EP0259232A1 - Gut bearbeitbare und schweissbare Aluminiumlegierung und Verfahren zu ihrer Herstellung - Google Patents
Gut bearbeitbare und schweissbare Aluminiumlegierung und Verfahren zu ihrer Herstellung Download PDFInfo
- Publication number
- EP0259232A1 EP0259232A1 EP87420190A EP87420190A EP0259232A1 EP 0259232 A1 EP0259232 A1 EP 0259232A1 EP 87420190 A EP87420190 A EP 87420190A EP 87420190 A EP87420190 A EP 87420190A EP 0259232 A1 EP0259232 A1 EP 0259232A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- homogenization
- bending
- alloy according
- trapezoid
- 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
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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
- 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 to its manufacturing process.
- alloys of the 6000 series according to the nomenclature of the Aluminum Association have been developed essentially in the form of profiles, although some of these alloys such as 6061 or 6082, are commonly found in the form of sheets or strips, intended for the stamping.
- Patent application FR 2 375 332 describes a process in which an alloy rich in Si is treated 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 recrystallization inhibiting elements from the group Mn, Cr, Zr.
- Mn in particular has several drawbacks: . it gives rise to the solidification of intermetallic compounds based on Fe, Mn, Si which reduce the deformation capacity of the alloy and can initiate decohesions and ruptures, during shaping operations; . it increases the critical quenching speed and therefore limits the possibilities of heat treatments for thick products; . it gives the alloy a fairly poor corrosion behavior; . it is not suitable for short-term homogenizations, such as those generally obtained in passage ovens.
- the alloy comprises (in% by weight) contents of Si and Mg defined by the trapezoid of coordinates: Cu 0.1 - 0.5 Mn 0 - 0.2 Ti 0 - 0.1 Fe 0 - 0.35 others each ⁇ 0.05 total ⁇ 0.15 remains Al.
- 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 Mg2Si during solidification as much as possible.
- the fine precipitation Mg2Si 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 has been admitted up to 0.2% maximum due to possible contamination in this element, due to the recycling of waste. It should be noted that the alloy does not contain intentional additions of Cr and / or Zr.
- the Ti associated with B controls, as is known, the fineness of the primary crystallization of the raw casting products (plates, strips, billets, etc.) and allows shorter homogenizations and solutions, in particular in which concerns the processing of flat products (sheets, strips).
- the effective contents 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).
- the range of manufacturing of the alloys according to the invention generally comprises the continuous or semi-continuous casting of blanks, possible homogenization, hot transformation, possible cold transformation, dissolution and tempering.
- homogenization at high temperature between 550 ° C and 570 ° C with a holding time of 6 to 24 hours is desirable. Homogenization is preferably preceded by a slow rise in temperature.
- 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 during operation. In the case of sheets and strips, these coarse hot recrystallizations are the source of macroscopic deformation lines, visible after stamping, therefore unacceptable for this application.
- the temperature at the end of hot transformation to avoid these recrystallizations, must imperatively be 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 temperature rise before dissolving must be rapid (V ⁇ 10 ° C / sec) and dissolving preferably carried out either in a through oven, or in a sheet-to-sheet processing oven.
- the processing time varies from a few seconds to a few minutes, without being able to exceed one hour.
- the sheets and strips thus obtained have good isotropy and an average grain size not exceeding 60 ⁇ m.
- the quenching must be rapid and depends on the thickness of the product. For sheets and strips, it is generally carried out in calm or pulsed air.
- the parts undergo hardening income, under the usual conditions; the hardening is due to the precipitation of the Mg2Si 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 field of composition of the elements Si and Mg of the alloy
- FIG. 2 represents the field of dissolution or homogenization of 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.
- 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 time for keeping at temperature of 560 ° C. being of the order of 1 minute and the speed of temperature rise about 25 ° C / sec.
- the anisotropy was estimated by making buckets and measuring the rate of the horns according to the AFNOR NF-A-50-301 standard. 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 of the automobile body, in this case a front cover.
- Example 1 A sheet of the same composition as that of Example 1 was welded to another sheet of the same composition by spot welding, under the following conditions: "Mallory 328" tapered electrode with apex angle 60 ° and pellet diameter ⁇ 5.5 mm. Support force: 400 kg Intensity: 27,000 A Frequency: 2 Hz.
- 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 undergoes after quenching only the finishing operations (such as dressing, leveling, etc.) which are strictly necessary.
- the alloys according to the invention are mainly used in the fields of automobile bodywork and casing.
