EP1785499B1 - Elément de construction pour l'absorption d'énergie - Google Patents

Elément de construction pour l'absorption d'énergie Download PDF

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Publication number
EP1785499B1
EP1785499B1 EP06123946.3A EP06123946A EP1785499B1 EP 1785499 B1 EP1785499 B1 EP 1785499B1 EP 06123946 A EP06123946 A EP 06123946A EP 1785499 B1 EP1785499 B1 EP 1785499B1
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Prior art keywords
weight
component
max
maximum
alloy
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German (de)
English (en)
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EP1785499A3 (fr
EP1785499A2 (fr
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Joachim Dr. Becker
Mathias Dr.-Ing. Hilpert
Gregor Dr.-Ing. Terlinde
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Otto Fuchs KG
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Otto Fuchs KG
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    • 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
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the invention relates to an energy absorption component for absorbing kinetic energy by deformation to form an at least partially bellows-like structure, made of an aluminum alloy of the type Al-Mg-Si.
  • Energy absorption components are used in vehicles, for example in motor vehicles, for absorbing kinetic energy in the event of an impact, for example by an accident, for example as a bumper support, as a frame part (eg sills) or the like. These components are typically profiled components. For optimal energy absorption in the event of an impact is required that such energy absorption components are plastically deformed as possible crack-free. An embodiment is preferred in which, in the event of an impact, such a profile is compressed in total or at least in sections as bellows. For this reason, the material from which such components are made, to have a relatively high deformability. When using such an energy absorbing component in a frame construction or as an other carrier, such as in a chassis are also placed on such a component high demands on the static strength (yield strength / tensile strength).
  • such components are employed from aluminum alloys of the 6000-series Al-Mg-Si type according to the classification of the Aluminum Association. Such alloys are for example in EP 0 902 842 B1 . EP 0 936 278 B1 . US 2001/0037844 A1 . EP 0 805 219 B1 or JP2003183757 described. Al alloys for other purposes are in JP 2001234271 A . WO 99/07906 and WO 97/39156 disclosed. Energy absorption components are usually produced by extrusion. Therefore, in addition to the abovementioned ductility and strength properties of the semi-finished products produced therewith, the alloys used should have good extrudability. To meet these requirements, the previously known alloys and the methods for producing such a crashworthy component are designed to set a fine-grained recrystallization structure in the component.
  • crash profiles for producing energy-absorbing components can be produced by extrusion, which meet the conventional requirements for plastic deformation on the one hand and the static strength on the other hand.
  • the requirements for the static strength of such components are becoming increasingly higher.
  • altering the alloy composition by increasing the typically strength affecting elements and adapting the method of manufacturing such a component will result in higher static strength components.
  • these components then no longer satisfy the requirements imposed on the plastic deformation.
  • the crash behavior of such components which consist of an alloy described in the aforementioned documents in the ranges of the proportions of the elements involved in the alloy, is different, which was initially not assumed. Therefore, whether an energy absorbing member made of any one of the prior art alloys exhibits the desired crash performance or not can be determined only after performing a compression test.
  • the ductility of the material of which an energy absorbing component is made is conventionally often considered a measure of the crash performance of such a component.
  • Aluminum alloys typically contain a certain Fe content, which is used to measure the degree of purity of the aluminum used to melt the alloy. The purer the aluminum used to make the alloy, the more expensive the aluminum. Therefore, aluminum is used for the production of energy absorbing components, which has a certain iron content for reasons of cost. It is known from the prior art that with iron contents of the aluminum alloys in question of up to 0.40% by weight, an energy absorption component produced therefrom has a ductility which satisfies the requirements. Consequently, the crash behavior of a crash element made of an alloy with relatively high Fe contents would also have to meet the requirements of a sufficient crash behavior.
  • the invention is therefore the object of an energy absorbing component of the type mentioned in such a form that this not only meets higher and / or highest strength requirements, but that also statements on its crashworthiness can be made without compelling Compression tests must be undertaken and thus also a quality control in an ongoing manufacturing process for producing such components is simplified.
  • this energy absorption component is ensured by adjusting the alloy and by a corresponding method for producing the component, in particular the semifinished that the perpendicular to the surface of the component extending grain size, which is referred to in the context of these embodiments as effective grain size, a certain size , that does not exceed 100 microns.
