EP0902842B1 - Bauteil - Google Patents
Bauteil Download PDFInfo
- Publication number
- EP0902842B1 EP0902842B1 EP97920475A EP97920475A EP0902842B1 EP 0902842 B1 EP0902842 B1 EP 0902842B1 EP 97920475 A EP97920475 A EP 97920475A EP 97920475 A EP97920475 A EP 97920475A EP 0902842 B1 EP0902842 B1 EP 0902842B1
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- EP
- European Patent Office
- Prior art keywords
- component according
- alloy
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- weight
- alloy contains
- 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.)
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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
- C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
Definitions
- the invention relates to a component according to the preamble of claim 1.
- Crash behavior is increasingly important in vehicle construction Aspect. This applies to road traffic as well as to rail transport.
- the requirements for the finished component must also be observed.
- the construction can be, for example certain strength level, certain minimum values of Elongation, corrosion resistance or other essential Characteristic values must be specified.
- the alloy AA6005A currently used in wagon construction brings with it a number of problems in manufacturing, related to the tendency to recrystallize grainy.
- With a coarse grain structure it is difficult to comply with the prescribed bending radii, which reduces the inclination to form grain boundary openings during welding is reinforced. This leads to a high number of non-conformities at the production. If you want to avoid this, you have to be produced so that the profile cross section predominantly Has fiber structure. This is currently only with one Alloy composition possible, which leads to higher pressing forces and significantly lower press speeds leads. However, this must result in major productivity losses in Purchase.
- An alloy according to one of the features of claim 1 is in the DE-A-32 43 371 and disclosed in US-A-5 527 404. From aluminum pocket book (1983), pp. 141-143 is the course of the Hot curing at AlMgSi, known.
- the invention has for its object a material with particularly good ductility with good mechanical To provide properties of the component.
- the material is a comparable with the alloy AA6005A or have a lower strength level, but a higher one Ensure manufacturing reliability and higher productivity.
- a component with the features of claim 1 leads to the achievement of the object according to the invention.
- the alloy used is in terms of strength and stretch much less sensitive to quench than that Alloy AA6005A, and occurs even with wall thicknesses of 6 mm still a fine grain throughout. So that's it Alloy basically for use with large profiles suitable.
- the content limits for silicon and magnesium in% by weight are preferably set as follows: silicon 0.45 to 0.75, in particular 0.55 to 0.65 magnesium 0.45 to 0.65, in particular 0.50 to 0.60
- silicon 0.45 to 0.60 In particular 0.45 to 0.55 magnesium 0.40 to 0.60, especially 0.45 to 0.55
- alloy composition according to the invention for the production of components with high energy absorption capacity leads to a favorable microstructure of the component structure.
- the to improve the deformation properties The smallest possible grain size is achieved with the one according to the invention Alloy composition reached.
- the special heat treatment gives the component particularly good properties Energy absorption with good strength values.
- This first heat treatment consists in the generation of the aged or partially cured state T64, i.e. the alloy is not cured to maximum strength.
- the Aged condition can be caused by a glow in the area between 120 and 170 ° C are produced, the annealing time in the range is between 4 and 16 h.
- the desired degree of aging can be determined using a simple series of experiments become.
- the second heat treatment in particular in the automotive industry also with paint baking can be combined consists in the generation of the outdated condition, T72, which is caused by a glow between and reached 230 ° C during an annealing period of 1 to 5 hours can be.
- the components according to the invention are in the simplest case Extruded profiles. However, components are also conceivable that starting from an extruded profile as a preform, are finished by hydroforming. After a Another variant of the invention can also be a component Be a forged part.
- a preferred use of the component according to the invention is seen as a safety part in vehicle construction.
- the characteristic values of the tensile test can fluctuate depending on the precise analysis, degree of deformation, profile thickness and cooling conditions.
- the following minimum values have been established based on previous experience: Profile thickness range 2 - 4 mm 4 - 8 mm Rp0.2 Rm A5 Rp0 Rm A5 [MPa] [MPa] [%] [MPa] [MPa] [%] Basic material 230 275 10 230 270 8th Butt joint (MIG) 120 180 .. 115 165 ..
