EP1785499A2 - 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
EP1785499A2
EP1785499A2 EP06123946A EP06123946A EP1785499A2 EP 1785499 A2 EP1785499 A2 EP 1785499A2 EP 06123946 A EP06123946 A EP 06123946A EP 06123946 A EP06123946 A EP 06123946A EP 1785499 A2 EP1785499 A2 EP 1785499A2
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EP
European Patent Office
Prior art keywords
max
component
weight
component according
alloy
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Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
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EP06123946A
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German (de)
English (en)
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EP1785499A3 (fr
EP1785499B1 (fr
Inventor
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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Publication of EP1785499A3 publication Critical patent/EP1785499A3/fr
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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 or EP 0 805 219 B1 described. 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.
  • a change in the alloy composition by increasing the strength-influencing elements and a corresponding adaptation of the method for producing such a component lead to components with higher static strengths.
  • 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 absorption 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.
  • an energy absorption component mentioned above in which the right angle to the surface of the component extending effective grain size is less than 100 microns, especially less than 50 microns and preferably less than 30 microns or 25 microns and in which the structure of the component at least largely unrecrystallized and the grains in the L-ST directions have an aspect ratio ( L: ST ) greater than 4: 1.
  • this energy absorption component is ensured by adjusting the alloy and by a corresponding method for producing the component, in particular of the semifinished product that perpendicular To the surface of the component extending grain size, which is referred to in the context of these statements as effective grain size, a certain size, namely does not exceed 100 microns.
  • effective grain size a certain size, namely 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 selected so that the proportion of the Fe-containing phases forming at the grain boundaries is as small as possible and these phases have the smallest possible size as a result of 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 on.
  • 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 component 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.
  • the sum of the possible recrystallization-accompanying elements scandium, hafnium, strontium, vanadium, zirconium and titanium in the sum of at most 1.0 wt .-%, in addition to the manganese contained in the alloy anyway.
  • 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 aging resistance of the semifinished product in the hot aging.
  • 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.
  • 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.
  • 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 Crash-tolerant 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 an alloy of the type 1 according to the aforementioned method is shown in FIG. 1 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. Due to their size, the particles of the precipitation phase are so small due to alloying and due to the process that they can not be recognized in the selected magnification in FIG. These fine precipitation phases are distributed in relatively high density homogeneously and finely dispersed in the structure, as can be seen in a transmission electron micrograph (FIG. 2). It can also be seen from FIG. 1 that no recognizable 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 with FIG. 1, a scanning electron micrograph of an energy absorption component with a poor compression behavior.
  • Clearly recognizable in this photograph which has the same scale as the image of Figure 1, that are arranged at the grain boundaries in a recognizable size Ausscheidungsphasen. 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 compression of such an energy absorption component cracking under Involvement of the or the elimination phases arises.
  • 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.
  • homogenization is carried out at about 500 ° C ⁇ 10 ° C for 12 hours, followed by an extrusion step as a hot working step and the extrusion by taking advantage of 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. 4 a shows a structural cube of a crash component according to the invention that is virtually constructed from three sections.
  • a crash component in the L-ST , L-LT and LT-ST planes has been sampled and correspondingly oriented polished sections have been produced. Photographs of cut-outs of these cuts have been assembled into the pattern cube depicted in FIG. 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 pattern cube of the pressing direction, the LT direction of the width of the crash component, and the ST direction correspond to the direction perpendicular to the profile surface.
  • 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 shows individual grains of a crash component in the L-ST plane in order to explain the term "effective grain size".
  • the individual grains shown isolated in Figure 4b have been stretched by an extrusion process.
  • the extent of the grains shown extending in the ST direction in the region of their respective ends, as indicated by the arrows directed against one another at the ends, represents the respective effective grain size 4b grains, this is about 10 - 25 microns.
  • the L-direction also forms that direction for the crash component, which represents the main load direction when upsetting.
  • 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 representation of the ground plane L-ST of the microstructure cube of FIG. 4c in FIG. 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.
  • 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.
  • FIG. 5 shows an image 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 has been absorbed therefrom by the wrinkling shown in FIG. The energy absorbing member has been deformed into a bellows-like structure.
  • the energy absorption component is deformed, at least in one section, into the bellows-like structure shown in FIG.
  • 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 Figure 5 shows, just in the region 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. 6 shows in a comparative representation the alloys described in the context of these embodiments (type 1, type 2 and type 3) in comparison with previously known 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 having a very narrow range of elements involved in the assembly of these alloys, which in turn is a prerequisite for having an energy absorbing component made therefrom having a crashworthy texture.

