EP0997547A1 - Stranggepresste Al-Mg-Si Legierung auf Aluminium Basis - Google Patents

Stranggepresste Al-Mg-Si Legierung auf Aluminium Basis Download PDF

Info

Publication number
EP0997547A1
EP0997547A1 EP99120845A EP99120845A EP0997547A1 EP 0997547 A1 EP0997547 A1 EP 0997547A1 EP 99120845 A EP99120845 A EP 99120845A EP 99120845 A EP99120845 A EP 99120845A EP 0997547 A1 EP0997547 A1 EP 0997547A1
Authority
EP
European Patent Office
Prior art keywords
aluminum alloy
based aluminum
alloy extrusion
extrusion
compressing
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.)
Withdrawn
Application number
EP99120845A
Other languages
English (en)
French (fr)
Inventor
Shinji Yoshihara
Hitoshi Kawai
Masakazu Hirano
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.)
Kobe Steel Ltd
Original Assignee
Kobe Steel Ltd
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
Priority claimed from JP10305616A external-priority patent/JP3077974B2/ja
Priority claimed from JP11056368A external-priority patent/JP3077976B1/ja
Application filed by Kobe Steel Ltd filed Critical Kobe Steel Ltd
Publication of EP0997547A1 publication Critical patent/EP0997547A1/de
Withdrawn legal-status Critical Current

Links

Images

Classifications

    • 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
    • C22C21/02—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
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions

Definitions

  • the present invention relates to an aluminum alloy extrusion, and in particular to an aluminum alloy extrusion which has the following action: when the extrusion receives compressive impact load or compressive static load along its extrusive axis direction, the extrusion absorbs the compressive impact load or compressive static load.
  • the aluminum alloy extrusion is suitably applied in particular to fabrics for cars, for example, a side member or a bumper stay.
  • an object of the present invention is to provide an Al-Mg-Si based aluminum alloy extrusion which causes compressing cracks not to be generated even when deformation in its axial direction occurs at a high speed, as seen in actual collision, and which has large absorbable energy and satisfactory energy absorption property.
  • Another object of the present invention is to provide an Al-Mg-Si based aluminum alloy extrusion suitable for fabrics of cars excellent in axial compressing property (high strength and resistance against compressing cracking).
  • the inventors made various experiments and researches to develop an Al-Mg-Si based aluminum alloy extrusion excellent in axial compressing property. As a result, the inventors have found that excellent axial compressing property can be obtained if the followings are within specific ranges: the size and the distribution of Mg 2 Si precipitation in specified directions of the (1 0 0) plane inside grains of an alloy; and the size of precipitations such as Mg 2 Si on grain boundaries.
  • the present invention has been made on basis of these findings.
  • a first aspect of the present invention is an Al-Mg-Si based aluminum alloy extrusion, wherein the average size of Mg 2 Si precipitation in the [1 0 0] and [0 1 0] directions of the (1 0 0) plane inside grains is 20 nm or more, the distribution density of the Mg 2 Si precipitation in the [0 0 1] direction of the (1 0 0) plane is 100 or more per ⁇ m 2 , and the size of precipitations on grain boundaries is 1000 nm or less.
  • This Al-Mg-Si based aluminum alloy extrusion has satisfactory axial compressing property.
  • the extrusion is suitable for use as a crushable member (i.e., a member having such an action that when it receives compressive impact load or compressive static load in its axial direction, it crushes in the axial direction to absorb the impact load or the static load).
  • a crushable member i.e., a member having such an action that when it receives compressive impact load or compressive static load in its axial direction, it crushes in the axial direction to absorb the impact load or the static load.
  • a second aspect of the present invention is an Al-Mg-Si based aluminum alloy extrusion excellent in impact energy absorption property, wherein a tensile strength obtained from a tensile test performed at a strain rate of 1000 per second is from 150 to 400 N/mm 2 (both inclusive), preferably from 200 to 370 N/mm 2 (both inclusive).
  • the Al-Mg-Si based aluminum alloy extrusion satisfying these requirements can be deformed in bellows when it is compressed and deformed at a high speed, to exhibit excellent impact energy absorption property.
  • the Mg 2 Si precipitation inside the grains precipitates in a rod form in the ⁇ 1 0 0 ⁇ direction at the time of artificial aging treatment, so as to disturb dislocation movement. This causes the strength of the extrusion to be raised. If the average size of the precipitation in the [1 0 0] and [0 1 0] directions of the (1 0 0) plane inside the grains is less than 20 nm, the precipitated grains are shorn by the dislocation at the time of the compression and deformation of the extrusion. In this case, subsequent dislocation moves very easily on the slip plane (the (1 1 1)plane), so that straight and coarse slip band texture is generated. For this reason, stress concentrates on the grain boundaries so that the grain boundaries are ruptured.
  • the average size of the precipitation is 30 nm or more. However, if the size of the precipitation is too large, the strength drops. Thus, it is desirable that the average size thereof is not over 1000 nm.
  • the distribution density of the Mg 2 Si precipitation has an influence on the strength of the extrusion.
  • the distribution density of the precipitation in the [0 0 1] direction of the (1 0 0) plane inside the grains is less than 100 per ⁇ m 2
  • the extrusion has low strength and less absorbed energy at the time of compression and deformation of the extrusion. Therefore, the distribution density is set up to 100 per ⁇ m 2 or more.
  • the distribution density is preferably 400 per ⁇ m 2 or more. If the distribution density becomes too large, compressing cracking is liable to occur.
  • the distribution density is preferably 2000 per ⁇ m 2 or more.
  • the size and the distribution density of the Mg 2 Si precipitation are measured by a measuring method that will be described later.
  • the Mg 2 Si precipitation, a simple substance Si and the like on the grain boundaries are produced in the cooling after the extruding or the solution treatment, and have an influence on the rupture form of the grain boundaries. If the size of the grain boundary precipitations is over 1000 nm, the precipitations become starting points of cracks so that the grain boundaries rupture. This makes the resistance against compressing cracking of the extrusion poor.
  • the size of the precipitations is preferably 500 nm or less.
  • its crystal texture is preferably a fiber texture.
  • the fiber texture is a hot-worked texture, as seen in extrusions, wherein grains are stretched in its extrusive direction.
  • the strain in a material when it is deformed, is induced by the movement of dislocation.
  • This dislocation disappears at a portion where the arrangement of metal crystal is irregular, such as a grain boundary. Therefore, lattice gaps accumulate in such a portion so that strains concentrate on the portion.
  • the distribution of the dislocation (that is, the distribution of the strains) is likely to be more uniform in the material as the size of its grains is smaller.