  • effective grain size a certain size , that does not exceed 100 microns.
  • the energy absorption component has a structure that is characterized by the presence of only one type of precipitation phases. At least 40% of the precipitate phase forming particles are partially coherent or incoherent, with usually the particles being partially coherent. Preferably, the proportion of partially or incoherent particles of the precipitation phase is more than 50%.
  • kinetic energy absorption forms closely staggered sliding surface shares as a result of a multiplicity of quasi-parallel runs.
  • the alloy composition is chosen so that the proportion of Fe-forming Phases at the grain boundaries is as low as possible and these phases have as small a size as possible due to the manufacturing process.
  • Other phases formed at the grain boundaries obviously impair the crashworthiness of an energy absorbing component less than the Fe-containing phases. Nevertheless, it is desirable to keep these phases as small as possible in terms of their size and number.
  • the alloy for producing such a component it is not desirable to reduce the Fe content to an absolute minimum. Rather, some, albeit low, Fe content is desired because the alloy employed typically has an excess of Si and it is believed that the Fe contained in the alloy will bind excess Si resulting in deleterious precipitation films at the grain boundaries.
  • the alloy used for producing such an energy absorption component contains a certain Cu content.
  • Cu copper
  • the use of copper (Cu) as an alloying ingredient promotes the formation of only one (single) precipitation phase, which is an (Al) Mg-Si-Cu phase in this intracrystalline phase.
  • Copper as an alloying constituent also contributes to increasing the static strength properties. Nevertheless, when using copper as an alloy constituent, it must be ensured that the copper content is not so great that excessively Cu phases form at the grain boundaries, in particular Fe-Cu phases. Excessive formation of these phases, especially if the phases contain not only Cu but also Fe, leads to the weakening of the grain composite and thus to a deterioration of the crash behavior. Therefore, the Cu content should be controlled.
  • the energy absorption components according to the invention have average, higher and highest static strengths.
  • Semi- static strength components have an R p 0.2 value of about 200 MPa to 240 MPa.
  • Components with higher static strengths have an R p0.2 value of about 240 to 280 MPa.
  • Crash elements that meet the highest static strengths achieve an R p0.2 value greater than 280 MPa.
  • An energy absorption member made of an aluminum alloy of the type Al-Mg-Si, which has at least one of the properties described above, has a good crash behavior, without this would necessarily be occupied by compression tests. If the desired crash behavior is once occupied by compression tests in such an energy absorption component, the production of further energy absorption components can be readily monitored on the basis of the parameters described above.
  • an aluminum alloy of the type Al-Mg-Si is used, which has the following composition: Si: 0.30-1.3% by weight, Fe: 0.08 - 0.35 wt .-%, Cu: Max. 0.5% by weight, mg: 0.35-1.0% by weight, Mn: 0.02-0.8% by weight, Zn: Max. 0.2% by weight, Cr: Max. 0.15% by weight Ti: Max. 0.1% by weight, in addition to unavoidable impurities, of which each individual element is max. 0.05 wt .-% and these elements together max. 0.15 wt .-%, and a balance aluminum.
  • an aluminum alloy with the following composition is particularly suitable: Si: 0.60-0.80 wt%, Fe: 0.08 - 0.35 wt .-%, Cu: Max. 0.50 wt.%, mg: 0.40-0.50 wt%, Mn: 0.02-0.70 wt.%, Zn: Max. 0.20% by weight, Cr: Max. 0.12 wt.%, Ti: Max. 0.08% by weight, in addition to unavoidable impurities, of which each individual element is max. 0.05 wt .-% and these elements together max. 0.15 wt .-%, and a balance aluminum.
  • an alloy with one of the abovementioned compositions is melted and produced by continuous casting into round blocks.
  • the round blocks are homogenized at a homogenization temperature of 500 ° C - 590 ° C for up to 10 hours and then at temperatures between 440 ° C and 520 ° C, in particular at 460 ° C - 490 ° C transformed.
  • the hot forming can be done by an extrusion process. Likewise, a forging is possible.
  • the hot-worked semi-finished products are solution-annealed and quenched. Quenching is carried out in water or air, with water spray quenching being preferred.
