EP0805219B1 - Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung - Google Patents

Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung Download PDF

Info

Publication number
EP0805219B1
EP0805219B1 EP19960107023 EP96107023A EP0805219B1 EP 0805219 B1 EP0805219 B1 EP 0805219B1 EP 19960107023 EP19960107023 EP 19960107023 EP 96107023 A EP96107023 A EP 96107023A EP 0805219 B1 EP0805219 B1 EP 0805219B1
Authority
EP
European Patent Office
Prior art keywords
alloy
extruded
quenching
aluminum
extrusion
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.)
Expired - Lifetime
Application number
EP19960107023
Other languages
English (en)
French (fr)
Other versions
EP0805219A1 (de
Inventor
Allison S. Alcoa Technical Center Warren
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.)
Howmet Aerospace Inc
Original Assignee
Aluminum Company of America
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=8222749&utm_source=***_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP0805219(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Aluminum Company of America filed Critical Aluminum Company of America
Priority to DE69633002T priority Critical patent/DE69633002T2/de
Priority to EP19960107023 priority patent/EP0805219B1/de
Publication of EP0805219A1 publication Critical patent/EP0805219A1/de
Application granted granted Critical
Publication of EP0805219B1 publication Critical patent/EP0805219B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

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
    • C22F1/05—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
    • 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
    • C22F1/043—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