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  • 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)
  • Vibration Dampers (AREA)
  • Body Structure For Vehicles (AREA)
EP06123946.3A 2005-11-14 2006-11-13 Elément de construction pour l'absorption d'énergie Revoked EP1785499B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102005054588 2005-11-14
DE102005060297A DE102005060297A1 (de) 2005-11-14 2005-12-16 Energieabsorbtionsbauteil

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

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Cited By (7)

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CN101880805A (zh) * 2010-07-30 2010-11-10 浙江巨科铝业有限公司 汽车车身板用Al-Mg-Si系铝合金及其制造方法
CN101935784A (zh) * 2010-08-30 2011-01-05 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
EP2841611A1 (fr) 2012-04-25 2015-03-04 Norsk Hydro ASA Alliage d'aluminium al-mg-si à propriétés améliorées
CN109666826A (zh) * 2018-12-29 2019-04-23 安徽鑫发铝业有限公司 一种电源外壳铝型材
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
US10661338B2 (en) 2010-04-26 2020-05-26 Hydro Extruded Solutions Ab Damage tolerant aluminium material having a layered microstructure
US20230256491A1 (en) * 2020-10-30 2023-08-17 Arconic Technologies Llc 6xxx aluminum alloys

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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

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WO1997039156A1 (fr) 1996-04-15 1997-10-23 Alcan International Limited Alliage a base d'aluminium et extrusion d'aluminium
EP0805219B1 (fr) 1996-05-03 2004-07-28 Aluminum Company Of America Pièces pour la châssis d'un véhicule ayant un absorption d'énergie amélioré, procédé pour leur fabrication et un alliage
EP0902842B1 (fr) 1996-05-22 2001-09-05 Alusuisse Technology & Management AG Element de construction
WO1999007906A1 (fr) 1997-08-04 1999-02-18 Hoogovens Aluminium Walzprodukte Gmbh ALLIAGE Al-Mg-Zn-Si HAUTE RESISTANCE POUR STRUCTURES SOUDEES ET BRASAGE
EP0936278B1 (fr) 1998-02-17 2004-08-04 Corus Aluminium Profiltechnik Bonn GmbH Alliage d'aluminium et procédé pour sa fabrication
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Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10661338B2 (en) 2010-04-26 2020-05-26 Hydro Extruded Solutions Ab Damage tolerant aluminium material having a layered microstructure
CN101880805A (zh) * 2010-07-30 2010-11-10 浙江巨科铝业有限公司 汽车车身板用Al-Mg-Si系铝合金及其制造方法
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
CN101935784A (zh) * 2010-08-30 2011-01-05 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
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
EP2841611A1 (fr) 2012-04-25 2015-03-04 Norsk Hydro ASA Alliage d'aluminium al-mg-si à propriétés améliorées
EP2841611B1 (fr) 2012-04-25 2018-04-04 Norsk Hydro ASA Profil extrudé d'une alliage d'aluminium Al-Mg-Si à propriétés améliorées
CN109666826A (zh) * 2018-12-29 2019-04-23 安徽鑫发铝业有限公司 一种电源外壳铝型材
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
US20230256491A1 (en) * 2020-10-30 2023-08-17 Arconic Technologies Llc 6xxx aluminum alloys

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EP1785499B1 (fr) 2019-01-02

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