  • the semi-finished product When quenched in air, the semi-finished product obtains average static strengths with R p0.2 values of 200 MPa to 240 MPa. By quenching in water higher static strengths with R p0,2 values of 240 MPa to 280 MPa can be achieved. After quenching, the semifinished product is cured by means of thermal aging, at temperatures between 170 ° C - 220 ° C for 3 - 16 hours.
  • the abovementioned alloy is distinguished from the previously known alloys with the exception of manganese by means of narrowly limited intervals of the alloying elements involved. This is also a prerequisite for the reproducibility of the components to achieve the desired component properties.
  • the element copper in the specified proportions is used.
  • the copper component compulsorily contained in the aforementioned alloy serves, besides the purpose of producing a single precipitation phase ((Al) -Mg-Si-Cu precipitation phase) for increasing the overaging resistance of the Semi-finished product during the aging process. While in previous alloys copper has been used exclusively to increase the strength, this element is used in connection with the production of an energy absorption component using one of the two abovementioned alloys, especially the two aforementioned purposes.
  • the copper content used is so low that the grain composite is not excessively weakened by Cu-containing, in particular Fe-Cu-containing phases. In a further development, it is provided that the copper content of the alloy used is at least 0.1% by weight.
  • the Mn content of the alloy used for higher strength energy absorbing components is given as 0.02-0.70 wt%.
  • the desired properties of the energy absorption component, produced from this alloy, can be achieved in particular if higher manganese contents are used, in particular those between 0.50 and 0.70 wt.% And additionally a Cr content of 0.05% -0. 12%.
  • the content of the recrystallization-inhibiting elements is sufficiently high to prevent recrystallization and to maintain the press texture in an energy-absorbing member produced by an extrusion process.
  • alloys are suitable for producing extruded energy-absorbing components, in particular also those components with only a small wall thickness of less than 10 mm, in particular less than 5 mm or even less than 3 mm.
  • energy absorption components are preferably designed as a multi-chamber hollow profile, in particular with low wall thicknesses.
  • an aluminum alloy having the following composition: Si: 0.90-1.10% by weight, Fe: 0.08 - 0.35 wt .-%, Cu: Max. 0.50 wt.%, mg: 0.55-0.75% by weight, Mn: 0.40-0.70 wt%, Zn: Max. 0.20% by weight, Cr: Max. 0.12% by weight Ti: Max. 0.08% by weight, in addition to unavoidable impurities, of which each individual element is max. 0.05 wt .-% and these elements together max. 0.15 wt .-%, and a balance aluminum.
  • This alloy is characterized in each case by narrow limits by comparatively high Si and Mg contents.
  • This alloy is suitable for extrusion and is homogenized at 480 ° C - 540 ° C for up to 15 hours and extruded using the so-called pressing effect, whereby a strength-increasing effect is achieved.
  • this variant also contains higher Mn and Cr contents in order to prevent recrystallization.
  • alloy compositions of three Al-Mg-Si type aluminum alloys with which components have been produced wherein the alloy designated Type 1 is a comparative alloy, and the alloys of Type 2 and Type 3 alloys for producing the alloys crashworthy energy absorption components according to the invention are: Element (% by weight) TYPE 1 TYPE 2 TYPE 3 minute Max. minute Max. minute Max.
  • FIG. 1 The microstructure of a component produced using a type 1 alloy according to the above method is shown in FIG. 1 shown in a scanning electron micrograph. Due to the aforementioned alloy composition, only a single precipitation phase is present in this component, namely an (Al) -Mg-Si-Cu phase. The particles of the precipitation phase are due to their size due to alloying and process-related so small that they are in FIG. 1 can not be seen in the selected magnification. These fine precipitation phases are distributed in relatively high density homogeneously and finely dispersed in the structure as in a transmission electron microscope Recording recognizes ( FIG. 2 ). Out FIG. 1 It can also be seen that no identifiable Fe-Cu-containing phases are present on the grain boundaries. Because of this property and the above-described property of having a single precipitation phase, wherein the particles of the precipitation phase are more than 50% partially coherent, this energy absorption component has a good compression behavior and is therefore to be designated as crashworthy.
  • FIG. 3 shows in a comparison to FIG. 1 a scanning electron micrograph of an energy absorption component with a poor compression behavior.