Definitions

  • This invention concerns a method of producing improved aluminum alloy elongate products and components by operations including extrusion; and specifically improved elongated products and components that are particularly useful in the manufacture of vehicle primary structures.
  • each subassembly being composed of several separate components that can include lineal frame members.
  • Each subassembly is manufactured by joining together several members by means of a node structure that can be a cast, extruded, or sheet component.
  • the frames and subassemblies can be assembled by adhesive bonding, welding, or mechanical fastening; or by combinations of these and other joining techniques.
  • An example of such a vehicle frame structure is available in United States Patent No. 4,618,163, entitled "Automotive Chassis" the entire contents of which are incorporated herein by reference.
  • Aluminum alloys are highly desirable for such vehicle frame constructions because they offer low density, good strength and corrosion resistance.
  • aluminum alloys can be employed to improve the vehicle frame stiffness and performance characteristics.
  • Use of aluminum provides the potential for environmental benefits and efficiencies through a lightweight aluminum vehicle frame that also demonstrates reduced fuel consumption due to the lightweighting.
  • the application of aluminum alloy components in a vehicle frame presents an opportunity to ultimately recycle the aluminum components/subassemblies when the useful life of the vehicle is spent.
  • an aluminum vehicle frame retains the perceived strength and crashworthiness typically associated with much heavier, conventional steel frame vehicle designs.
  • crashworthiness in conjunction with reducing the overall vehicle weight and/or improving vehicle performance.
  • crashworthiness reflects the ability of a vehicle to sustain some amount of collision impact without incurring unacceptable distortion of the passenger compartment or undue deceleration of the occupants.
  • the structure Upon impact, the structure should deform in a prescribed manner; the energy of deformation absorbed by the structure should balance the kinetic energy of impact; the integrity of the passenger compartment should be maintained; and the primary structure should crush in such a manner as to minimize the occupant deceleration.
  • Various standard tests can be used to evaluate the physical and mechanical properties of an aluminum alloy for use in an automotive structure or other applications.
  • tensile testing and standard formability tests can be used to provide information on strength and relative performance expectations, or a tear test can be used to examine fracture characteristics and provide a measure of the resistance to crack growth or toughness under either elastic or plastic stresses.
  • tear test can be used to examine fracture characteristics and provide a measure of the resistance to crack growth or toughness under either elastic or plastic stresses.
  • the static axial crush test provides the severe conditions necessary to examine a component's response to compressive loading.
  • a specified length of an energy absorbing component is compressively loaded at a predetermined rate creating a final deformed component height of approximately half the original free length or less.
  • Various modes of collapse can be experienced under these conditions; including: regular folding - stable collapse, irregular folding, and bending.
  • the desired response for evaluation of energy absorbing components is stable axial collapse characterized by regular folding.
  • the crushed sample is examined to determine material response to the severe deformation created during this test. It is generally desirable to demonstrate the ability to deform without cracking.
  • samples are visually examined following static axial crush testing and assigned a rating based on the appearance of the deformed samples. The results of the examination are registered on a scale of from 1 to 3.
  • a “3” indicates that the area proximate the fold shows evidence of open cracking that is often visible to the naked eye and roughening damage.
  • a “3” rated material is considered to be unacceptable.
  • a “2” indicates that the area proximate the folds or displaced side wall material of the extrusion is roughened and may be slightly cracked, but the basic integrity of the side wall is maintained.
  • a sample rated "2” is better than one rated a "3” but not as good as a sample rated "1".
  • a rating of "1" indicates that the crushed extrusion contains no cracking or roughened areas and the folds are substantially smooth; this is the preferred material response following the static axial crush test.
  • the ability of a structure or structural component to absorb energy and deform in a desired, progressive manner under compressive loading during both static and dynamic crash testing is a function of both the component design, e.g., geometry, cross-section shape, size, length, thickness, joint types included in the assembly, and the properties of the material from which the component is manufactured, i.e., yield and ultimate tensile strength at the actual loading rate, modulus of elasticity, fracture behavior, etc.
  • Various aluminum alloys are potential candidates for the manufacture of a primary body structure which includes such energy absorbing components. For example, 6XXX alloys, could be utilized in the production of extruded components for incorporation into aluminum intensive vehicles.
  • the 6XXX series alloys are a popular family of aluminum alloys, designated as such in accordance with the Aluminum Association system wherein the 6XXX series refers to heat treatable aluminum alloys containing magnesium and silicon as their major alloying additions. Strengthening in the 6XXX alloys is accomplished through precipitation of Mg2Si or its precursors. The 6XXX are widely used in either the naturally aged -T4 or artificially aged -T6 tempers. This series of alloys also commonly includes other elements such as chromium, manganese, or copper, or combinations of these and other elements for purposes of forming additional phases or modifying the strengthening phase to provide improved property combinations.
  • Alloy 6063 represents one of the most widely used 6XXX products. It provides typical yield strengths of 90 MPa [13 ksi], 145 MPa [21 ksi], and 215 MPa [31 ksi] in the naturally aged -T4 and artificially aged -T5 and -T6 tempers, respectively.
