11 1996-06-11 Aluminum Company Of America Corrosion resistant aluminum alloy rolled sheet
US5919323A (en) * 1994-05-11 1999-07-06 Aluminum Company Of America Corrosion resistant aluminum alloy rolled sheet
CH688379A5 (de) * 1994-11-29 1997-08-29 Alusuisse Lonza Services Ag Tiefziehbare und schweissbare Aluminiumlegierung vom Typ AlMgSi
US5582660A (en) * 1994-12-22 1996-12-10 Aluminum Company Of America Highly formable aluminum alloy rolled sheet
US6267922B1 (en) 1995-09-19 2001-07-31 Alcan International Limited Precipitation-hardened aluminum alloys for automotive structural applications
FR2748035B1 (fr) * 1996-04-29 1998-07-03 Pechiney Rhenalu Alliage aluminium-silicium-magnesium pour carrosserie automobile
CH690916A5 (de) * 1996-06-04 2001-02-28 Alusuisse Tech & Man Ag Tiefziehbare und schweissbare Aluminiumlegierung vom Typ AlMgSi.
WO1998014626A1 (en) * 1996-09-30 1998-04-09 Alcan International Limited Aluminium alloy for rolled product process
US6780259B2 (en) * 2001-05-03 2004-08-24 Alcan International Limited Process for making aluminum alloy sheet having excellent bendability
FR2835533B1 (fr) * 2002-02-05 2004-10-08 Pechiney Rhenalu TOLE EN ALLIAGE Al-Si-Mg POUR PEAU DE CARROSSERIE AUTOMOBILE
US6959476B2 (en) * 2003-10-27 2005-11-01 Commonwealth Industries, Inc. Aluminum automotive drive shaft
FR2979576B1 (fr) 2011-09-02 2018-07-20 Constellium France Tole plaquee pour carrosserie automobile
KR101572773B1 (ko) 2011-11-11 2015-11-27 노벨리스 인코퍼레이티드 알루미늄 합금
ES2501041T5 (es) 2011-11-11 2018-11-13 Novelis, Inc. Aleación de aluminio
DE202011110888U1 (de) 2011-11-11 2017-01-24 Novelis Inc. Aluminiumlegierung
US11203801B2 (en) 2019-03-13 2021-12-21 Novelis Inc. Age-hardenable and highly formable aluminum alloys and methods of making the same

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3149001A (en) * 1962-04-05 1964-09-15 Aluminum Co Of America Enameled aluminous metal product
US3370943A (en) * 1965-11-04 1968-02-27 Kaiser Aluminium Chem Corp Aluminum alloy
US4082578A (en) * 1976-08-05 1978-04-04 Aluminum Company Of America Aluminum structural members for vehicles
CH624147A5 (de) * 1976-12-24 1981-07-15 Alusuisse
FR2446865A1 (fr) * 1979-01-16 1980-08-14 Pechiney Aluminium Alliage d'aluminium type a-gs a resistance mecanique et tenacite elevees

Also Published As

Publication number Publication date
DE3771017D1 (de) 1991-08-01
CA1340260C (fr) 1998-12-15
ES2022918T5 (es) 1998-03-16
GR3026104T3 (en) 1998-05-29
FR2601040A1 (fr) 1988-01-08
EP0259232B1 (de) 1991-06-26
US4814022A (en) 1989-03-21
ES2022918B3 (es) 1991-12-16
FR2601040B1 (fr) 1988-09-02
GR3002191T3 (en) 1992-12-30
EP0259232A1 (de) 1988-03-09

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