EP3303646B1 - Metallblech für eine kraftfahrzeugkarosserie mit hoher mechanischer festigkeit - Google Patents

Metallblech für eine kraftfahrzeugkarosserie mit hoher mechanischer festigkeit Download PDF

Info

Publication number
EP3303646B1
EP3303646B1 EP16735908.2A EP16735908A EP3303646B1 EP 3303646 B1 EP3303646 B1 EP 3303646B1 EP 16735908 A EP16735908 A EP 16735908A EP 3303646 B1 EP3303646 B1 EP 3303646B1
Authority
EP
European Patent Office
Prior art keywords
temperature
alloy
content
hours
sheet
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.)
Active
Application number
EP16735908.2A
Other languages
English (en)
French (fr)
Other versions
EP3303646A1 (de
Inventor
Estelle MULLER
Mary-Anne Kulas
Olivier Rebuffet
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.)
Constellium Neuf Brisach SAS
Original Assignee
Constellium Neuf Brisach SAS
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
Application filed by Constellium Neuf Brisach SAS filed Critical Constellium Neuf Brisach SAS
Publication of EP3303646A1 publication Critical patent/EP3303646A1/de
Application granted granted Critical
Publication of EP3303646B1 publication Critical patent/EP3303646B1/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • B21B1/463—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a continuous process, i.e. the cast not being cut before rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B22D11/003—Aluminium alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
    • B22D11/041—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds for vertical casting
    • 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
    • C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
    • 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
    • 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
    • C22F1/053—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 zinc as the next major constituent