  • precipitation phases are arranged on the grain boundaries in a recognizable size. Consequently, the precipitation phases form deposits on the grain boundaries, which already weaken the crystal composite due to the size of the precipitation phases. It can be observed that when such an energy absorption component is compressed, cracking occurs involving the precipitation phase (s).
  • the components of which are the scanning electron microscopic images of the FIG. 1 and FIG. 3 were made using the same alloy (type 1). However, the components are manufactured with different manufacturing processes. While the component of FIG. 1 after the solution annealing has been spray-quenched with water, this is in FIG. 3 Component shown cooled after solution annealing in air. It is clear from this that not only the alloy composition but also the process parameters for the production of the component are decisive for the crashworthiness of the component.
  • Energy absorbing components using the Type 2 or Type 3 alloys of the present invention are made to achieve the desired microstructural properties in accordance with a method different from the preceding methods.
  • an alloy which has 0.50-0.70% by weight of Mn and 0.05-0.10% by weight of chromium.
  • the homogenization is carried out at about 500 ° C ⁇ 10 ° C for 12 hours, followed by an extrusion step as a hot forming step and the extrusion is carried out by utilizing the pressing effect. This creates an increase in strength for the component.
  • Solution heat treatment either integrated in the pressing process or separately, quenching and thermal aging, including curing, is carried out as described for the Type 1 alloy, warm aging at a temperature of 170 ° C ⁇ 10 ° C for 12 hours has been.
  • the semi-finished product obtains average static strengths with R p0.2 values of 200 MPa to 240 MPa.
  • R p0,2 values of 240 MPa to 280 MPa can be achieved.
  • FIG. 4a shows a virtually constructed of three poles Ge Glakelnchiefel a crash component according to the invention.
  • the FIG. 4a have taken a crash component in the levels L-ST , L-LT and LT-ST samples and prepared appropriately oriented polished sections. Photographs of excerpts of these cuts are to that in FIG. 4 have been assembled together. In this way, the grain structure can be visualized in three dimensions.
  • the crash component has been manufactured by an extrusion process as described above utilizing the press effect of a type 2 alloy as described above.
  • the L direction in the microstructure cube corresponds to the pressing direction
  • the ST direction corresponds to the perpendicular to the profile surface Direction.
  • the effective grain size used in these embodiments is the size of the grains in the ST direction, particularly the grain boundaries pointing in the L direction, with which the individual grains adjoin the grains adjacent in the pressing direction ( L direction).
  • FIG. 4b to explain the term "effective grain size" individual grains of a crash component in the L-ST plane.
  • the isolated in FIG. 4b shown individual grains have been stretched in the way of an extrusion process.
  • the extent of the grains shown in the ST direction in the region of their respective ends represent the respective effective grain size, as indicated by the arrows directed against one another at the ends.
  • the L- direction also forms the direction for the crash component, which represents the main load direction when upsetting.
  • the crash component represents the main load direction when upsetting.
  • FIG. 4b Shown schematically by individual grains crash component, the forces indicated by the block arrows forces. These attack the grains at their only a small size occupying extension in the ST direction. This is responsible for the good cohesion of the structure in a compression load without causing cracks.
  • the enlarged view of the ground plane L-ST of the microstructure cube of FIG. 4a in Figure 4c illustrates the enormous elongation of the grains, so that the grains of this crash component have an aspect ratio L: ST of more than 20: 1.
  • L: ST aspect ratio
  • the above-described crash component Due to the alloy composition and the manufacturing process, the above-described crash component has the desired static strengths.
  • the described grain structure and indeed the effective grain size are responsible in addition to the alloy composition that this crash component also meets the requirements placed on the compression behavior.
  • Crash components are preferably produced which satisfy both the requirements regarding the intracrystalline precipitation phase described for Type 1 as reference alloy, the Fe control and the above-mentioned structural parameters with respect to the effective grain size described for the energy-absorbing components produced from the alloys of Type 2 and Type 3.
  • the statements made above with respect to the intracrystalline precipitation phases and the Fe control for alloy type 1 thus apply equally to the energy absorption components produced from alloy types 2 and 3.
  • the latter differ with respect to their structural parameters, as in the Figures 1 and 2 to the alloy type 1, but not with regard to the precipitation phases described for this purpose. Therefore, the relevant explanations also apply to energy absorbing components made of type 2 and 3 alloys.