- the typical yield strength values are around 240 MPa the strength in the basic material lengthways around 290 MPa, the strains A5 by 12%. In the transverse direction are the yield strength and strength about the same height. A5 drops to 6%.
- Cross samples were determined by profile and sample shape Press seams included. In no case was a break in the immediate Proximity of the press seam determined what on the due to the high degree of deformation particularly fine grain in the Press seam area is attributable. The hardness is in the range from 94 to 105 HB.
- the characteristics of the welded joint apply to MIG machine welds. Differentiate in the specified thickness range the characteristic values when using SG-AlMg4, 5Mn-, SG-AlMg5- and SG-AlSi5 filler materials only a little. Error, such as edge misalignment, which is related to the problems with Welding can be attributed to large profiles the results stronger.
- the typical values of the processed Weld connections are 130 for Rp0.2 MPa, for Rm at 210 MPa and for A100 at 4%. These are at one test was achieved about 30 days after welding. Cold curing in the heat affected zone is after not yet completed this time. In an exam after around 90 days there will be a further increase in Rp0.2 by around 10 MPa was found, while the strength only slightly increases, and the elongation within the measurement accuracy remains constant.
- N 10 4 > 10 7 ⁇ ⁇ [MPa] [MPa] Basic material (lengthways) 110 Butt joint (MIG) 90 45 with raised seams 95 55 without night cant
- the value for the base material was on 3 mm thick sections determined. Under comparable conditions, for AA6005A generally reaches values ⁇ 100 MPa. The values of Welded joints were determined on 4 mm thick samples.
- the typical values of strength in the basic material lengthways are at 255 MPa, the strains A5 by 22%. In the transverse direction the strength drops slightly to 250 MPa. A5 falls to 12% from. Press seams are included in all tested cross samples. In no case was a break in the immediate vicinity of the Press seam determined. The hardness is in the range from 74 to 85 HB.
- the typical values of the welded joint processed are 130 MPa for Rp0.2, 210 MPa for Rm and A100 at 10%. Such a high elongation is exceptional. This has a very favorable effect in the event of a crash. Also be here even higher after about 90 days of storage at room temperature Rp0.2 values reached.
- Position 1 is entirely in the weld metal, position 5 in the unaffected basic material.
- the behavior in the event of a crash essentially depends on the material properties, shape and dimension of the crash element used.
- a first requirement for the suitability of a material in a certain shape and dimension is folding without premature breakage.
- Sections of pipes or hollow sections of rectangular cross-section that are compressed are used to test the crash behavior.
- Alloys A, B and C were compared in a first series of experiments, and alloys B, D and E in a second series of experiments with the compositions below.
- Si Fe Cu Mn Mg Cr Zn V Ti A 0.45 0.21 0.02 0.02 0.43 - 0.03 - 0.02 B 0.54 0.21 - 0.08 0.59 - - - 0.01 C.
- D 0.52 0.21 - 0.08 0.57 - - 0.09 0.01 E 0.51 0.21 0.11 0.06 0.49 - - 0.10 0.01
- Alloys D and E have the highest values of the absorbed Energy related to the mass of the crash element.
- the alloy recrystallizes fine-grained when pressed, with a remnant of a deformation structure in the grains remains. This is the main foundation for the below many aspects better properties compared to the alloy AA6005A.
- the fine-grained recrystallization requires a sufficient degree of deformation in relation to time.
- the alloy according to the invention is easy to weld. At Butt joints from profile sections, from large profiles worked out and welded with SG-AlMg4.5Mn filler material are never significant for wall thicknesses up to 6 mm Grain boundary openings have been observed.
- the alloy according to the invention is well suited for the Use in vehicle construction.
- the for the basic material and the Welded connection required characteristic values of the tensile test will be reached safely.
- the alloy is for small and for large profiles can be used in the same way. It is for Crash elements and for components that are formed by hydroforming are produced, equally suitable.
- the production security is due to the lower quench sensitivity and fine-grained recrystallization the alloy according to the invention much better than for the alloy AA6005A.
