CH688379A5 - Thermaformed and weldable aluminum alloy of the AlMgSi type - Google Patents
Thermaformed and weldable aluminum alloy of the AlMgSi type Download PDFInfo
- Publication number
- CH688379A5 CH688379A5 CH03600/94A CH360094A CH688379A5 CH 688379 A5 CH688379 A5 CH 688379A5 CH 03600/94 A CH03600/94 A CH 03600/94A CH 360094 A CH360094 A CH 360094A CH 688379 A5 CH688379 A5 CH 688379A5
- Authority
- CH
- Switzerland
- Prior art keywords
- sep
- alloy
- max
- alloy according
- cel
- Prior art date
Links
Classifications
-
- 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
- C22F1/043—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 silicon 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
- C22C21/02—Alloys based on aluminium with silicon 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
-
- 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
Landscapes
- 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)
- Shaping Metal By Deep-Drawing, Or The Like (AREA)
- Continuous Casting (AREA)
Description
Die Erfindung betrifft eine tiefziehbare und schweissbare Aluminiumlegierung vom Typ AlMgSi in der Form von Bändern oder Blechen sowie ein Verfahren zu ihrer Herstellung.
In der Praxis bekannte Legierungen, die zur Herstellung von Karosserieblechen für die Automobilindustrie eingesetzt werden, sind in DE-A 2 714 395, US-A 4 082 578 und EP-B 0 259 232 beschrieben. Jede dieser Legierungen hat ihre Vorzüge, indem gewisse mechanische Eigenschaften wie beispielsweise die Festigkeit optimiert sind, allerdings zumeist unter Inkaufnahme einer Verschlechterung anderer Eigenschaften wie beispielsweise des Umformvermögens.
Angesichts dieser Gegebenheiten hat sich der Erfinder die Aufgabe gestellt, eine Legierung der eingangs erwähnten Art zu schaffen, die bei guter Festigkeit ein gegenüber Legierungen nach dem Stand der Technik verbessertes Umformverhalten mit möglichst geringer Rückfederung nach dem Tiefziehen zeigt.
Zur erfindungsgemässen Lösung der Aufgabe führt, dass die Gehalte (Gew.-%) der Legierungselemente Mg und Si durch das Trapez A, B, C, D, E mit den Koordinaten
<tb><TABLE> Columns=3
<tb>Head Col 2 AL=L: Si
<tb>Head Col 1: Mg
<tb><SEP>A<SEP>0,50<SEP>0,35
<tb><SEP>B<SEP>0,50<SEP>0,60
<tb><SEP>C<CEL AL=L>0,95<SEP>0,60
<tb><SEP>D<SEP>0,95<SEP>0,40
<tb><SEP>E<SEP>0,80<SEP>0,35
<tb></TABLE>
begrenzt sind und die Legierung zusätzlich
<tb><TABLE> Columns=2
<tb><SEP>Cu<SEP>0,05-0,4
<tb><SEP>Mn<SEP>max. 0,15
<tb><SEP>Fe<SEP>max. 0,25
<tb></TABLE>
sowie weitere Legierungselemente einzeln max. 0,05, insgesamt max. 0,15 und Aluminium als Rest enthält.
Alle für die Legierungselemente verwendeten Gehaltsangaben beziehen sich auf Gewichtsprozente.
Spezielle und weiterbildende Ausführungsarten der erfindungsgemässen Legierung sind Gegenstand von abhängigen Patentansprüchen.
Die erfindungsgemässe Legierungszusammensetzung ermöglicht die Herstellung von tiefgezogenen Karosserieteilen mit optimalen Eigenschaften bezüglich mechanischer Festigkeit und Umformverhalten.
Bei einer bevorzugten Legierungszusammensetzung sind die Gehalte (Gew.-%) der Legierungselemente Mg und Si durch die Eckpunkte A min B min C min D min mit den Koordinaten
<tb><TABLE> Columns=3
<tb>Head Col 2 AL=L: Si
<tb>Head Col 1: Mg
<tb><SEP>A min <SEP>0,55<SEP>0,35
<tb><SEP>B min <SEP>0,55<SEP>0,45
<tb><CEL AL=L>C min <SEP>0,7<SEP>0,45
<tb><SEP>D min <SEP>0,7<SEP>0,35
<tb></TABLE>
begrenzt.