Definitions

  • the invention relates to the field of Al-Si-Mg alloy sheets, more particularly alloy type AA6xxx according to the designation of the "Aluminum Association", added with hardening elements and intended for the manufacture by stamping of lining parts , of structure or reinforcement of the white box of motor vehicles.
  • an alloy comprising 0.6-1.15% Si; 0.6-1% Cu; 0.8-1.2% Mg; 0.55-0.86% Zn; less than 0.1% Mn, 0.2-0.3% Cr and about 0.2% Fe, used in the T6 state, combines good resistance to intergranular corrosion, as well as a Rp 0.2 of 380 MPa.
  • WO03006697 relates to an alloy of the AA6xxx series with 0.2 to 0.45% Cu.
  • the object of the invention is to propose an AA6013 type alloy with a reduced Cu level, targeting 355 MPa of Rm at the T6 state and good resistance to intergranular corrosion.
  • the claimed composition is as follows: 0.8-1.3% Si, 0.2-0.45% Cu, 0.5-1.1% Mn, 0.45-1.0% Mg.
  • % chromium the rest mainly aluminum, secondary elements and impurities; (B) homogenization, (C) heat distortion (D) dissolution and (E) quenching; wherein the product has a ductility loss of at least 5% less than a comparable treated alloy comprising about 0.88 wt% Cu, 0.05 wt%, 0.75 wt% Si, 0 wt. 17 wt.% Fe, 0.42 wt.% Mn, 0.95 wt.% Mg, 0.08 wt.% Ti, and ⁇ 0.01 wt.% Cr.
  • the patent application JPH05112840 describes a car body sheet of composition, in% by weight, 0.4 to 1.5% Mg, 0.24 to 1.5% Si, 0.12 to 1.5 % Cu, 0.1 to 1.0% Zn, 0.005 to 0.15% Ti and at most 0.25% Fe, wherein Si and Mg satisfy the Si ratio at most 0.6 Mg (%), and containing at least one of 0.08 to 0.30% Mn, 0.05 to 0.20% Cr, 0.05 to 0.20% Zr, 0 , 04 to 0.10% V and from 0.0002 to 0.05% of B and the remainder of Al with unavoidable impurities.
  • the object of the present invention is to provide aluminum alloy sheets for lining, reinforcement or automotive body structure having a resistance mechanical operation, after shaping and baking paints, also, or even higher, than the sheets of the prior art, while having a good resistance to corrosion, particularly intergranular or filiform, a formability by stamping at temperature satisfactory ambient and good behavior in various assembly processes such as spot welding, laser welding, gluing, clinching or riveting.
  • the homogenization and reheating steps above are replaced by a single reheating step at a temperature between 550 and 570 ° C with a maintenance between 2 and 12 h, preferably between 4 and 6 h, followed by hot rolling as above.
  • the sheet obtained by the above process has, after optional maturation at room temperature of between 72 h and 6 months, a controlled tensile pre-deformation of 2% to simulate the shaping, and treatment of typically paints for 20 min at 185 ° C, a yield strength Rp 0.2 of at least 300 MPa.
  • the invention is based on the finding made by the applicant that a narrow composition range within the composition of an alloy of the AA6xxx family registered with the "Aluminum Association", combined with a combined addition of Zn, V and Ti, allowed to obtain all the desired properties, namely high mechanical strength in service, after shaping and baking paints, related in particular to the addition of zinc but combined surprisingly and unexpectedly, because a priori of the simultaneous presence of V and Ti, to a resistance to corrosion, intergranular and filiform, very satisfactory and formability in stamping at satisfactory ambient temperature.
  • the sheets according to the invention have a satisfactory ability to draw at room temperature.
  • they have, in use, after shaping, assembly and baking paints, high mechanical properties, good resistance to corrosion, in particular intergranular corrosion and filiform corrosion.
  • Table 1 summarizes the nominal chemical compositions (% by weight) of the alloys used in the tests.
  • the foundry plates of these different alloys were obtained by vertical semi-continuous casting.
  • the plates of cases 1, 6, 7, 8 and 10 have undergone a homogenization treatment to 570 ° C consisting of a rise in temperature at a speed of 30 ° C / h up to 570 ° C, a maintenance of the order of 5 hours at 570 ° C and a controlled cooling with forced air up to ambient temperature.
  • This homogenization step is followed by a heating step consisting of a rise in temperature at a speed of 70 ° C./h up to 480 ° C. with a holding time of the order of 40 minutes, directly followed by hot rolling.
  • the plates of case 2 underwent a homogenization treatment at 562 ° C.
  • the homogenization step is followed by a heating step consisting of a rise in temperature at a speed of 60 ° C./h up to 530 ° C. with a maximum temperature retention of 2 hours, followed by rolling. hot.
  • the plates of cases 3 and 5 were reheated consisting of a rise at respectively 565 ° C and 550 ° C with minimum maintenance of 2 hours at these temperatures, directly followed by hot rolling.