  • the Al-Mg-Si based aluminum alloy according to the first aspect of the present invention is a precipitation hardening alloy made mainly of Mg and Si.
  • a preferable composition thereof is a composition comprising Mg: 0.2-1.6%(% represents % by weight (wt) throughout the present specification) and Si: 0.2-1.8%, and optionally Cu: 1.0% or less, Mn: 0.05-0.5%, and one or more selected from the following: Ti: 0.01-0.1%, Cr: 0.01-0.2% and Zr: 0.01-0.2%.
  • the balance thereof is Al and impurities. If the amount of Fe as an impurity is 0.7% or less and each amount and the total amount of other impurities are 0.05% or less and 0.15%, respectively, the properties of the present alloy are not adversely effected.
  • Mg and Si are elements for forming the Mg 2 Si precipitation and strengthen the alloy.
  • Mg less than 0.2% or Si: less than 0.2%
  • Mg over 1.6% or Si: over 1.8%
  • the deforming ability of the extrusion drops, so that secondary working thereof becomes difficult.
  • the deformation in the extrusive axis direction easily causes compressing cracking. Therefore, the composition of the alloy is set to comprise Mg: 0.2-1.6% and Si: 0.2-1.8%, and especially preferable Mg: 0.4-0.8% and Si: 0.7-1.1%.
  • Cu has an action of improving the matrix strength of the alloy in accordance with the added amount thereof.
  • Cu may be appropriately added.
  • the added amount of cu is preferably 0.1% or more.
  • the alloy has reduced corrosion resistance, resistance against stress corrosion cracking and weldability. Furthermore, compressing cracking is liable to occur by the deformation in the extrusive axial direction. Therefore, if Cu is added, the upper limit of the amount thereof is 1.0%. In the case, the amount thereof is especially preferably from 0.15-0.7%.
  • Mn has effect of suppressing recrystallization of the alloy texture to make the texture fine.
  • Mn may be appropriately added.
  • Mn has an function for stabilizing the fiber texture of the extrusion.
  • Ti is generated as nuclei at the time of melting and casting of the alloy, and has an action of making the texture of the cast product fine.
  • Ti may be appropriately added. This effect becomes remarkable by the addition of 0.005% or more of Ti. If the added amount thereof is over 0.1%, coarse compounds are generated to cause the deterioration in resistance against compressing cracking. Thus, the added amount thereof is preferably from 0.01 to 0.1%.
  • Cr has a pinning effect in the grain boundaries of the alloy to stabilize the fiber texture of the extrusion.
  • Cr may be appropriately added. This effect can be exhibited by the addition of 0.01% or more of Cr.
  • the added amount thereof is preferably from 0.01 to 0.2%.
  • Zr also has a pinning effect in the grain boundaries of the alloy to stabilize the fiber texture of the extrusion.
  • Zr may be appropriately added. This effect can be exhibited by the addition of 0.01% or more of Zr. However, if the amount thereof is over 0.2%, the effect for stabilizing the fiber texture is not improved any more. Thus, the added amount thereof is preferably from 0.01 to 0.2%.
  • the alloy is melted and cast in the usual manner to prepare an ingot.
  • the ingot is then subjected to a homogenizing treatment.
  • the resultant is hot-extruded into a desired sectional shape, and immediately thereafter, the extruding is quenched (press-quenched).
  • the resultant is hot-extruded and then is subjected to a solution and quenching treatment.
  • the hot-extruding/press-quenching is a treatment of extruding an ingot and simultaneously using extruding-temperature to conduct a solution treatment.
  • the extruding temperature is set up to temperature for the solution treatment.
  • the extruding-temperature is set to an appropriate temperature in the manner that the fiber texture after the extruding is not recrystallized into coarse recrystallized grains.
  • the fiber texture is not recrystallized into coarse recrystallized grains after the hot-extruding or during the solution treatment.
  • the extension after the aging treatment preferably has a tensile strength of 200 N/mm 2 or more and a proof stress of 150 N/mm 2 or more to obtain high absorbable energy.
  • an aluminum alloy extrusion which is very excellent in axial compressing property and is suitable for fabrics for cars such as a side member by restricting the size of the precipitation inside the grains and the distribution density and the size of the grain boundary precipitations.
  • a strain rate of 1000 per second is selected as a tensile rate at a high-speed tensile test.
  • the tensile strength obtained in the tensile test performed under this condition is decided as an index for representing energy absorption property at the time of high-speed compression and deformation of any alloy extrusion.
  • the tensile test performed under a strain rate of 1000 per second corresponds to a strain rate of a car material deformed when a car collides at about 30-40 km/h.
  • the behavior of a car when it collides at 30-40 km/h is similar to that of the car when it collides at any speed more than 30-40 km/h.
  • the alloy extrusion has only small absorbable energy at the time of compressing and deforming the alloy extrusion at a high speed and the alloy extrusion does not satisfy strength necessary for fabrics for cars.
  • the tensile strength at a strain rate of 1000 per second is over 400 N/mm 2 , compressing cracking occurs at the time of compressing and deforming the alloy extrusion at a high speed.
  • the alloy extrusion is unsuitable for energy absorbable members.
  • the Al-Mg-Si based aluminum alloy according to the second aspect of the present invention is a precipitation hardening alloy.
  • a preferable composition thereof is a composition comprising Mg: 0.2-1.6% and Si: 0.2-1.8%, and optionally (1) Cu: 1.0% or less, (2) Ti: 0.005-0.2%, and (3) one or more selected from the following: Mn: 0.05-0.5% or less, Cr: 0.01-0.2% and Zr: 0.01-0.2%. Any one or a combination of the (1)-(3) may be contained. The balance thereof is Al and impurities.