- the pressing speed can be compared to AA6005A in general be increased by more than 50%.
- the alloy according to the invention has proven to be one Alloy with a good combination of properties of strength, Elongation, weldability and production security proven.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Body Structure For Vehicles (AREA)
- Glass Compositions (AREA)
- Transition And Organic Metals Composition Catalysts For Addition Polymerization (AREA)
- Superconductors And Manufacturing Methods Therefor (AREA)
- Conductive Materials (AREA)
- Extrusion Of Metal (AREA)
- Laminated Bodies (AREA)
Description
Silizium | 0.45 bis 0.75, insbesondere 0.55 bis 0.65 |
Magnesium | 0.45 bis 0.65, insbesondere 0.50 bis 0.60 |
Silizium | 0.45 bis 0.60, insbesondere 0.45 bis 0.55 |
Magnesium | 0.40 bis 0.60, insbesondere 0.45 bis 0.55 |
Eisen | 0.18 bis 0.25 | |
Kupfer | 0.08 bis 0.16 | |
Mangan | 0.05 bis 0.10 | |
Vanadium | 0.06 bis 0.15 | |
Chrom | max. | 0.08, vorzugsweise max. 0.01 |
Titan | max. | 0.05 |
Profildickenbereich | 2 - 4 mm | 4 - 8 mm | ||||
Rp0.2 | Rm | A5 | Rp0 Rm | A5 | ||
[MPa] | [MPa] | [%] | [MPa] | [MPa] | [%] | |
Grundmaterial | 230 | 275 | 10 | 230 | 270 | 8 |
Stumpfstoss (MIG) | 120 | 180 | .. | 115 | 165 | .. |
N = | 104 | > 107 | |
Δδ | Δδ | ||
[MPa] | [MPa] | ||
Grundmaterial (längs) | 110 | ||
Stumpfstoss (MIG) | 90 | 45 | mit Nahtüberhöhung |
95 | 55 | ohne Nachtüberhöhung |
Profildickenbereich | 2 - 4 mm | ||
Rp0.2 | Rm | A5 | |
[MPa] | [MPa] | [%] | |
Grundmaterial | 140 - 180 | >220 | >18 |
Stumpfstoss (MIG) | >120 | >180 | >5(A100) |
SG-AlMg5-Zusatzwerkstoff | |||||
Position | Rp0.2 | Rm | Ag | A5 | |
mm | MPa | MPa | % | % | |
1 | 0 | 108 | 214 | 17.2 | 20.9 |
2 | 9 | 117 | 221 | 21.3 | 27.7 |
3 | 15 | 118 | 181 | 15.5 | 22.7 |
4 | 27 | 136 | 210 | 16.4 | 21.3 |
5 | 84 | 159 | 245 | 17.4 | 19.5 |
SG-AlSi5-Zusatzwerkstoff | |||||
Position | Rp0.2 | Rm | Ag | A5 | |
mm | MPa | MPa | % | % | |
1 | 0 | 106 | 205 | 14.7 | 16.2 |
2 | 9 | 111 | 195 | 20.7 | 25.7 |
3 | 15 | 140 | 207 | 17.0 | 22.1 |
4 | 27 | 154 | 238 | 19.6 | 21.9 |
5 | 84 | 159 | 240 | 17.3 | 18.6 |
Ermüdung | N = | 104 | > 107 | |
Δδ | Δδ | |||
[MPa] | [MPa] | |||
Grundmaterial (längs) | 95 | |||
Stumpfstoss (MIG) | 85 | 45 | mit Nahtüberhöhung | |
95 | 50 | ohne Nachtüberhöhung |
Zugversuch | Grundmaterial | 160°C 10 h | längs | |
n = 6 | Rp0.2 | Rm | Ag | A5 |
Mittelwert | 241 | 291 | 10.8 | 12.9 |
Standardabweichung | 1.4 | 2.1 | 0.3 | 0.5 |
Minimum | 239 | 288 | 10.4 | 12.3 |
Zugversuch | Grundmaterial | 140°C 8 h | längs | |
n = 6 | Rp0.2 | Rm | Ag | A5 |
Mittelwert | 165 | 255 | 18.6 | 23.3 |
Standardabweichung | 0.5 | 0.3 | 0.4 | 0.4 |
Minimum | 164 | 255 | 17.9 | 22.9 |