  • the plates of cases 4 and 9, made of AA6016 and AA5182 type alloys, have undergone standard homogenizations for these types of alloys.
  • the next hot rolling step takes place on a reversible rolling mill followed according to the case of a hot tandem rolling mill with 4 stands up to a thickness of between 3 and 10 mm.
  • the hot rolling output thicknesses of the tested cases are given in Table 2.
  • This hot rolling step is followed by a cold rolling step which makes it possible to obtain sheets having thicknesses of between 1.7 and 2.5 mm.
  • the cold rolling output thicknesses of the tested cases are given in Table 2.
  • the rolling steps are followed by a solution heat treatment step and quenching.
  • the dissolution is done at a temperature above the solvus temperature of the alloy, while avoiding burning.
  • the dissolved sheet is then quenched at a minimum speed of 50 ° C / s.
  • this step is carried out in a passing furnace by raising the temperature of the metal to 570 ° C in less than about one minute directly followed by quenching.
  • the quenching is followed by a pre-tempered heat treatment, intended to improve the curing performance during the baking of the paints.
  • this step is performed by winding at a temperature of at least 60 ° C followed by cooling in the open air.
  • the winding temperatures are described in Table 2.
  • yield strengths of alloy sheets 1, 2 and 3, according to the invention are greater than 300 MPa, as claimed, which is not the case for other alloys.
  • yield strengths of alloy sheets 1, 2 and 3, according to the invention are greater than 350 MPa, as claimed, which is not the case for other alloys.
  • the ductility in service can be estimated by a "three-point bend test" according to the NF EN ISO 7438 standard and the VDA 238-100 procedure.
  • the folding device is as presented in figure 1 .
  • the punch is brought into contact with the sheet with a pre-force of 30 Newtons. Once the contact is established, the displacement of the punch is indexed to zero. The test then consists in moving the punch so as to perform the "three-point folding" of the sheet.
  • the test stops when a micro-cracking of the sheet leads to a force drop on the punch of at least 30 Newtons, or when the punch has moved 14.2 mm, which corresponds to the stroke maximum allowed.
  • the sheet sample is thus folded as illustrated in figure 2 .
  • the ductility in service is then evaluated by measuring the angle of folding ⁇ , here called ⁇ 10% , in degrees.
  • ⁇ 10% the angle of folding ⁇
  • the higher the angle ⁇ 10% the better the crimping or folding ability of the sheet.
  • angle ⁇ 10% of the sheet according to the invention is greater than 60 °.
  • the LDH parameter is widely used for the evaluation of the drawability of sheets with a thickness of 0.5 to 3.0 mm. It has been the subject of numerous publications, in particular that of R. Thompson, "The LDH test to evaluate sheet Metal Formability - Final Report of the LDH Committee of the North American Deep Drawing Research Group, "SAE Conference, Detroit, 1993, SAE Paper No. 930815 .
  • the blanking pressure is controlled to prevent slippage in the rod.
  • the blank dimensions 120 x 160 mm, is biased in a mode close to the plane strain.
  • the punch used is hemispherical.
  • the figure 3 specifies the dimensions of the tools used to perform this test.
  • the lubrication between the punch and the plate is ensured by graphited grease (Shell HDM2 grease).
  • the speed of descent of the punch is 50 mm / min.
  • the value called LDH is the value of the displacement of the punch at break, the limit depth of the stamping. It actually corresponds to the average of three tests, giving a 95% confidence interval on the 0.2 mm measurement.
  • Table 6 shows the values of the LDH parameter obtained on test pieces of 120 ⁇ 160 mm cut from the above-mentioned sheets with a thickness of 2.5 mm and for which the dimension of 160 mm was positioned parallel to the rolling direction. ⁇ b> Table 6 ⁇ / b> LDH (mm) Alloy 8 37.1 Invention 2 36.5
  • the sheet according to the invention has an LDH value similar to the LDH value obtained for an alloy sheet of the AA5182 (alloy 8) type, reference alloy when it comes to panels. bodywork for severe stamping.
  • the intergranular corrosion test according to ISO 11846 consists of immersing the test pieces for 24 h in a solution of sodium chloride (30 g / l) and hydrochloric acid (10 ml / l) at a temperature of 30 ° C ( obtained by means of holding in a drying oven), after stripping with hot soda (5% by mass) and with nitric acid (70% by mass) at room temperature.
  • the samples have a dimension of 40 mm (rolling direction) x 30 mm x thickness.
  • the type and depth of corrosion caused is determined by a micrographic sectional examination of the metal. The maximum depth of corrosion is measured.
  • the maximum depth of attack appears significantly lower for the alloy according to the invention, reflecting a better resistance to intergranular corrosion.