Der Kupfergehalt der erfindungsgemässen Legierung liegt bevorzugt zwischen 0,2 und 0,4 Gew.-%.
Durch einen Zusatz von 0,05 bis 0,4 Gew.-%, insbesondere 0,1 bis 0,3 Gew.-% Zink kann eine weitere Festigkeitssteigerung verbunden mit einer leichten Verbesserung des Umformvermögens erreicht werden.
Ein zusätzlicher Gehalt an Vanadium von 0,05 bis 0,2 Gew.-% führt zu einer weiteren Verbesserung des Umformverhaltens.
Die mittlere Korngrösse im Blech sollte 80 mu m nicht übersteigen und liegt bevorzugt unter 60 mu m.
Die erfindungsgemässe Legierung wird auf übliche Weise durch Strang- oder Bandgiessen, Warm- und Kaltwalzen zu einem Blech oder Band verarbeitet. Zur Erzielung der vorstehend beschriebenen optimalen Eigenschaften der Legierung bezüglich Festigkeit und Umformverhalten hat sich als besonders vorteilhaft herausgestellt, wenn die Lösungsglühung in einem Banddurchlaufofen in einem Temperaturbereich von 520 DEG C bis 580 DEG C, jedoch höchstens bis zur Solidustemperatur der Legierung durchgeführt wird.
Die Legierung kann bei Bedarf auf Enddicke abgewalzt, lösungsgeglüht und anschliessend einem Temperaturbereich von 160 DEG C bis 220 DEG C warmausgehärtet werden. Vorteilhaft ist auch eine Umformung um maximal 25% nach der Lösungsglühung und vor der Endglühung im erwähnten Temperaturbereich.
Wenn mit der Legierung lackierte Karosserieteile hergestellt werden, kann es vorteilhaft sein, die Endglühung mit der Lackeinbrennung zu kombinieren.
Die erfindungsgemässe Legierung ist insbesondere geeignet zur Herstellung tiefgezogener Karosserieteile.
Weitere Vorteile, Merkmale und Einzelheiten der erfindungsgemässen Legierung ergeben sich aus der nachfolgenden Beschreibung eines bevorzugten Ausführungsbeispiels sowie anhand der Zeichnung; diese zeigt in
Fig. 1 ein Diagramm mit den Gehaltsgrenzen für die Legierungselemente Mg und Si.
Beispiel
Eine Legierung der Zusammensetzung
<tb><TABLE> Columns=2
<tb><SEP>Si<SEP>0,69
<tb><SEP>Mg<SEP>0,37
<tb><SEP>Cu<SEP>0,38
<tb><SEP>Mn<CEL AL=L>0,06
<tb><SEP>Fe<SEP>0,23
<tb></TABLE>
mit Aluminium als Rest und eine Standardkarosserielegierung AA6016 als Vergleichslegierung wurden auf übliche Weise durch Stranggiessen, Warm- und Kaltwalzen zu einem Blech mit einer Dicke von 1,3 mm verarbeitet.
Die an Blechproben ermittelten mechanischen Eigenschaften der erfindungsgemässen Legierung und der Vergleichslegierung sind nachfolgend einander gegenübergestellt.
<tb><TABLE> Columns=7
<tb>Head Col 2 AL=L: Rm (MPa)
<tb>Head Col 1: Rp0,2 (MPa)
<tb>Head Col 2: Rp0,2/Rm
<tb>Head Col 3: A10(%)
<tb>Head Col 4: n5%
<tb>Head Col 5: r
<tb><SEP>Erfindung<SEP>212<SEP>106<SEP>0,5<SEP>26,5<SEP>0,30<CEL AL=L>0,65
<tb><CEL AL=L>AA6016<SEP>222<SEP>114<SEP>0,5<SEP>28,0<SEP>0,27<SEP>0,55
<tb></TABLE>
Die Bleche wurden in praxisnahen Versuchen tiefgezogen und weiteren, bei der Herstellung von Karosserieteilen üblichen Umformoperationen unterzogen. Die durchgeführten Praxistests haben die erwarteten Verbesserungen des Umformverhaltens bei gleichzeitig ausgezeichneten Festigkeitswerten bestätigt. Im Vergleich zur Standardkarosserielegierung AA6016 (Anticorodal-120) besitzt die erfindungsgemässe Le gierung insbesondere eine tiefere Streckgrenze sowie höhere n- bzw. r-Werte, d.h. eine geringere Rückfederung und verbesserte Streckzieh- und Tiefzieheigenschaften.