  • both the -T5 and -T6 temper designations for extrusions can refer to a product which has been press quenched and artificially aged in lieu of the strict definition of -T6 that includes a solution heat treatment and quenching operation.
  • Quenching from elevated temperature processing operations is often critical to the development of properties and performance required of the final product.
  • the objective of quenching is to retain the Mg, Si and other elements in the solid solution resulting from an elevated temperature operation such as extrusion.
  • the product In the case of extrusion, the product is often quenched as it exits the extrusion press to avoid the additional cost associated with a separate solution heat treatment and quenching operation.
  • Water quenching can be used to provide a fast cooling rate from the extrusion temperature. A fast cooling rate provides the best retention of the elements in solid solution.
  • Air cooling is commonly used for press quenching of 6063 products.
  • Air cooling reduces the distortion experienced and improves dimensional capability in hollow products.
  • 6XXX products typically exhibit some quench sensitivity or loss of strength or other properties with reduced quench rates experienced in air quenching.
  • Quench sensitivity is due to precipitation of elements from the solid solution during a slow quench. This precipitation typically occurs on grain boundaries and other heterogeneous sites in the microstructure. Precipitation during the quenching operation makes the solute unavailable for precipitation of strengthening phases during subsequent aging operations.
  • a slow quench typically results in a loss of strength, toughness, formability or corrosion resistance.
  • a slow quench can also adversely effect the fracture performance of the product by promoting low energy grain boundary fracture. Quench sensitivity with respect to yield strength is generally small in dilute alloys such as 6063.
  • U.S. Patent No. 4,525,326 teaches that the quench sensitivity with respect to strength of a 6XXX alloy (Si, Fe, Cu, Mg) can be improved by the addition of vanadium.
  • the patent discloses the addition of 0.05 to 0.2% vanadium and manganese in a concentration equal to 1/4 to 2/3 of the iron concentration to an aluminum alloy for the manufacture of extruded products. Notwithstanding such efforts to develop alloys that offer reduced quench sensitivity with respect to strength; there remains a need for alloys that provide reduced quench sensitivity with respect to static axial crush performance.
  • An alloy that could be air quenched would provide the ability to produce thin walled hollow extruded shapes meeting the dimensional capabilities desired for assembly of automotive structures and providing the characteristics desired for use in the final structure including good strength and the ability to deform in a regular way in components designed to absorb energy when compressively loaded in the event of a collision; and allow production of these components in a cost effective manner.
  • composition percentages set forth herein are by weight. Additionally, this aluminum alloy demonstrates relatively lower quench sensitive with respect to the static axial crush performance and provides good strength, formability and corrosion resistance. The alloy composition of this invention is therefore ideally suited for air quench yet capable of an increased range of shapes and improved dimensional capability.
  • the quenching process can include the application of a forced air quenching of the extruded product in addition to the steps of homogenization, reheating, extrusion, natural and/or artificial aging.
  • the alloy composition is formulated to contain 0.45 to 0.7% magnesium, preferably 0.48 to 0.64% magnesium, and about 0.35 to 0.6%, preferably 0.4 to 0.5% silicon, and 0.1 to 0.35%, preferably 0.2% vanadium, and, 0.1 - 0.4% iron, preferably 0.15 to 0.3%, more preferably 0.2%, the balance aluminum and incidental elements and impurities.
  • the alloy composition of this invention is free from the intentional addition of copper and is consistent with the Aluminum Association composition standards for acceptable levels of impurities.
  • the alloy is typically solidified into extrusion ingot by continuous casting or semi-continuous casting into a shape suitable for extrusion which is typically a cylindrical ingot billet.
  • the ingot can be machined or scalped to remove surface imperfections, if desired, or it can be extruded without machining if the surface is suitable.
  • the extrusion process produces a substantially reduced diameter but greatly increased length compared to the extrusion billet.
  • the metal is typically subjected to thermal treatments to improve workability and properties.
  • the as-cast billet can be homogenized above the Mg2Si solvus temperature to allow dissolution of existing Mg2Si particles and reduce chemical segregation resulting from the casting process. Following homogenization, ingot can be allowed to air cool. Prior to extrusion, billets are reheated to the hot working temperature and extruded by direct or indirect extrusion practices.
  • extrusion be conducted at cylinder temperatures just before extrusion which are typically 28 to 56°C (50 to 100°F) less than that of the extrusion; typically within the range of about 371°C (700°F) up to about 538°C (1000°F), preferably at a temperature of 482°C (900°F).
  • Extrusion circle size varies but the extrusion typically has a wall thickness of 1.5 mm and greater.
  • the extrusion typically has ends cropped off and can be cut to desired lengths for subsequent operations.
  • the extruded shape enters a quenching zone where it is then quenched, preferably by application of forced air cooling practices, that reduces the temperature of the extrusion to between approximately 121 to 232°C (250°F. to 450°F).
  • the extruded product is at a temperature of about 177°C (350°F) as it exits the quenching zone.
  • the cooling rate that is the change in temperature of the extruded product as it traverses the quench zone is ultimately a function of the geometry of the extruded component, the speed at which the extruded product traverses the quenching zone, and the air temperature.
  • product was provided with a forced air quench to produce a cooling rate of 2 to 3°C (3 to 6°F)/sec.