Claims (14)

  1. Blech für tiefgezogene Auskleidungs-, Verstärkungs- oder Strukturteile einer Kraftfahrzeugkarosserie, auch Rohkarosserie genannt, aus einer Aluminiumlegierung der Serie AA6xxx mit der Zusammensetzung (Gew.-%):
    Si: 0,85 - 1,20 Fe: < 0,30 Cu: 0,10 - 0,30 Mg: 0,70 - 0,90 Mn: < 0,30 Zn: 0,9 - 1,60 V: 0,02 - 0,30 Ti: 0,05 - 0,20
    weitere Elemente jeweils < 0,05 und insgesamt < 0,15, Rest Aluminium.
  2. Blech nach Anspruch 1, dadurch gekennzeichnet, dass der Si-Gehalt zwischen 0,90 und 1, 10 % liegt.
  3. Blech nach einem der Ansprüche 1 oder 2, dadurch gekennzeichnet, dass der Cu-Gehalt zwischen 0,10 und 0,20 % liegt.
  4. Blech nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass der Mg-Gehalt zwischen 0,70 und 0,80 % liegt.
  5. Blech nach einem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass der Zn-Gehalt zwischen 0,10 und 1,60 % und vorzugsweise zwischen 1,20 und 1,50 % liegt.
  6. Blech nach einem der Ansprüche 1 bis 5, dadurch gekennzeichnet, dass der V-Gehalt zwischen 0,05 und 0,30 % und vorzugsweise zwischen 0,10 und 0,20 % liegt.
  7. Blech nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass der Ti-Gehalt zwischen 0,08 und 0,15 % liegt.
  8. Blech nach einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, dass der Mn-Gehalt zwischen 0,10 und 0,20 % liegt.
  9. Blech nach einem der Ansprüche 1 bis 8, dadurch gekennzeichnet, dass der Fe-Gehalt zwischen 0,15 und 0,25 % liegt.
  10. Verfahren zur Herstellung eines Blechs nach einem der Ansprüche 1 bis 9, umfassend die folgenden Schritte:
    - typischerweise halbkontinuierliches Vertikalstranggießen eines Barrens und eventuelles Fräsen des Barrens,
    - Homogenisieren des Barrens bei einer Temperatur von 550 bis 570°C mit einer Haltezeit zwischen 2 und 12 h, vorzugsweise zwischen 4 und 6 h, und anschließendes rasches Abkühlen,
    - Erwärmen auf eine Temperatur zwischen 450 und 550°C mit einer Haltezeit zwischen 30 min und 3 h, vorzugsweise etwa 2 h,
    - Warmwalzen des Barrens zu einem Band mit einer Dicke zwischen 3 und 10 mm,
    - Kaltwalzen bis auf die Enddicke,
    - Lösungsglühen des gewalzten Bandes bei einer Temperatur oberhalb der Solvustemperatur der Legierung unter Vermeidung von Verbrennungen, d. h. zwischen 550 und 570°C für 5 s bis 5 min, und anschließendes Abschrecken mit einer Geschwindigkeit von 50°C/s und vorzugsweise mehr als 100°C/s,
    - Vorauslagerungsbehandlung, oder Reversion, durch Aufwickeln bei einer Temperatur von mindestens 60°C, und anschließendes Abkühlen des erhaltenen Coils an der Luft.
  11. Verfahren zur Herstellung eines Blechs nach einem der Ansprüche 1 bis 9, umfassend die folgenden Schritte:
    - typischerweise halbkontinuierliches Vertikalstranggießen eines Barrens und eventuelles Fräsen des Barrens,
    - Erwärmen dieses Barrens auf eine Temperatur zwischen 550 und 570°C mit einer Haltezeit zwischen 2 und 12 h, vorzugsweise zwischen 4 und 6 h,
    - Warmwalzen des Barrens zu einem Band mit einer Dicke zwischen 3 und 10 mm,
    - Kaltwalzen bis auf die Enddicke,
    - Lösungsglühen des gewalzten Bandes bei einer Temperatur oberhalb der Solvustemperatur der Legierung unter Vermeidung von Verbrennungen, d. h. zwischen 550 und 570°C für 5 s bis 5 min, und anschließendes Abschrecken mit einer Geschwindigkeit von 50°C/s und vorzugsweise mehr als 100°C/s,
    - Vorauslagerungsbehandlung, oder Reversion, durch Aufwickeln bei einer Temperatur von mindestens 60°C und anschließendes Abkühlen des erhaltenen Coils an der Luft.
  12. Blech, welches durch das Verfahren nach einem der Ansprüche 10 oder 11 erhalten wird, dadurch gekennzeichnet, dass es nach eventueller Kaltauslagerung bei Raumtemperatur zwischen 72 h und 6 Monaten, einem Vorumformen durch kontrolliertes Recken von 2 % und Einbrennen der Lackierung, typischerweise 20 min bei 185°C, eine Dehngrenze Rp0,2 von mindestens 300 MPa aufweist.
  13. Blech, welches durch das Verfahren nach einem der Ansprüche 10 oder 11 erhalten wird, dadurch gekennzeichnet, dass es im Werkstoffzustand T6 gemäß EN 515 eine Dehngrenze Rp0,2 von mindestens 350 MPa aufweist.
  14. Blech mit einer Dicke von 2 mm, welches durch das Verfahren nach einem der Ansprüche 10 oder 11 erhalten wird, dadurch gekennzeichnet, dass es nach eventueller Kaltauslagerung bei Raumtemperatur zwischen 72 h und 6 Monaten, einem Vorumformen durch kontrolliertes Recken von 10 % und Einbrennen der Lackierung, typischerweise 20 min bei 185°C, einen « Drei-Punkt-Biegewinkel » α10%, gemessen nach NF EN ISO 7438 und VDA-Verfahren 238-100, von mindestens 60° aufweist.
EP16735908.2A 2015-06-05 2016-06-03 Metallblech für eine kraftfahrzeugkarosserie mit hoher mechanischer festigkeit Active EP3303646B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR1555129A FR3036986B1 (fr) 2015-06-05 2015-06-05 Tole pour carrosserie automobile a resistance mecanique elevee
PCT/FR2016/051333 WO2016193640A1 (fr) 2015-06-05 2016-06-03 Tole pour carrosserie automobile a résistance mécanique élevée