The invention relates to a deep-drawable and weldable aluminum alloy of the AlMgSi type in the form of strips or sheets, and to a method for the production thereof.
Alloys known in practice which are used for the production of body panels for the automotive industry are described in DE-A 2 714 395, US-A 4 082 578 and EP-B 0 259 232. Each of these alloys has its advantages in that certain mechanical properties such as, for example, the strength are optimized, but usually with the acceptance of a deterioration in other properties such as, for example, the formability.
In view of these circumstances, the inventor has set himself the task of creating an alloy of the type mentioned at the outset, which, with good strength, exhibits improved forming behavior compared to alloys according to the prior art, with the least possible springback after deep drawing.
In order to achieve the object according to the invention, the contents (% by weight) of the alloy elements Mg and Si through the trapezoid A, B, C, D, E with the coordinates
<tb> <TABLE> Columns = 3
<tb> Head Col 2 AL = L: Si
<tb> Head Col 1: Mg
<tb> <SEP> A <SEP> 0.50 <SEP> 0.35
<tb> <SEP> B <SEP> 0.50 <SEP> 0.60
<tb> <SEP> C <CEL AL = L> 0.95 <SEP> 0.60
<tb> <SEP> D <SEP> 0.95 <SEP> 0.40
<tb> <SEP> E <SEP> 0.80 <SEP> 0.35
<tb> </TABLE>
are limited and the alloy in addition
<tb> <TABLE> Columns = 2
<tb> <SEP> Cu <SEP> 0.05-0.4
<tb> <SEP> Mn <SEP> max. 0.15
<tb> <SEP> Fe <SEP> max. 0.25
<tb> </TABLE>
as well as further alloy elements individually max. 0.05, total max. 0.15 and aluminum as the rest.
All content information used for the alloying elements refer to percentages by weight.
Special and further developing embodiments of the alloy according to the invention are the subject of dependent patent claims.
The alloy composition according to the invention enables the production of deep-drawn body parts with optimal properties with regard to mechanical strength and forming behavior.
In a preferred alloy composition, the contents (% by weight) of the alloy elements Mg and Si through the corner points are A min B min C min D min with the coordinates
<tb> <TABLE> Columns = 3
<tb> Head Col 2 AL = L: Si
<tb> Head Col 1: Mg
<tb> <SEP> A min <SEP> 0.55 <SEP> 0.35
<tb> <SEP> B min <SEP> 0.55 <SEP> 0.45
<tb> <CEL AL = L> C min <SEP> 0.7 <SEP> 0.45
<tb> <SEP> D min <SEP> 0.7 <SEP> 0.35
<tb> </TABLE>
limited.
The copper content of the alloy according to the invention is preferably between 0.2 and 0.4% by weight.
By adding 0.05 to 0.4% by weight, in particular 0.1 to 0.3% by weight, zinc, a further increase in strength combined with a slight improvement in the formability can be achieved.
An additional vanadium content of 0.05 to 0.2% by weight leads to a further improvement in the forming behavior.
The average grain size in the sheet should not exceed 80 μm and is preferably less than 60 μm.
The alloy according to the invention is processed in the usual way by continuous casting or strip casting, hot and cold rolling to form a sheet or strip. To achieve the optimal properties of the alloy described above with regard to strength and forming behavior, it has proven to be particularly advantageous if the solution annealing is carried out in a continuous belt furnace in a temperature range from 520 ° C. to 580 ° C., but at most up to the solidus temperature of the alloy.
If required, the alloy can be rolled to its final thickness, solution-annealed and then heat-cured in a temperature range from 160 ° C to 220 ° C. Forming by a maximum of 25% after solution annealing and before final annealing in the temperature range mentioned is also advantageous.
If body parts painted with the alloy are produced, it can be advantageous to combine the final annealing with the paint baking.
The alloy according to the invention is particularly suitable for producing deep-drawn body parts.