  • FIG. 5 shows a picture detail of a compression test of a box-shaped energy absorption component. Shown is the energy absorption component in the region of an edge at which the adjacent side surfaces in the uncompressed state of the energy absorption component include an angle of 90 ° degrees.
  • the energy absorbing member was made with the alloy of type 2 according to the above-described process steps and then subjected to a compression test. The energy absorption component has been compressed in the compression test in its longitudinal extent (in the L direction). The energy introduced into the energy absorbing member is dissipated therefrom by the in FIG. 5 wrinkling has been absorbed. The energy absorbing member has been deformed into a bellows-like structure.
  • the energy absorption component For proper absorption of the kinetic energy induced by a collision, it is essential that the energy absorption component at least in a section in the in FIG. 5 shown bellows-like structure is deformed.
  • the term "kinetic energy absorbing" used in the context of these embodiments is to be understood as meaning the energy induced by an impact in the energy absorption component, the impact energy being used to transform the energy absorption component in the manner described.
  • Critical in such a deformation are regularly the edges of such a profile, as they are subjected to particularly high deformation stresses. As FIG. 5 shows, just in the area of the original edges of the energy absorption component Aufplatzept or cracks are not visible. Rather, the energy absorption component has just in the area of its edges in regular folds.
  • FIG. 5 A regular wrinkling, as in FIG. 5 is shown, it is desired to avoid the occurrence of cracks.
  • the wrinkling takes place transversely to the L extension of the structure of the energy absorption component, ie in the transverse direction to the longitudinal extent of the grains (cf. FIGS. 4a, 4b ).
  • Such a regular or almost regular wrinkle formation in the manner of a bellows characterizes the energy absorption components according to the invention, which at the same time satisfy medium, higher or highest strengths.
  • FIG. 6 shows in a comparative representation of the alloys described in the context of these statements (type 1, type 2 and type 3) compared to prior art alloys.
  • the prior art alloys are all characterized by relatively wide range of indications of the elements used to form the alloy. Within the specified limits, the previously known alloys or the components produced therefrom should have the same properties. This is, as studies have shown, at least with respect to the crashworthiness of energy absorption components made therefrom not the case. Rather, it has been shown that energy absorption components with a good compression behavior necessary for crash components can be achieved reproducibly with the alloys indicated in the diagram type 2 and type 3 using the aforementioned manufacturing method.
  • the alloy compositions of Type 2 and Type 3 alloys are alloys with a very narrow range the respective elements involved in the construction of these alloys, which in turn are a prerequisite for an energy absorption component produced therefrom having a crashworthy structure.

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Claims (9)

  1. Pièce d'absorption d'énergie pour absorber l'énergie cinétique par déformation en réalisant, du moins par tronçon, une structure architecturale à la manière d'un soufflet, fabriquée en alliage d'aluminium du type Al-Mg-Si, la structure métallique de la pièce étant non recristallisée à au moins 80 % de son volume, et la granulométrie effective des grains dans la zone non recristallisée, lesquels s'étendent perpendiculairement à la surface de la pièce, mesurée dans le sens ST au niveau de leurs extrémités respectives est inférieure à 100 µm et que les grains dans les sens L-ST présentent un ratio d'allongement (L:ST) de plus de 10:1, l'alliage d'aluminium présentant la composition suivante: Si : 0,30 - 1,3 % de poids, Fe : 0,08 - 0,35 % de poids, Cu : max. 0,5 % de poids, Mg : 0,35 - 1,0 % de poids, Mn : 0,02 - 0,8 % de poids, Zn : max. 0,2 % de poids, Cr : max. 0,15 % de poids, Ti : max. 0,1 % de poids,
    le total des éléments d'accompagnement inhibant la recristallisation, le titane, le scandium, le hafnium, le strontium, le zircon et/ou le vanadium, représentant au maximum 1,0 % de poids, en plus des inévitables impuretés dont chaque élément isolé représente un maximum de 0,05 % de poids et tous ces éléments ensemble, un maximum de 0,15 % de poids, et un reste d'aluminium et que le procédé pour fabriquer la pièce a été réalisé de telle sorte que la structure métallique de la pièce présente en principe une seule phase de durcissement intracristalline ordonnée avec une répartition finement dispersée, avec une proportion de plus de 40 % de particules partiellement cohérentes et/ou incohérentes et que la proportion de phases contenant du Fe existant aux joints de grains est si faible, que l'assemblage de grains n'est pas excessivement affaibli par ces particules lors de l'absorption d'énergie cinétique.