  • the extruded component can then be stretched about 1/4 to 1-1/2% to straighten it if desired.
  • the extruded product is naturally aged. Suitable properties are achieved within a natural aging period between four and thirty days.
  • the extruded component can be artificially aged to develop its strength properties.
  • This typically includes heating above 121 to 132°C (250° or 270°F), typically above 149°C (300°F), for instance from about 165 to 232°C (330° to about 450°F) for a period of time from about an hour or a little less to about 10 or 15 hours, typically about 2 or 3 hours for temperatures about 177 to 204°C (350° to 400°F).
  • the time used varies inversely with temperature (higher temperature for less time or lower temperature for longer time) and this develops so called peak or -T6 strength.
  • Extrusions representing three combinations of aluminum alloy composition and thermal processing were prepared for evaluation. Samples of each composition were extruded using water quenching and air quenching.
  • the alloys designated “A” and “B” are 6063 type compositions that do not contain copper. Samples “A” were homogenized and artificially aged using the practices recommended by the Aluminum Association for production of 6063-T6; homogenization 4 hours at 579°C (1075°F) and aging 8 hours 177°C at (350°F). All other process steps were identical to those used for production of the other example materials. Samples “B” were homogenized and artificially aged according to the process of the invention. Finally, the alloy of this invention is designated “C” and contains approximately 0.2 vanadium.
  • Table I also provides the registered composition range for 6063 aluminum alloy.
  • Composition Samples Alloy Si Fe Cu Mg V A 6063 0.48 0.24 0.02 0.47 --- A 6063 0.48 0.24 0.02 0.47 --- B 6XXX 0.51 0.2 --- 0.48 --- B 6XXX 0.51 0.2 --- 0.48 --- C New 0.51 0.2 --- 0.48 0.2 C New 0.51 0.2 --- 0.48 0.2 6063 AA range 0.2-0.6 0.35 max 0.10 max 0.45-0.9
  • Table II sets forth the data obtained from the analysis of extruded product produced using water quenching.
  • Three alloys, the commercially available 6063 (sample “A”), the 6063 type alloy (sample “B”), and the alloy of this invention (sample “C”) were used to produce extruded product using a conventional water quench process.
  • the extruded product was then aged to the -T6 temper and evaluated using the static axial crush test and standard tensile tests.
  • 7.6 cm (3 inch) sections of the extrusion were saw cut with ends parallel and subjected to axial displacement. This test rendered a crushed sample approximately 3.2 cm (1.25 inch) in height having one (1) severe fold.
  • the deformed regions of the crushed product were then subject to a visual examination and assigned a crush rating as per the rating system described previously where a rating of "1" constitutes the desired outcome and a rating of "3" indicates the presence of cracking.
  • the second column of Table II provides the results of a static axial crush test. As can be seen, all three alloys, when subject to water quenching, showed the preferred performance in the static axial crush test.
  • Tables III and IV set forth the data obtained from the analysis of extruded product samples produced using forced air quenching. All three alloys; the 6063, the 6063 type, and the alloy of this invention were extruded using a forced air quench as described above. The extruded product samples were then aged to the -T6 temper and evaluated using the static axial crush test, longitudinal tensile tests, and test methods commonly used to indicate relative levels of fracture toughness, corrosion resistance and formability. The relative fracture toughness of these materials is indicated by comparing the unit propagation energy (UPE) values determined using the Kahn tear test. The relative corrosion resistance of these materials is compared through the use of bulk solution potential measurements.
  • UEE unit propagation energy
  • the relative formability of these materials was evaluated using the Olsen dome test under dry and lubricated conditions, and the guided bend test.
  • the Olsen dome test is typically used to provide an indication of relative formability in sheet products.
  • samples of the -T6 extrusion product were evaluated in the dry and lubricated conditions which simulate plane strain and equal biaxial forming conditions.
  • a dry or lubricated punch is used to determine the dome height at which necking or failure occurs in the material under evaluation with a higher value indicating better relative formability.
  • the guided bend test was originally developed to provide evaluation of formability under conditions designed to simulate sheet forming operations.
  • the samples evaluated represent -T4 sheet product that are given a 10% prestrain to simulate deformation expected in drawing operations and are subsequently bent over mandrels of different radii.
  • strip samples were evaluated in the -T6 condition and no prestrain was used.
  • the desired outcome of this testing is the ability to bend over a smaller mandrel without cracking; data from this evaluation is typically expressed as a ratio of the limiting radius, R, over the thickness of the sample, t. In this case, a smaller R/t ratio indicates better relative formability.
  • the resultant data as shown in Table III and Table IV demonstrates that the forced air cooled aluminum alloy extrusions of 6063 and 6063 type materials demonstrated reduced levels of performance in the static axial crush test (as compared to extrusions that were subject to water quenching), while the new alloy of this invention maintained desirable performance levels and demonstrated performance results similar to those obtained on spray water quenched product.
  • the aluminum alloy of this invention exhibits improved toughness as indicated by the unit propagation energy, UPE, values measured by the Kahn tear test with no adverse effect on strength. Typically in aluminum alloys, as toughness increases it does so at the cost of strength. Bulk solution potential measurements on these alloys are similar indicating that bulk corrosion performance can be expected to be comparable. Comparison of the results of the formability indicator tests illustrates that the tested extrusion of the alloy of the instant invention demonstrated desired increases in the measured results from both the dry and lubricated Olsen heights and a desired decrease in the guided bend radius achieved.