  • An especially preferable composition is a composition comprising Mg: 0.35-1.1%, Si: 0.5-1.3%, Cu: 0.15-0.7%, Ti: 0.005-0.2%, Zr: 0.01-0.2%, and one or two of Mn: 0.05-0.5% and Cr: 0.05-0.15%. If the amount of Fe as an impurity is 0.7% or less and each amount and the total amount of other impurities are 0.05% or less and 0.15% or less, respectively, the properties of the present alloy are not adversely effected.
  • the crystal texture is a fiber texture.
  • the Zr is added in an amount more than the given amount, resistance against compressing cracking of the alloy extrusion subjected to over aging treatment is greatly improved.
  • Zr causes a less drop in press-quenching ability than Mn and Cr. Since Cr causes deterioration in the surface performance of the extrusion, it is preferable that Zr is first added and subsequently Mn and/or Cr are/is added.
  • the composition of the extrusion is set up to comprise Zr: 0.06-0.2% and further Mn: 0.05-0.5% and Cr: 0.05-0.15%.
  • the producing conditions for obtaining the extrusion according to the second aspect of the present invention is as follows:
  • an aluminum alloy extrusion which has excellent energy absorption property, when being deformed at a high speed, and is suitable for a raw material of fabrics for cars such as a side member.
  • ingots (diameter: 155 mm) of several kinds of aluminum alloys comprising Mg and Si as mainly-added elements.
  • these ingots were subjected to a homogenizing treatment at 550 °C for 8 hours.
  • the respective billets were extruded at an extruding temperature of 500 °C and an extruding speed of 5 m/min.
  • the resultant extrusions were cooled with water (average cooling rate: about 12000 °C/min.) or air (average cooling rate: about 190 °C/min.) to obtain angular pipes having a long side of 60 mm, a short side of 40 mm and a thickness of 2 mm.
  • Tables 1 and 2 show alloy compositions and treatment conditions of the respective samples.
  • Chemical Components (% by weight) No. Si Fe Cu Mn Mg Cr Zn Ti Zr 1 0.40 0.15 tr. tr. 0.70 tr. tr. 0.02 tr. 2 0.55 0.15 0.10 0.10 0.70 0.05 tr. 0.02 0.05 3 0.90 0.25 0.50 0.35 0.60 tr. tr. 0.02 0.15 4 0.90 0.25 0.50 0.35 0.60 tr. tr. 0.02 0.15 5 0.90 0.25 0.50 0.35 0.60 tr. tr.
  • Test pieces according to JIS No. 5 were taken out from these samples. These test pieces were used to measure their tensile strength ⁇ B , proof stress ⁇ 0.2 and rupture elongation ⁇ according to a metallic material tensile test defined in JIS Z 2241.
  • FIG. 2 illustrates a method of the compressing tests.
  • a load was applied to a sample 1 in its axial direction by means of a universal test machine 2. Based on the test results, a displacement-load diagram was prepared. From this diagram, absorbable energy up to a displacement of 100 mm was obtained. Cracking resistance was evaluated based on cracks generated in the compressing test. The samples in which no cracking occurred are represented by ⁇ . The samples in which cracking occurred are represented by X.
  • Test pieces were taken out from the samples and then a transmission electron microscope was used to observe the (1 0 0) plane thereof at 200,000 magnifications.
  • Respective grains of Mg 2 Si precipitation precipitated in the [1 0 0] and [0 1 0] directions only precipitated grains having a length in the [1 0 0] or [0 1 0] direction of 5 nm or more were measured about their length.
  • the same (1 0 0) plane was observed to examine the number of Mg 2 Si grains which were precipitated in the [1 0 0] direction and had a diameter of 1 nm or more. Thus, the distribution density thereof was obtained.
  • Aluminum alloy billets having the compositions shown in Table 4 and having a diameter of 155 mm were first produced by melting and casting in a usual way.
  • Chemical compositions (% by weight) No. Si Fe Cu Mn Mg Cr Zn Ti Zr 1 0.90 0.30 0.50 0.35 0.65 tr. tr. 0.02 0.13 2 0.55 0.20 0.10 0.10 0.70 0.05 tr. 0.02 0.05 3 0.40 0.15 tr. tr. 0.60 tr. tr. 0.02 tr. 4 0.40 0.15 tr. tr. 0.60 tr. tr. 0.02 tr. 5 0.59 0.23 0.20 0.15 0.51 tr. tr. 0.02 0.11 6 0.20 0.20 tr. tr. 0.65 tr. tr. 0.02 tr. 7 1.20 0.30 0.90 0.36 1.00 0.15 tr. 0.02 0.13 (tr.: trace)
  • Test pieces based on JIS No. 5 test pieces disclosed in Japanese Patent Application Laid-Open No. 10-318894 were taken out in their longitudinal direction from these samples, and then they were subjected to a tensile test at a strain rate of 1000 per second in which the measuring method disclosed in this publication was used. The results are shown in Table 6.
  • FIG. 3 shows the compressing test.
  • a load 200kgf
  • the load was measured with a load cell 4.
  • the speed of the dropping weight was about 50 km/hour.
  • displacement-load diagrams were prepared. From the displacement-load diagrams, absorbable energies were measured in the range up to a displacement of 100 mm. Samples having an absorbable energy of 2000 J or more are represented by ⁇ , and samples having an absorbable energy of less than 2000 J are represented by X. At the same time, resistance against compressing cracking of the compressing samples was judged with naked eyes. Samples in which no cracking occurred are represented by ⁇ , and samples in which cracking occurred are represented by X. The results are also shown in Table 6.
  • Samples Nos. 1-5 satisfying the requirements according to the second aspect of the present invention were deformed into the form of bellows, and had good absorbable energy and resistance against compressing cracking. They were suitable for a material of car parts such as a side member.
  • sample No. 1 was a sample subjected to an over aging treatment, and had especially high strength and absorbable energy, i.e., especially good resistance against compressing cracking.
  • samples No. 6 and No. 7 were poor in the absorbable energy and the resistance against compressing cracking, respectively, and thus were unsuitable for a raw material of car parts.