  2. Pièce selon la revendication 1, caractérisée en ce que le ratio d'allongement (L:ST) est supérieur à 20:1.
  3. Pièce selon l'une des revendications 1 ou 2, caractérisée en ce que la granulométrie effective est inférieure à 50 µm, plus particulièrement inférieure à 30 µm ou 15 µm.
  4. Pièce selon l'une des revendications 1 à 3, caractérisée en ce que la texture cristallographique des grains de la pièce présente des orientations privilégiées.
  5. Pièce selon l'une des revendications 1 à 4, caractérisée en ce que l'alliage d'aluminium présente la composition suivante : Si : 0,60 - 0,80 % de poids, Fe : 0,08 - 0,35 % de poids, Cu : max. 0,50 % de poids, Mg : 0,40 - 0,50 % de poids, Mn : 0,02 - 0,70 % de poids, Zn : max. 0,20 % de poids, Cr : max. 0,12 % de poids, Ti : max. 0,08 % de poids,
    en plus des inévitables impuretés, dont chaque élément isolé représente un maximum de 0,05 % de poids et tous ces éléments ensemble, un maximum de 0,08 % de poids, et un reste d'aluminium.
  6. Pièce selon la revendication 5, caractérisée en ce que l'alliage d'aluminium contient 0,50 à 0,70 % de poids de Mn et 0,05 à 0,10 % de poids de Cr.
  7. Pièce selon l'une des revendications 1 à 4, caractérisée en ce que l'alliage d'aluminium présente la composition suivante : Si : 0,90 - 1,10 % de poids, Fe : 0,08 - 0,35 % de poids, Cu : max. 0,50 % de poids, Mg : 0,55 - 0,75 % de poids, Mn : 0,40 - 0,70 % de poids, Zn : max. 0,20 % de poids, Cr : max. 0,12 % de poids, Ti : max. 0,08 % de poids,
    en plus des inévitables impuretés, dont chaque élément isolé représente un maximum de 0,05 % de poids et tous ces éléments ensemble, un maximum de 0,15 % de poids, et un reste d'aluminium.
  8. Pièce selon la revendication 7, caractérisée en ce que l'alliage contient au moins 0,1 % de poids de Cu et au maximum 0,25 % de poids de Cu.
  9. Pièce selon l'une des revendications 6 à 8, caractérisée en ce que la pièce d'absorption d'énergie est un profilé creux à compartiments multiples avec des épaisseurs de paroi inférieures à 5 mm, et notamment inférieures à 3 mm.
EP06123946.3A 2005-11-14 2006-11-13 Elément de construction pour l'absorption d'énergie Revoked EP1785499B1 (fr)

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DE102005054588 2005-11-14
DE102005060297A DE102005060297A1 (de) 2005-11-14 2005-12-16 Energieabsorbtionsbauteil

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EP1785499A2 EP1785499A2 (fr) 2007-05-16
EP1785499A3 EP1785499A3 (fr) 2010-11-03
EP1785499B1 true EP1785499B1 (fr) 2019-01-02

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DE102008008326A1 (de) * 2008-02-07 2011-03-03 Audi Ag Aluminiumlegierung
WO2011122958A1 (fr) 2010-03-30 2011-10-06 Norsk Hydro Asa Alliage d'aluminium stable à haute température
JP2013525608A (ja) 2010-04-26 2013-06-20 サパ アーベー 階層状の微細構造を有する損傷耐性アルミ材
CN101880805B (zh) * 2010-07-30 2012-10-17 浙江巨科铝业有限公司 汽车车身板用Al-Mg-Si系铝合金制造方法
CN101935784B (zh) * 2010-08-30 2011-11-23 佛山市鸿金源铝业制品有限公司 高速铁路接触网用铝材及其制造方法
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CN109722577A (zh) * 2019-01-16 2019-05-07 山东友升铝业有限公司 一种改善挤压型材延伸率用变形铝合金
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