Landscapes
- 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)
- Filtering Materials (AREA)
- Pressure Welding/Diffusion-Bonding (AREA)
- Heat Treatment Of Articles (AREA)
- Mold Materials And Core Materials (AREA)
- Heat Treatment Of Steel (AREA)
- Arc Welding In General (AREA)
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 true EP0259232A1 (de) | 1988-03-09 |
EP0259232B1 EP0259232B1 (de) | 1991-06-26 |
EP0259232B2 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) |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1995014113A1 (fr) * | 1993-11-17 | 1995-05-26 | Pechiney Rhenalu | Alliage de type aluminium-silicon-magnesium a ductilite et emboutissabilite ameliorees et procede d'obtention |
WO1995031580A1 (en) * | 1994-05-11 | 1995-11-23 | Aluminum Company Of America | Corrosion resistant aluminum alloy rolled sheet |
EP0714993A1 (de) * | 1994-11-29 | 1996-06-05 | Alusuisse-Lonza Services AG | Tiefziehbare und schweissbare Aluminiumlegierung vom Typ ALMgSi |
EP0811700A1 (de) * | 1996-06-04 | 1997-12-10 | Alusuisse Technology & Management 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 |
WO2013030469A1 (fr) | 2011-09-02 | 2013-03-07 | Constellium France | Tôle plaquée pour carrosserie automobile |
Families Citing this family (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB9318041D0 (en) * | 1993-08-31 | 1993-10-20 | Alcan Int Ltd | Extrudable a1-mg-si alloys |
US5919323A (en) * | 1994-05-11 | 1999-07-06 | Aluminum Company Of America | Corrosion resistant aluminum alloy rolled sheet |
US5582660A (en) * | 1994-12-22 | 1996-12-10 | Aluminum Company Of America | Highly formable aluminum alloy rolled sheet |
EP0851942B2 (de) * | 1995-09-19 | 2005-08-24 | Alcan International Limited | Verwendung von gewalzte aluminiumlegierungen für konstruktionsteile von fahrzeuge |
FR2748035B1 (fr) * | 1996-04-29 | 1998-07-03 | Pechiney Rhenalu | Alliage aluminium-silicium-magnesium pour carrosserie automobile |
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 |
RU2596509C2 (ru) | 2011-11-11 | 2016-09-10 | Новелис Инк. | Алюминиевый сплав |
ES2501041T5 (es) | 2011-11-11 | 2018-11-13 | Novelis, Inc. | Aleación de aluminio |
DE202011110888U1 (de) | 2011-11-11 | 2017-01-24 | Novelis Inc. | Aluminiumlegierung |
CN113574192A (zh) | 2019-03-13 | 2021-10-29 | 诺维尔里斯公司 | 可时效硬化且可高度成形的铝合金及其制备方法 |
Citations (5)
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 |
FR2360684A1 (fr) * | 1976-08-05 | 1978-03-03 | Aluminum Co Of America | Elements de structure ameliores en aluminium, pour vehicules automobiles |
FR2375332A1 (fr) * | 1976-12-24 | 1978-07-21 | Alusuisse | Procede de fabrication de toles d'aluminium bien transformables, pauvres en cornes et d'une haute resistance mecanique |
FR2446865A1 (fr) * | 1979-01-16 | 1980-08-14 | Pechiney Aluminium | Alliage d'aluminium type a-gs a resistance mecanique et tenacite elevees |
-
1986
- 1986-07-07 FR FR8610028A patent/FR2601040B1/fr not_active Expired
-
1987
- 1987-06-30 US US07/068,118 patent/US4814022A/en not_active Expired - Lifetime
- 1987-07-02 DE DE8787420190T patent/DE3771017D1/de not_active Expired - Lifetime
- 1987-07-02 ES ES87420190T patent/ES2022918T5/es not_active Expired - Lifetime
- 1987-07-02 EP EP87420190A patent/EP0259232B2/de not_active Expired - Lifetime
- 1987-11-17 CA CA000552025A patent/CA1340260C/fr not_active Expired - Fee Related
-
1991
- 1991-06-27 GR GR90401165T patent/GR3002191T3/el unknown
-
1998
- 1998-02-12 GR GR980400273T patent/GR3026104T3/el unknown
Patent Citations (5)
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 |
FR2360684A1 (fr) * | 1976-08-05 | 1978-03-03 | Aluminum Co Of America | Elements de structure ameliores en aluminium, pour vehicules automobiles |
FR2375332A1 (fr) * | 1976-12-24 | 1978-07-21 | Alusuisse | Procede de fabrication de toles d'aluminium bien transformables, pauvres en cornes et d'une haute resistance mecanique |
FR2446865A1 (fr) * | 1979-01-16 | 1980-08-14 | Pechiney Aluminium | Alliage d'aluminium type a-gs a resistance mecanique et tenacite elevees |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1995014113A1 (fr) * | 1993-11-17 | 1995-05-26 | Pechiney Rhenalu | Alliage de type aluminium-silicon-magnesium a ductilite et emboutissabilite ameliorees et procede d'obtention |
FR2713664A1 (fr) * | 1993-11-17 | 1995-06-16 | Pechiney Rhenalu | Alliage type Al-Si-Mg à ductilité et emboutissabilité améliorées et procédé d'obtention. |
WO1995031580A1 (en) * | 1994-05-11 | 1995-11-23 | Aluminum Company Of America | Corrosion resistant aluminum alloy rolled sheet |
EP0714993A1 (de) * | 1994-11-29 | 1996-06-05 | Alusuisse-Lonza Services AG | Tiefziehbare und schweissbare Aluminiumlegierung vom Typ ALMgSi |
CH688379A5 (de) * | 1994-11-29 | 1997-08-29 | Alusuisse Lonza Services Ag | Tiefziehbare und schweissbare Aluminiumlegierung vom Typ AlMgSi |
EP0811700A1 (de) * | 1996-06-04 | 1997-12-10 | Alusuisse Technology & Management AG | Tiefziehbare und schweissbare Aluminiumlegierung vom Typ AlMgSi |
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 |
WO2013030469A1 (fr) | 2011-09-02 | 2013-03-07 | Constellium France | Tôle plaquée pour carrosserie automobile |
Also Published As
Publication number | Publication date |
---|---|
EP0259232B1 (de) | 1991-06-26 |
DE3771017D1 (de) | 1991-08-01 |
FR2601040A1 (fr) | 1988-01-08 |
FR2601040B1 (fr) | 1988-09-02 |
GR3002191T3 (en) | 1992-12-30 |
ES2022918B3 (es) | 1991-12-16 |
US4814022A (en) | 1989-03-21 |
CA1340260C (fr) | 1998-12-15 |
GR3026104T3 (en) | 1998-05-29 |
EP0259232B2 (de) | 1998-01-28 |
ES2022918T5 (es) | 1998-03-16 |
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