Further advantages, features and details of the alloy according to the invention result from the following description of a preferred exemplary embodiment and from the drawing; this shows in
Fig. 1 is a diagram with the content limits for the alloying elements Mg and Si.
example
An alloy of the composition
<tb> <TABLE> Columns = 2
<tb> <SEP> Si <SEP> 0.69
<tb> <SEP> Mg <SEP> 0.37
<tb> <SEP> Cu <SEP> 0.38
<tb> <SEP> Mn <CEL AL = L> 0.06
<tb> <SEP> Fe <SEP> 0.23
<tb> </TABLE>
with aluminum as the remainder and a standard body alloy AA6016 as a comparison alloy were processed in the usual way by continuous casting, hot and cold rolling to a sheet with a thickness of 1.3 mm.
The mechanical properties of the alloy according to the invention and the comparative alloy determined on sheet metal samples are compared below.
<tb> <TABLE> Columns = 7
<tb> Head Col 2 AL = L: Rm (MPa)
<tb> Head Col 1: Rp0.2 (MPa)
<tb> Head Col 2: Rp0.2 / Rm
<tb> Head Col 3: A10 (%)
<tb> Head Col 4: n5%
<tb> Head Col 5: r
<tb> <SEP> Invention <SEP> 212 <SEP> 106 <SEP> 0.5 <SEP> 26.5 <SEP> 0.30 <CEL AL = L> 0.65
<tb> <CEL AL = L> AA6016 <SEP> 222 <SEP> 114 <SEP> 0.5 <SEP> 28.0 <SEP> 0.27 <SEP> 0.55
<tb> </TABLE>
The sheets were deep-drawn in practical tests and subjected to further forming operations that are common in the manufacture of body parts. The practical tests carried out have confirmed the expected improvements in forming behavior with excellent strength values. In comparison to the standard body alloy AA6016 (Anticorodal-120), the alloy according to the invention in particular has a lower yield strength and higher n or r values, i.e. a lower springback and improved stretching and deep drawing properties.
Claims (9)
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CH03600/94A CH688379A5 (en) | 1994-11-29 | 1994-11-29 | Thermaformed and weldable aluminum alloy of the AlMgSi type |
EP19950810691 EP0714993B1 (en) | 1994-11-29 | 1995-11-03 | Deep drawable and weldable AlMgSi type aluminium alloy |
DE59507951T DE59507951D1 (en) | 1994-11-29 | 1995-11-03 | Thermoformable and weldable aluminum alloy of the type ALMgSi |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CH03600/94A CH688379A5 (en) | 1994-11-29 | 1994-11-29 | Thermaformed and weldable aluminum alloy of the AlMgSi type |
Publications (1)
Publication Number | Publication Date |
---|---|
CH688379A5 true CH688379A5 (en) | 1997-08-29 |
Family
ID=4259491
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CH03600/94A CH688379A5 (en) | 1994-11-29 | 1994-11-29 | Thermaformed and weldable aluminum alloy of the AlMgSi type |
Country Status (3)
Country | Link |
---|---|
EP (1) | EP0714993B1 (en) |
CH (1) | CH688379A5 (en) |
DE (1) | DE59507951D1 (en) |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CH690916A5 (en) * | 1996-06-04 | 2001-02-28 | Alusuisse Tech & Man Ag | Thermaformed and weldable aluminum alloy of the AlMgSi type. |
AUPO084796A0 (en) * | 1996-07-04 | 1996-07-25 | Comalco Aluminium Limited | 6xxx series aluminium alloy |
AU4314697A (en) * | 1996-09-30 | 1998-04-24 | Alcan International Limited | Aluminium alloy for rolled product process |
CH693673A5 (en) * | 1999-03-03 | 2003-12-15 | Alcan Tech & Man Ag | Use of an aluminum alloy of the AlMgSi type for the production of structural components. |
DE102004022817A1 (en) * | 2004-05-08 | 2005-12-01 | Erbslöh Ag | Decorative anodizable, easily deformable, mechanically highly loadable aluminum alloy, process for its production and aluminum product made from this alloy |
Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2360684A1 (en) * | 1976-08-05 | 1978-03-03 | Aluminum Co Of America | IMPROVED ALUMINUM STRUCTURAL ELEMENTS, FOR MOTOR VEHICLES |
EP0259232A1 (en) * | 1986-07-07 | 1988-03-09 | Pechiney Rhenalu | Easily workable and weldable aluminium alloy, and process for its manufacture |
EP0300927A1 (en) * | 1987-06-23 | 1989-01-25 | Pechiney Rhenalu | Aluminium based alloy for cans and process of manufacturing |
DE3829911A1 (en) * | 1987-09-03 | 1989-03-16 | Kobe Steel Ltd | ALUMINUM PLATE WITH IMPROVED WELDING CAPABILITY, FILIFORM CORROSION STRENGTH, HEAT TREATMENTABILITY AND DEFORMABILITY AND METHOD FOR THE PRODUCTION THEREOF |
EP0375572A1 (en) * | 1988-12-21 | 1990-06-27 | Pechiney Rhenalu | Aluminium alloy for cupping, containing silicon, magnesium and copper |
JPH0441648A (en) * | 1990-06-07 | 1992-02-12 | Sumitomo Light Metal Ind Ltd | High strength aluminum alloy for forming, excellent in baking hardenability |
JPH0570908A (en) * | 1991-05-01 | 1993-03-23 | Sumitomo Light Metal Ind Ltd | Production of aluminum alloy material for forming |
EP0548007A1 (en) * | 1991-12-16 | 1993-06-23 | Alusuisse-Lonza Services Ag | Car body sheet |
JPH05279780A (en) * | 1992-03-31 | 1993-10-26 | Furukawa Alum Co Ltd | Medium-strength aluminum alloy excellent in bendability and its production |
Family Cites Families (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2713664B1 (en) * | 1993-11-17 | 1996-05-24 | Pechiney Rhenalu | Al-Si-Mg alloy with improved ductility and stampability and process for obtaining it. |
-
1994
- 1994-11-29 CH CH03600/94A patent/CH688379A5/en not_active IP Right Cessation
-
1995
- 1995-11-03 EP EP19950810691 patent/EP0714993B1/en not_active Expired - Lifetime
- 1995-11-03 DE DE59507951T patent/DE59507951D1/en not_active Expired - Lifetime
Patent Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2360684A1 (en) * | 1976-08-05 | 1978-03-03 | Aluminum Co Of America | IMPROVED ALUMINUM STRUCTURAL ELEMENTS, FOR MOTOR VEHICLES |
EP0259232A1 (en) * | 1986-07-07 | 1988-03-09 | Pechiney Rhenalu | Easily workable and weldable aluminium alloy, and process for its manufacture |
EP0300927A1 (en) * | 1987-06-23 | 1989-01-25 | Pechiney Rhenalu | Aluminium based alloy for cans and process of manufacturing |
DE3829911A1 (en) * | 1987-09-03 | 1989-03-16 | Kobe Steel Ltd | ALUMINUM PLATE WITH IMPROVED WELDING CAPABILITY, FILIFORM CORROSION STRENGTH, HEAT TREATMENTABILITY AND DEFORMABILITY AND METHOD FOR THE PRODUCTION THEREOF |
EP0375572A1 (en) * | 1988-12-21 | 1990-06-27 | Pechiney Rhenalu | Aluminium alloy for cupping, containing silicon, magnesium and copper |
JPH0441648A (en) * | 1990-06-07 | 1992-02-12 | Sumitomo Light Metal Ind Ltd | High strength aluminum alloy for forming, excellent in baking hardenability |
JPH0570908A (en) * | 1991-05-01 | 1993-03-23 | Sumitomo Light Metal Ind Ltd | Production of aluminum alloy material for forming |
EP0548007A1 (en) * | 1991-12-16 | 1993-06-23 | Alusuisse-Lonza Services Ag | Car body sheet |
JPH05279780A (en) * | 1992-03-31 | 1993-10-26 | Furukawa Alum Co Ltd | Medium-strength aluminum alloy excellent in bendability and its production |
Non-Patent Citations (3)
Title |
---|
PATENT ABSTRACTS OF JAPAN vol. 016, no. 219 (C - 0943) 22 May 1992 (1992-05-22) * |
PATENT ABSTRACTS OF JAPAN vol. 017, no. 394 (C - 1088) 23 July 1993 (1993-07-23) * |