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)
  • Body Structure For Vehicles (AREA)
EP99120845A 1998-10-27 1999-10-26 Stranggepresste Al-Mg-Si Legierung auf Aluminium Basis Withdrawn EP0997547A1 (de)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP30561698 1998-10-27
JP10305616A JP3077974B2 (ja) 1998-10-27 1998-10-27 軸圧壊特性に優れるＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金押出形材
JP11056368A JP3077976B1 (ja) 1999-03-04 1999-03-04 押出軸方向の衝撃エネルギー吸収特性に優れるＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金押出形材
JP5636899 1999-03-04

Publications (1)

Publication Number Publication Date
EP0997547A1 true EP0997547A1 (de) 2000-05-03

Family

ID=26397318

Family Applications (1)

Application Number Title Priority Date Filing Date
EP99120845A Withdrawn EP0997547A1 (de) 1998-10-27 1999-10-26 Stranggepresste Al-Mg-Si Legierung auf Aluminium Basis

Country Status (2)

Country Link
US (2) US20020014287A1 (de)
EP (1) EP0997547A1 (de)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101130656B1 (ko) * 2003-11-20 2012-04-02 노벨리스 인코퍼레이티드 차체 부품
US8940406B2 (en) 2008-08-13 2015-01-27 Novelis Inc. Automobile body part
EP2841611B1 (de) 2012-04-25 2018-04-04 Norsk Hydro ASA Strangpressprofil aus einer Al-Mg-Si-aluminiumlegierung mit verbesserten eigenschaften
EP2553131B1 (de) 2010-03-30 2019-05-08 Norsk Hydro ASA Hochtemperaturstabile aluminiumlegierung
WO2019206826A1 (en) * 2018-04-24 2019-10-31 Constellium Singen Gmbh 6xxx aluminum alloy for extrusion with excellent crash performance and high yield strength and method of production thereof