Si | Fe | Cu | Mn | Mg | Cr | Zn | V | Ti | |
A | 0.45 | 0.21 | 0.02 | 0.02 | 0.43 | -- | 0.03 | -- | 0.02 |
B | 0.54 | 0.21 | -- | 0.08 | 0.59 | -- | -- | -- | 0.01 |
C | 0.62 | 0.26 | 0.16 | 0.07 | 0.56 | -- | -- | 0.10 | 0.01 |
D | 0.52 | 0.21 | -- | 0.08 | 0.57 | -- | -- | 0.09 | 0.01 |
E | 0.51 | 0.21 | 0.11 | 0.06 | 0.49 | -- | -- | 0.10 | 0.01 |
Crash - Test an Rohrelementen | |||||
Leg. | Zustand | Durchm. | Dicke | Art der | Absorbierte |
Faltung | Energie/Masse | ||||
[mm] | [mm] | [kJ/kg] | |||
A | T4 | 92 | 1.5 | as | 14.4 |
B | T4 | 92 | 1.5 | as | 17.8 |
C | T4 | 92 | 1.5 | as | 22.1 |
C | T64 | 92 | 1.5 | as | 25 |
C | T6 | 92 | 1.5 | as | 25.7 |
A | T4 | 70 | 5 | rs | 52 |
B | T4 | 70 | 5 | rs | 47 |
C | T4 | 70 | 5 | rs | 58 |
Crash - Test an rechteckförmigen Hohlprofilelementen | |||
Leg. | Kühlung an der Presse | Absorbierte Energie/Masse [kJ/kg] | |
T72 | T6 | ||
B | Gebläse | 14.6 | 17.6 |
D | Gebläse | 19.0 | 18.8 |
E | Gebläse | 20.9 | 20.0 |
B | Wassersprühung | 19.1 | 16.8 |
D | Wassersprühung | 19.8 | 18.2 |
E | Wassersprühung | 21.6 | 18.2 |
Claims (15)
- Bauteil aus einer Legierung vom Typ AlMgSi, mit hohem Aufnahmevermögen für kinetische Energie durch plastische Verformung,
dadurch gekennzeichnet, dass
die Legierung in Gew.-%Silizium 0.40 bis 0.80 Magnesium 0.40 bis 0.70 Eisen max. 0.30 Kupfer max. 0.20 Mangan max. 0.15 Vanadium 0.05 bis 0.20 Chrom max. 0.10 Titan max. 0.10 Zink max. 0.10 - Bauteil nach Anspruch 1, dadurch gekennzeichnet, dass die Legierung in Gew.-%Silizium 0.45 bis 0.75, vorzugsweise 0.55 bis 0.65, undMagnesium 0.45 bis 0.65, vorzugsweise 0.50 bis 0.60
- Bauteil nach Anspruch 1, dadurch gekennzeichnet, dass die Legierung in Gew.-%Silizium 0.40 bis 0.60, vorzugsweise 0.45 bis 0.55, undMagnesium 0.40 bis 0.60, vorzugsweise 0.45 bis 0.55
- Bauteil nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Legierung 0.18 bis 0.25 Gew.-% Eisen enthält.
- Bauteil nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Legierung 0.12 bis 0.16 Gew.-% Kupfer enthält.
- Bauteil nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Legierung 0.05 bis 0.10 Gew.-% Mangan enthält.
- Bauteil nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Legierung 0.06 bis 0.15 Gew.-% Vanadium enthält.
- Bauteil nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Legierung max. 0.08, vorzugsweise max. 0.01 Gew.-% Chrom enthält.
- Bauteil nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Legierung max. 0.05 Gew.-% Titan enthält.
- Bauteil nach einem der Ansprüche 1 bis 9, dadurch gekennzeichnet, dass die Legierung nach einer Wärmebehandlung während 4 bis 16 h bei 120 bis 170°C im teilausgehärteten Zustand T64 vorliegt.