Publications (2)

Publication Number Publication Date
EP3303646A1 EP3303646A1 (de) 2018-04-11
EP3303646B1 true EP3303646B1 (de) 2019-04-24

Family

ID=54015010

Family Applications (1)

Application Number Title Priority Date Filing Date
EP16735908.2A Active EP3303646B1 (de) 2015-06-05 2016-06-03 Metallblech für eine kraftfahrzeugkarosserie mit hoher mechanischer festigkeit

Country Status (11)

Country Link
US (1) US10829844B2 (de)
EP (1) EP3303646B1 (de)
JP (1) JP2018521229A (de)
KR (1) KR20180016375A (de)
CN (1) CN107709590B (de)
AR (1) AR104913A1 (de)
BR (1) BR112017023524A2 (de)
FR (1) FR3036986B1 (de)
RU (1) RU2017145569A (de)
TR (1) TR201907640T4 (de)
WO (1) WO2016193640A1 (de)

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CA3008021C (en) 2016-01-08 2020-10-20 Arconic Inc. 6xxx aluminum alloys, and methods of making the same
MX2019001802A (es) 2016-08-26 2019-07-04 Shape Corp Proceso de modelacion en caliente y aparato para flexion transversal de una viga de aluminio extrudida para modelar en caliente un componente estructural del vehiculo.
WO2018078527A1 (en) 2016-10-24 2018-05-03 Shape Corp. Multi-stage aluminum alloy forming and thermal processing method for the production of vehicle components
US10030295B1 (en) 2017-06-29 2018-07-24 Arconic Inc. 6xxx aluminum alloy sheet products and methods for making the same
EP3704279A4 (de) 2017-10-31 2021-03-10 Howmet Aerospace Inc. Verbesserte aluminiumlegierungen und verfahren zur herstellung davon
CN108754363A (zh) * 2018-06-22 2018-11-06 中南大学 调控铝合金构件应力松弛行为的方法
CN112941432B (zh) * 2019-11-26 2022-08-16 晟通科技集团有限公司 6系铝型材及铝型材的热处理工艺
EP3839085B1 (de) * 2019-12-17 2023-04-26 Constellium Neuf-Brisach Verbessertes verfahren zur herstellung eines strukturteils für eine kraftfahrzeugkarosserie
CN114107744B (zh) * 2020-08-26 2022-10-21 宝山钢铁股份有限公司 薄带连铸6xxx铝合金板带及其制备方法