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20030226935A1 (en) * 2001-11-02 2003-12-11 Garratt Matthew D. Structural members having improved resistance to fatigue crack growth
DE102005060297A1 (de) 2005-11-14 2007-05-16 Fuchs Kg Otto Energieabsorbtionsbauteil
KR101357050B1 (ko) * 2011-10-10 2014-02-04 한국생산기술연구원 다이캐스팅용 고열전도도 Ａｌ-Ｍｇ-Ｆｅ-Ｓｉ 합금
JP6022882B2 (ja) * 2012-10-05 2016-11-09 株式会社Uacj 高強度アルミニウム合金押出材及びその製造方法
CN105238961B (zh) * 2015-10-12 2017-11-07 苏州中色研达金属技术有限公司 一种6xxx系铝合金及其加工方法
CN105296811A (zh) * 2015-10-23 2016-02-03 苏州有色金属研究院有限公司 手机部件用高强6xxx系铝合金及其加工方法
CN114959374B (zh) * 2022-05-30 2023-08-29 中国科学院长春应用化学研究所 一种高可挤压性高强度铝合金及其制备方法

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0711368A (ja) * 1993-04-30 1995-01-13 Kobe Steel Ltd 曲げ性が優れたＡｌ−Ｍｇ−Ｓｉ系合金押出材
JPH0754090A (ja) * 1993-08-13 1995-02-28 Kobe Steel Ltd 曲げ加工性及び衝撃吸収性が優れたアルミニウム合金材及びその製造方法
EP0687743A1 (de) * 1994-06-16 1995-12-20 The Furukawa Electric Co., Ltd. Verstärkungsmaterial aus Aluminium-Legierung für Stossfänger und Verfahren zur Herstellung
JPH08225874A (ja) * 1995-02-14 1996-09-03 Furukawa Electric Co Ltd:The 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
JPH08232035A (ja) * 1995-02-24 1996-09-10 Sumitomo Light Metal Ind Ltd 曲げ加工性に優れたバンパー用高強度アルミニウム合金材およびその製造方法
JPH08295975A (ja) * 1995-04-21 1996-11-12 Kobe Steel Ltd 焼入れ歪性に優れたアルミニウム合金押出材及びその製造方法
EP0805219A1 (de) * 1996-05-03 1997-11-05 Aluminium Company Of America Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0711368A (ja) * 1993-04-30 1995-01-13 Kobe Steel Ltd 曲げ性が優れたＡｌ−Ｍｇ−Ｓｉ系合金押出材
JPH0754090A (ja) * 1993-08-13 1995-02-28 Kobe Steel Ltd 曲げ加工性及び衝撃吸収性が優れたアルミニウム合金材及びその製造方法
EP0687743A1 (de) * 1994-06-16 1995-12-20 The Furukawa Electric Co., Ltd. Verstärkungsmaterial aus Aluminium-Legierung für Stossfänger und Verfahren zur Herstellung
JPH08225874A (ja) * 1995-02-14 1996-09-03 Furukawa Electric Co Ltd:The 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
JPH08232035A (ja) * 1995-02-24 1996-09-10 Sumitomo Light Metal Ind Ltd 曲げ加工性に優れたバンパー用高強度アルミニウム合金材およびその製造方法
JPH08295975A (ja) * 1995-04-21 1996-11-12 Kobe Steel Ltd 焼入れ歪性に優れたアルミニウム合金押出材及びその製造方法
EP0805219A1 (de) * 1996-05-03 1997-11-05 Aluminium Company Of America Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung

Non-Patent Citations (4)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 1995, no. 04 31 May 1995 (1995-05-31) *
PATENT ABSTRACTS OF JAPAN vol. 1995, no. 05 30 June 1995 (1995-06-30) *
PATENT ABSTRACTS OF JAPAN vol. 1997, no. 01 31 January 1997 (1997-01-31) *
PATENT ABSTRACTS OF JAPAN vol. 1997, no. 03 31 March 1997 (1997-03-31) *