- Bauteil nach einem der Ansprüche 1 bis 9, dadurch gekennzeichnet, dass die Legierung nach einer Wärmebehandlung während 1 bis 5h bei 190 bis 230°C im überalterten Zustand T72 vorliegt.
- Bauteil nach einem der Ansprüche 1 bis 11, dadurch gekennzeichnet, dass es als Profil durch Strangpressen hergestellt ist.
- Bauteil nach einem der Ansprüche 1 bis 11, dadurch gekennzeichnet, dass es durch Innenhochdruckumformen aus einem stranggepressten Profil hergestellt ist.
- Bauteil nach einem der Ansprüche 1 bis 11, dadurch gekennzeichnet, dass es durch Schmieden hergestellt ist.
- Verwendung eines Bauteils nach einem der Ansprüche 1 bis 14 als Sicherheitsteil im Fahrzeugbau.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP97920475A EP0902842B2 (de) | 1996-05-22 | 1997-05-16 | Verfahren zur herstellung eines bauteils |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP96810325 | 1996-05-22 | ||
EP96810325A EP0808911A1 (de) | 1996-05-22 | 1996-05-22 | Bauteil |
PCT/CH1997/000193 WO1997044501A1 (de) | 1996-05-22 | 1997-05-16 | Bauteil |
EP97920475A EP0902842B2 (de) | 1996-05-22 | 1997-05-16 | Verfahren zur herstellung eines bauteils |
Publications (3)
Publication Number | Publication Date |
---|---|
EP0902842A1 EP0902842A1 (de) | 1999-03-24 |
EP0902842B1 true EP0902842B1 (de) | 2001-09-05 |
EP0902842B2 EP0902842B2 (de) | 2007-06-06 |
Family
ID=8225612
Family Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP96810325A Withdrawn EP0808911A1 (de) | 1996-05-22 | 1996-05-22 | Bauteil |
EP97920475A Expired - Lifetime EP0902842B2 (de) | 1996-05-22 | 1997-05-16 | Verfahren zur herstellung eines bauteils |
Family Applications Before (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP96810325A Withdrawn EP0808911A1 (de) | 1996-05-22 | 1996-05-22 | Bauteil |
Country Status (8)
Country | Link |
---|---|
US (1) | US6685782B1 (de) |
EP (2) | EP0808911A1 (de) |
AT (1) | ATE205261T1 (de) |
AU (1) | AU2688197A (de) |
DE (1) | DE59704542D1 (de) |
ES (1) | ES2162285T3 (de) |
WO (1) | WO1997044501A1 (de) |
ZA (1) | ZA974318B (de) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1785499A2 (de) | 2005-11-14 | 2007-05-16 | Otto Fuchs KG | Energieabsorptionsbauteil |
EP2072628A1 (de) * | 2007-12-19 | 2009-06-24 | Aleris Aluminum Bonn GmbH | Hochfeste und kollisionssichere Aluminiumlegierung |
Families Citing this family (22)
Publication number | Priority date | Publication date | Assignee | Title |
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ATE272725T1 (de) * | 1998-02-17 | 2004-08-15 | Corus Aluminium Profiltechnik | Aluminium-legierung und verfahren zu ihrer herstellung |
GB2376337B (en) * | 1998-05-05 | 2003-01-22 | Jay Chieh Chen | A cryptographic method for electronic transactions |
CH693673A5 (de) * | 1999-03-03 | 2003-12-15 | Alcan Tech & Man Ag | Verwendung einer Aluminiumlegierung vom Typ AlMgSi zur Herstellung von Strukturbauteilen. |
EP1118686B1 (de) * | 2000-01-19 | 2003-09-17 | ALUMINIUM RHEINFELDEN GmbH | Aluminium-Gusslegierung |