PATENT ABSTRACTS OF JAPAN vol. 018, no. 068 (C - 1161) 4 February 1994 (1994-02-04) * |
Also Published As
Publication number | Publication date |
---|---|
EP0714993A1 (en) | 1996-06-05 |
DE59507951D1 (en) | 2000-04-13 |
EP0714993B1 (en) | 2000-03-08 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP0104139B1 (en) | Aluminium alloy | |
DE60021619T3 (en) | brazing | |
EP2770071B1 (en) | Aluminium alloy for the production of semi-finished products or components for motor vehicles, method for producing an aluminium alloy strip from this aluminium alloy and aluminium alloy strip and uses thereof | |
DE10116636C2 (en) | Process for the production of AIMn strips or sheets | |
EP3176275B2 (en) | Aluminium-silicon die casting alloy method for producing a die casting component made of the alloy, and a body component with a die casting component | |
WO2016207274A1 (en) | High-strength and easily formable almg-strip, and method for producing the same | |
DE3411760A1 (en) | METHOD FOR PRODUCING SHEET OR STRIP FROM A ROLLING BAR OF AN ALUMINUM ALLOY | |
DE112008003052T5 (en) | Product of Al-Mg-Zn wrought alloy and manufacturing method therefor | |
EP2888382A1 (en) | Intergranular corrosion-resistant aluminum alloy strip, and method for the production thereof | |
DE69531229T2 (en) | brazing | |
EP1518000A1 (en) | Al/cu/mg/ag alloy with si, semi-finished product made from such an alloy and method for production of such a semi-finished product | |
WO2014029856A1 (en) | Highly malleable and igc-resistant almg strip | |
DE112019000856T5 (en) | Process for the manufacture of aluminum alloy components | |
CH617720A5 (en) | ||
DE602004005529T2 (en) | Wrought aluminum alloy | |
CH688379A5 (en) | Thermaformed and weldable aluminum alloy of the AlMgSi type | |
WO2014033048A1 (en) | Aluminum alloy resistant to intercrystalline corrosion | |
EP0811700B1 (en) | Deep drawable and weldable AlMgSi type aluminium alloy | |
EP1748088A1 (en) | Al-Mg-Mn aluminium alloy exhibiting cold and warm formability | |
EP0132650A1 (en) | Aluminium alloy for structural shaped elements of vehicles and process for manufacturing said elements | |
EP0552479A1 (en) | Process for improving the flexibility of cuprous semi-finished products | |
CH685707A5 (en) | Body panel. | |
DE60310381T2 (en) | AL-MG ALLOY BRACKET OR TAPE FOR THE PRODUCTION OF CURVED PARTS WITH SMALL BENDING ADLER | |
DE2716799C2 (en) | Process for the production of an aluminum alloy sheet suitable for automobile components | |
EP0714994A1 (en) | Deep drawable and weldable ALMgSiCu type aluminium alloy |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PFA | Name/firm changed |
Owner name: ALUSUISSE-LONZA SERVICES AG TRANSFER- ALUSUISSE TE |
|
NV | New agent |
Ref country code: CH Representative=s name: E. BLUM & CO. PATENTANWAELTE |
|
PFA | Name/firm changed |
Owner name: ALUSUISSE TECHNOLOGY & MANAGEMENT AG Free format text: ALUSUISSE TECHNOLOGY & MANAGEMENT AG#BADISCHE BAHNHOFSTRASSE 16#NEUHAUSEN AM RHEINFALL (CH) -TRANSFER TO- ALUSUISSE TECHNOLOGY & MANAGEMENT AG#BADISCHE BAHNHOFSTRASSE 16#NEUHAUSEN AM RHEINFALL (CH) |
|
NV | New agent |
Ref country code: CH Representative=s name: LUCHS & PARTNER PATENTANWAELTE |
|
PUE | Assignment |
Owner name: NOVELIS, INC. Free format text: ALUSUISSE TECHNOLOGY & MANAGEMENT AG#BADISCHE BAHNHOFSTRASSE 16#NEUHAUSEN AM RHEINFALL (CH) -TRANSFER TO- NOVELIS, INC.#191 EVANS AVENUE#TORONTO, ONTARIO M8Z 1J5 (CA) |
|
PL | Patent ceased |