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101130656B1 (ko) * 2003-11-20 2012-04-02 노벨리스 인코퍼레이티드 차체 부품
US9085328B2 (en) 2003-11-20 2015-07-21 Novelis Inc. Automobile body part
US9242678B2 (en) 2003-11-20 2016-01-26 Novelis Inc. Automobile body part
US9731772B2 (en) 2003-11-20 2017-08-15 Novelis Inc. Automobile body part
US8940406B2 (en) 2008-08-13 2015-01-27 Novelis Inc. Automobile body part
US9193134B2 (en) 2008-08-13 2015-11-24 Novelis Inc. Automobile body part
EP2553131B1 (de) 2010-03-30 2019-05-08 Norsk Hydro ASA Hochtemperaturstabile aluminiumlegierung
EP2841611B1 (de) 2012-04-25 2018-04-04 Norsk Hydro ASA Strangpressprofil aus einer Al-Mg-Si-aluminiumlegierung mit verbesserten eigenschaften
WO2019206826A1 (en) * 2018-04-24 2019-10-31 Constellium Singen Gmbh 6xxx aluminum alloy for extrusion with excellent crash performance and high yield strength and method of production thereof

Also Published As

Publication number Publication date
US20030041925A1 (en) 2003-03-06
US20020014287A1 (en) 2002-02-07

Similar Documents

Publication Publication Date Title
US6258465B1 (en) Energy absorbing member
US8105449B2 (en) High-strength aluminum alloy extruded product with excellent impact absorption and stress corrosion cracking resistance and method of manufacturing the same
CA2089171C (en) Improved lithium aluminum alloy system
EP2548984B1 (de) Aluminiumlegierungsmaterial für einen speicherbehälter für hochdruck-wasserstoffgas
EP2157200B1 (de) Aus Al-Mg-Si-Aluminiumlegierung extrudiertes Produkt, das eine hervorragende Gestaltfestigkeit und Schlagbruchzähigkeit aufweist
EP0642598B1 (de) Hochfeste-al-li-legierung mit niedriger dichte und hoher zähigkeit bei hohen temperaturen
EP0997547A1 (de) Stranggepresste Al-Mg-Si Legierung auf Aluminium Basis
CN111989415B (zh) 用于具有优异的碰撞性能和高屈服强度的挤压件的6xxx铝合金及其制备方法
JP4942372B2 (ja) 電磁成形用アルミニウム合金押出材
JP2008274441A (ja) 圧壊特性に優れるアルミニウム合金押出材
US20090191090A1 (en) Aluminum alloy extruded product exhibiting excellent impact cracking resistance and impact absorber
US20030207143A1 (en) Shock absorbing material
JP3077974B2 (ja) 軸圧壊特性に優れるＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金押出形材
JP3502939B2 (ja) 衝撃エネルギー吸収性に優れるＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金押出形材
JP3454755B2 (ja) 耐圧壊割れ性に優れた衝撃吸収部材
KR20010087232A (ko) 도어빔용 Ａℓ-Ｍｇ-Ｓｉ계 알루미늄합금압출재 및 도어빔
EP0805219A1 (de) Fahrzeugrahmenbauteile mit verbesserter Energieabsorptionsfähigkeit, Verfahren zu ihrer Herstellung und eine Legierung
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
JP2910920B2 (ja) アルミニウム合金製ドアビーム材
JP3077976B1 (ja) 押出軸方向の衝撃エネルギー吸収特性に優れるＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金押出形材
JP4183396B2 (ja) 圧壊特性に優れるアルミニウム合金押出材
JP3073197B1 (ja) 自動車のフレーム構造における衝撃吸収部材
JP4052641B2 (ja) 衝撃吸収特性に優れ、かつ良好な焼き入れ性と押出性を有するアルミニウム合金及びその製造方法
JP2003268474A (ja) 衝撃エネルギー吸収性に優れるＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金押出形材

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 FR GB

AX Request for extension of the european patent

Free format text: AL;LT;LV;MK;RO;SI

17P Request for examination filed

Effective date: 20000615

17Q First examination report despatched

Effective date: 20000918

AKX Designation fees paid

Free format text: DE FR GB

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

Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN

18D Application deemed to be withdrawn

Effective date: 20030114