US20050000609A1 (en) * | 2002-12-23 | 2005-01-06 | Butler John F. | Crash resistant aluminum alloy sheet products and method of making same |
FR2857376B1 (fr) * | 2003-07-09 | 2008-08-22 | Corus Aluminium Nv | ALLIAGE DE AlMgSi |
DE102004030021B4 (de) * | 2003-07-09 | 2009-11-26 | Aleris Aluminum Duffel Bvba | Gewalztes Produkt |
DE102007012894A1 (de) * | 2007-03-17 | 2008-04-03 | Daimler Ag | Verwendung eines Schweißzusatzwerkstoffs und Bauelement für ein Kraftfahrzeug |
CN100482828C (zh) * | 2007-05-09 | 2009-04-29 | 东北轻合金有限责任公司 | 一种高精度铝合金波导管的制造方法 |
CA2797446C (en) | 2010-04-26 | 2020-07-14 | Sapa Ab | Damage tolerant aluminium material having a layered microstructure |
EP2518173B1 (de) | 2011-04-26 | 2017-11-01 | Benteler Automobiltechnik GmbH | Verfahren zur Herstellung eines Blechstrukturbauteils sowie Blechstrukturbauteil |
ES2695698T3 (es) | 2012-04-25 | 2019-01-10 | Norsk Hydro As | Perfil extruido de aleación de aluminio Al-Mg-Si con propiedades mejoradas |
CN104046865A (zh) * | 2013-03-12 | 2014-09-17 | 亚太轻合金(南通)科技有限公司 | 一种高强度可锻造铝合金棒材及其制备方法 |
EP2993244B1 (de) | 2014-09-05 | 2020-05-27 | Constellium Valais SA (AG, Ltd) | Herstellungsverfahren eines Strangpressprofils aus 6xxx Aluminiumlegierung mit ausgezeichneter Crashverhalten |
CN104561686A (zh) * | 2014-12-31 | 2015-04-29 | 东莞市东兴铝业有限公司 | 能抵受冷热凝变的铝合金材料及其制备工艺 |
EP3064305A1 (de) | 2015-03-03 | 2016-09-07 | Constellium Valais SA (AG, Ltd) | Lichtbogen-geschweisste bauteile aus aluminiumlegierungen der 6xxx-serie, insbesondere für transportanwendungen |
FR3042140B1 (fr) | 2015-10-12 | 2017-10-20 | Constellium Neuf-Brisach | Composant de structure de caisse automobile presentant un excellent compromis entre resistance mecanique et comportement au crash |
CN105483464B (zh) * | 2015-12-17 | 2017-09-22 | 上海友升铝业有限公司 | 一种适用于汽车保险杠吸能盒的Al‑Mg‑Si系合金材料 |
US10835942B2 (en) | 2016-08-26 | 2020-11-17 | Shape Corp. | Warm forming process and apparatus for transverse bending of an extruded aluminum beam to warm form a vehicle structural component |
WO2018078527A1 (en) | 2016-10-24 | 2018-05-03 | Shape Corp. | Multi-stage aluminum alloy forming and thermal processing method for the production of vehicle components |
NO20211429A1 (en) * | 2021-11-24 | 2023-05-25 | Norsk Hydro As | A 6xxx aluminium alloy with improved properties and a process for manufacturing extruded products |
WO2023220830A1 (en) * | 2022-05-18 | 2023-11-23 | Rio Tinto Alcan International Limited | Aluminum alloy with improved strength and ductility |
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IT1154589B (it) * | 1982-11-26 | 1987-01-21 | Italia Alluminio | Leghe di alluminio per apparecchiature nucleari |
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JPS61163232A (ja) * | 1985-01-11 | 1986-07-23 | Kobe Steel Ltd | 高強度Al−Mg−Si系合金およびその製造法 |
JPS6296640A (ja) * | 1985-10-23 | 1987-05-06 | Nippon Light Metal Co Ltd | 微細再結晶粒を有するアルミニウム合金 |