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)
  • Extrusion Of Metal (AREA)

Claims (15)

  1. Verfahren zum Herstellen eines verbesserten, gestreckten Aluminiumlegierungsproduktes, umfassend:
    Bereitstellen einer Legierung, aufweisend: 0,45 bis 0,7% Magnesium, 0,35 bis 0,6% Silicium, 0,1 bis 0,35% Vanadium und 0,1 bis 0,4% Eisen, Rest Aluminium und zufällig auftretende Elemente und Verunreinigungen;
    Extrudieren eines Körpers der Legierung; und
    Härten des Körpers der Legierung.
  2. Verfahren nach Anspruch 1, bei welchem der Körper der Legierung luftgehärtet oder wassergehärtet ist.
  3. Verfahren nach Anspruch 1, bei welchem die Legierung 0,48 bis 0,64% Magnesium enthält.
  4. Verfahren nach Anspruch 1, bei welchem die Legierung 0,4 bis 0,5% Silicium enthält.
  5. Verfahren nach Anspruch 1, bei welchem die Legierung 0,2% Vanadium enthält.
  6. Verfahren nach Anspruch 1, bei welchem die Legierung enthält: 0,48 bis 0,64% Magnesium, 0,4 bis 0,5% Silicium, 0,2% Vanadium und 0,2% Eisen enthält.
  7. Verfahren nach Anspruch 1, bei welchem das Strangpressen mit Zylindertemperaturen von 371° bis 538°C (700° bis 1.000°F) ausgeführt wird.
  8. Verfahren nach Anspruch 1, bei welchem das Strangpressen mit Zylindertemperaturen von 454° bis 510°C (850° bis 950°F) ausgeführt wird.
  9. Verfahren nach Anspruch 1, bei welchem das Härten die Temperatur des stranggepressten Produktes von 121° bis 232°C (250° bis 450°F) herabsetzt.
  10. Verfahren nach Anspruch 1, bei welchem das Härten die Temperatur des stranggepressten Produktes bis 177°C (350°F) oder weniger herabsetzt.
  11. Verfahren nach Anspruch 1, bei welchem das stranggepresste Produkt nach dem Härten gestreckt wird.
  12. Verfahren nach Anspruch 11, bei welchem das stranggepresste Produkt um einen äquivalenten Betrag von 0,25% bis 1,50% gestreckt wird.
  13. Verfahren nach einem der Ansprüche 1 bis 12, welches Verfahren umfasst:
    Erhitzen der Legierung;
    Strangpressen der Legierung;
    Lufthärten der stranggepressten Legierung;
    künstliches Altern der stranggepressten Legierung.
  14. Verfahren nach einem der vorgenannten Ansprüche 1 bis 10, bei welchem das stranggepresste Produkt ein Rahmenlängsträger in einem Fahrzeug ist.
  15. Fahrzeugrahmen, aufweisend stranggepresste Aluminiumlegierungsteile, die zur Erzeugung eines Rahmens oder einer Unterbaugruppe verbunden sind, wobei mindestens eine Mehrzahl der stranggepressten Aluminiumteile eine nach dem Verfahren nach einem der Ansprüche 1 bis 13 hergestellte Aluminiumlegierung aufweist.
EP19960107023 1996-05-03 1996-05-03 Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung Expired - Lifetime EP0805219B1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
DE69633002T DE69633002T2 (de) 1996-05-03 1996-05-03 Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung
EP19960107023 EP0805219B1 (de) 1996-05-03 1996-05-03 Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP19960107023 EP0805219B1 (de) 1996-05-03 1996-05-03 Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung

Publications (2)

Publication Number Publication Date
EP0805219A1 EP0805219A1 (de) 1997-11-05
EP0805219B1 true EP0805219B1 (de) 2004-07-28

Family

ID=8222749

Family Applications (1)

Application Number Title Priority Date Filing Date
EP19960107023 Expired - Lifetime EP0805219B1 (de) 1996-05-03 1996-05-03 Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung

Country Status (2)

Country Link
EP (1) EP0805219B1 (de)
DE (1) DE69633002T2 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1785499A2 (de) 2005-11-14 2007-05-16 Otto Fuchs KG Energieabsorptionsbauteil

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20020014287A1 (en) * 1998-10-27 2002-02-07 Shinji Yoshihara A1-mg-si based aluminum alloy extrusion
CH693673A5 (de) * 1999-03-03 2003-12-15 Alcan Tech & Man Ag Verwendung einer Aluminiumlegierung vom Typ AlMgSi zur Herstellung von Strukturbauteilen.
EP1380661A1 (de) * 2002-07-05 2004-01-14 Alcan Technology & Management Ltd. Gegenstand aus einer AIMgSI-Legierung mit dekorativer anodischer Oxidschicht
US20050000609A1 (en) * 2002-12-23 2005-01-06 Butler John F. Crash resistant aluminum alloy sheet products and method of making same
EP1467114A1 (de) * 2003-04-09 2004-10-13 Alcan Technology & Management Ltd. Verbindungselement
DE102008008326A1 (de) 2008-02-07 2011-03-03 Audi Ag Aluminiumlegierung
CN108893661B (zh) * 2018-07-19 2020-07-28 中铝萨帕特种铝材（重庆）有限公司 一种高速动车组用宽幅薄壁6系铝合金型材及其制备方法
US20210172044A1 (en) * 2019-12-05 2021-06-10 Kaiser Aluminum Fabricated Products, Llc High Strength Press Quenchable 7xxx alloy

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3938991A (en) * 1974-07-15 1976-02-17 Swiss Aluminium Limited Refining recrystallized grain size in aluminum alloys
DE3243371A1 (de) * 1982-09-13 1984-03-15 Schweizerische Aluminium AG, 3965 Chippis Aluminiumlegierung
DE3346986A1 (de) * 1983-12-24 1985-07-18 Fleck, Andreas, 2000 Hamburg Wagenkasten
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
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

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1785499A2 (de) 2005-11-14 2007-05-16 Otto Fuchs KG Energieabsorptionsbauteil

Also Published As

Publication number Publication date
EP0805219A1 (de) 1997-11-05
DE69633002D1 (de) 2004-09-02
DE69633002T2 (de) 2005-07-21

Similar Documents

Publication Publication Date Title
US5527404A (en) Vehicle frame components exhibiting enhanced energy absorption, an alloy and a method for their manufacture
CN103608478B (zh) 高温下性能好的铝铜镁合金
CA1204654A (en) Aluminum 6xxx alloy products of high strength and toughness having stable response to high temperature artificial aging treatments and method for producing
JP5366748B2 (ja) 曲げ圧壊性と耐食性に優れたアルミニウム合金押出材
AU2006210790B2 (en) Aluminum-zinc-magnesium-scandium alloys and methods of fabricating same
US20120202086A1 (en) Aluminum alloy that is not sensitive to quenching, as well as method for the production of a semi-finished product
CN109844160B (zh) 6xxx挤压件的热机械时效
WO2004001086A1 (en) Method of producing high strength balanced al-mg-si alloy and a weldable product of that alloy
EP0851942B1 (de) Verwendung von gewalzte aluminiumlegierungen für konstruktionsteile von fahrzeuge
JP4942372B2 (ja) 電磁成形用アルミニウム合金押出材
WO2019171818A1 (ja) Ａｌ－Ｍｇ－Ｓｉ系アルミニウム合金中空押出材およびその製造方法
EP0805219B1 (de) Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung
US6544358B1 (en) A1 alloy and method
JP2011074470A (ja) 曲げ圧壊性と耐食性に優れたアルミニウム合金押出材
WO1996030554A1 (en) Improved alloy for cast components
JPH08225874A (ja) 自動車構造部材用アルミニウム合金押出材とその製造方法
JP5288671B2 (ja) プレス加工性に優れたＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金押出材
JP4587588B2 (ja) 軸圧壊特性に優れたアルミニウム合金押出材およびその製造方法
DE10231422A1 (de) Aluminium-Magnesium-Legierungserzeugnis
WO2015077880A1 (en) Aluminum alloy combining high strength and extrudability, and low quench sensitivity
JP3810855B2 (ja) 改良された細長いＡｌ合金成品を製造する方法およびその方法によって製造された成品
CH690916A5 (de) Tiefziehbare und schweissbare Aluminiumlegierung vom Typ AlMgSi.
JP3450209B2 (ja) 車両ボディ用フレーム材の製造方法
JPH07180010A (ja) エネルギー吸収部材及びその製造方法
JP4611543B2 (ja) 自動車のフレーム構造におけるエネルギー吸収部材