JPS6296638A (ja) * | 1985-10-24 | 1987-05-06 | Nippon Light Metal Co Ltd | リ−ドフレ−ム用アルミニウム合金 |
BE906107A (fr) * | 1986-12-30 | 1987-04-16 | Alusuisse | Alliage a base d'aluminium. |
JPH0747804B2 (ja) * | 1991-03-18 | 1995-05-24 | 住友軽金属工業株式会社 | 成形性、形状凍結性及び塗装焼付硬化性に優れた異方性の少ないアルミニウム合金材の製造法 |
JPH04147935A (ja) * | 1990-10-11 | 1992-05-21 | Mitsubishi Alum Co Ltd | ろう付け性の良好な高強度Al合金 |
JPH0747806B2 (ja) * | 1991-05-20 | 1995-05-24 | 住友軽金属工業株式会社 | 高強度アルミニウム合金押出形材の製造方法 |
JPH0747808B2 (ja) * | 1993-02-18 | 1995-05-24 | スカイアルミニウム株式会社 | 成形性および焼付硬化性に優れたアルミニウム合金板の製造方法 |
JP2626958B2 (ja) * | 1993-03-16 | 1997-07-02 | スカイアルミニウム株式会社 | 成形性および焼付硬化性に優れたアルミニウム合金板の製造方法 |
DE4421744C2 (de) * | 1993-07-02 | 1996-05-23 | Fuchs Fa Otto | Verwendung einer Knetlegierung des Types AlMgSiCu zur Herstellung von hochfesten und korrosionsbeständigen Teilen |
JPH073371A (ja) * | 1994-01-26 | 1995-01-06 | Sky Alum Co Ltd | 燐酸亜鉛処理用アルミニウム合金板およびその製造方法 |
US5571347A (en) * | 1994-04-07 | 1996-11-05 | Northwest Aluminum Company | High strength MG-SI type aluminum alloy |
US5527404A (en) * | 1994-07-05 | 1996-06-18 | Aluminum Company Of America | Vehicle frame components exhibiting enhanced energy absorption, an alloy and a method for their manufacture |
JP3359428B2 (ja) * | 1994-08-05 | 2002-12-24 | スカイアルミニウム株式会社 | 成形加工用アルミニウム合金板の製造方法 |
FR2726007B1 (fr) * | 1994-10-25 | 1996-12-13 | Pechiney Rhenalu | Procede de fabrication de produits en alliage alsimgcu a resistance amelioree a la corrosion intercristalline |
ATE188259T1 (de) * | 1996-04-10 | 2000-01-15 | Alusuisse Lonza Services Ag | Bauteil |
-
1996
- 1996-05-22 EP EP96810325A patent/EP0808911A1/de not_active Withdrawn
-
1997
- 1997-05-16 DE DE59704542T patent/DE59704542D1/de not_active Expired - Lifetime
- 1997-05-16 WO PCT/CH1997/000193 patent/WO1997044501A1/de active IP Right Grant
- 1997-05-16 US US09/194,294 patent/US6685782B1/en not_active Expired - Lifetime
- 1997-05-16 AU AU26881/97A patent/AU2688197A/en not_active Abandoned
- 1997-05-16 ES ES97920475T patent/ES2162285T3/es not_active Expired - Lifetime
- 1997-05-16 AT AT97920475T patent/ATE205261T1/de not_active IP Right Cessation
- 1997-05-16 EP EP97920475A patent/EP0902842B2/de not_active Expired - Lifetime
- 1997-05-19 ZA ZA9704318A patent/ZA974318B/xx unknown
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1785499A2 (de) | 2005-11-14 | 2007-05-16 | Otto Fuchs KG | Energieabsorptionsbauteil |
EP2072628A1 (de) * | 2007-12-19 | 2009-06-24 | Aleris Aluminum Bonn GmbH | Hochfeste und kollisionssichere Aluminiumlegierung |
Also Published As
Publication number | Publication date |
---|---|
EP0902842B2 (de) | 2007-06-06 |
DE59704542D1 (de) | 2001-10-11 |
US6685782B1 (en) | 2004-02-03 |
AU2688197A (en) | 1997-12-09 |
WO1997044501A1 (de) | 1997-11-27 |
EP0808911A1 (de) | 1997-11-26 |
ZA974318B (en) | 1998-01-30 |
ES2162285T3 (es) | 2001-12-16 |
EP0902842A1 (de) | 1999-03-24 |
ATE205261T1 (de) | 2001-09-15 |
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