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): DE ES FR GB IT NL SE

17P Request for examination filed

Effective date: 19980421

17Q First examination report despatched

Effective date: 19990111

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): DE ES FR GB IT NL SE

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REF Corresponds to:

Ref document number: 69633002

Country of ref document: DE

Date of ref document: 20040902

Kind code of ref document: P

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20041028

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20041108

PLAQ Examination of admissibility of opposition: information related to despatch of communication + time limit deleted

Free format text: ORIGINAL CODE: EPIDOSDOPE2

PLAR Examination of admissibility of opposition: information related to receipt of reply deleted

Free format text: ORIGINAL CODE: EPIDOSDOPE4

PLBQ Unpublished change to opponent data

Free format text: ORIGINAL CODE: EPIDOS OPPO

PLBI Opposition filed

Free format text: ORIGINAL CODE: 0009260

ET Fr: translation filed
PLAX Notice of opposition and request to file observation + time limit sent

Free format text: ORIGINAL CODE: EPIDOSNOBS2

26 Opposition filed

Opponent name: ERBSLOEH AG

Effective date: 20050423

NLR1 Nl: opposition has been filed with the epo

Opponent name: ERBSLOEH AG

PLBB Reply of patent proprietor to notice(s) of opposition received

Free format text: ORIGINAL CODE: EPIDOSNOBS3

PLCK Communication despatched that opposition was rejected

Free format text: ORIGINAL CODE: EPIDOSNREJ1

PLBN Opposition rejected

Free format text: ORIGINAL CODE: 0009273

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: OPPOSITION REJECTED

27O Opposition rejected

Effective date: 20070812

NLR2 Nl: decision of opposition

Effective date: 20070812

PLAB Opposition data, opponent's data or that of the opponent's representative modified

Free format text: ORIGINAL CODE: 0009299OPPO

NLT1 Nl: modifications of names registered in virtue of documents presented to the patent office pursuant to art. 16 a, paragraph 1

Owner name: ALCOA INC.

REG Reference to a national code

Ref country code: FR

Ref legal event code: CD

Ref country code: FR

Ref legal event code: CA

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20110131

REG Reference to a national code

Ref country code: FR

Ref legal event code: RN

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20100531

REG Reference to a national code

Ref country code: FR

Ref legal event code: D3

PGRI Patent reinstated in contracting state [announced from national office to epo]

Ref country code: FR

Effective date: 20110509

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: NL

Payment date: 20140521

Year of fee payment: 19

Ref country code: FR

Payment date: 20140527

Year of fee payment: 19

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20150521

Year of fee payment: 20

Ref country code: GB

Payment date: 20150521

Year of fee payment: 20

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20150514

Year of fee payment: 20

REG Reference to a national code

Ref country code: NL

Ref legal event code: MM

Effective date: 20150601

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20160129

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20150601

REG Reference to a national code

Ref country code: DE

Ref legal event code: R071

Ref document number: 69633002

Country of ref document: DE

REG Reference to a national code

Ref country code: GB

Ref legal event code: PE20

Expiry date: 20160502

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20150601

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20160502