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05112840A (ja) * 1991-10-18 1993-05-07 Nkk Corp プレス成形性に優れた焼付硬化性Ａｌ−Ｍｇ−Ｓｉ系合金板及びその製造方法
CA2218024C (en) * 1995-05-11 2008-07-22 Kaiser Aluminum And Chemical Corporation Improved damage tolerant aluminum 6xxx alloy
US6231809B1 (en) * 1998-02-20 2001-05-15 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Al-Mg-Si aluminum alloy sheet for forming having good surface properties with controlled texture
AU2001286386A1 (en) 2000-06-01 2001-12-11 Alcoa Inc. Corrosion resistant 6000 series alloy suitable for aerospace applications
ES2238584T3 (es) 2001-07-09 2005-09-01 Corus Aluminium Walzprodukte Gmbh Aleacion de al-mg-si de alta resistencia.
JP4101749B2 (ja) 2001-07-23 2008-06-18 コラス・アルミニウム・バルツプロドウクテ・ゲーエムベーハー 溶接可能な高強度Ａｌ−Ｍｇ−Ｓｉ合金
JP2003268475A (ja) * 2002-03-12 2003-09-25 Sky Alum Co Ltd 成形加工用アルミニウム合金板およびその製造方法
FR2856368B1 (fr) 2003-06-18 2005-07-22 Pechiney Rhenalu Piece de peau de carrosserie automobile en tole d'alliage ai-si-mg fixee sur structure acier
DE102005045340B4 (de) * 2004-10-05 2010-08-26 Aleris Aluminum Koblenz Gmbh Verfahren zum Wärmebehandeln eines Aluminiumlegierungselements
JP2006322064A (ja) * 2005-04-19 2006-11-30 Furukawa Electric Co Ltd:The 高成形性アルミニウム材料
JP4939093B2 (ja) * 2006-03-28 2012-05-23 株式会社神戸製鋼所 ヘム曲げ性およびベークハード性に優れる自動車パネル用６０００系アルミニウム合金板の製造方法
US20140356647A1 (en) * 2011-11-02 2014-12-04 Uacj Corporation Aluminum alloy clad material for forming

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
US10829844B2 (en) 2020-11-10
KR20180016375A (ko) 2018-02-14
CN107709590B (zh) 2020-10-13
WO2016193640A1 (fr) 2016-12-08
RU2017145569A (ru) 2019-07-09
JP2018521229A (ja) 2018-08-02
CN107709590A (zh) 2018-02-16
US20180179621A1 (en) 2018-06-28
FR3036986A1 (fr) 2016-12-09
EP3303646A1 (de) 2018-04-11
TR201907640T4 (tr) 2019-06-21
FR3036986B1 (fr) 2017-05-26
BR112017023524A2 (pt) 2018-07-24
AR104913A1 (es) 2017-08-23

Similar Documents

Publication Publication Date Title
EP3303646B1 (de) Metallblech für eine kraftfahrzeugkarosserie mit hoher mechanischer festigkeit
EP3362282B1 (de) Strukturbauteil einer kraftfahrzeugschale zur bereitstellung eines hervorragenden kompromisses zwischen mechanischer festigkeit und crashfestigkeit
EP1472380B1 (de) Blech aus al-si-mg-legierung für karroserie von kraftfahrzeugen
EP3317041B1 (de) Verfahren zum laserschweissen von monolithischem halbzeug aus einer aluminiumlegierung ohne fülldraht sowie entsprechendes bauteil und massgeschneiderter rohling
EP2750882B1 (de) Breitschlitzverbundfolie aus aluminum für karosseriewerkstatt
EP3384060B1 (de) Hochsteifes dünnes blech für eine fahrzeugkarosserie
EP1633900B1 (de) Dach eines kraftfahrzeugs aus einem an einem stahlrahmen befestigten blech aus einer al-si-mg-legierung
WO2018185425A1 (fr) Procede ameliore de fabrication de composant de structure de caisse automobile
EP3019637B1 (de) Blech aus aluminiumlegierung für die struktur eines kraftfahrzeugs
EP3555331B1 (de) Aluminiumlegierung zum laserschweissen ohne fülldraht
EP4355923A1 (de) Band aus 6xxx-legierung und herstellungsverfahren
WO2023094773A1 (fr) Bande en alliage 6xxx et procédé de fabrication

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

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

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

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20171213

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 602016012909

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C22C0021020000

Ipc: C22C0021080000

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

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

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 21/08 20060101AFI20181030BHEP

INTG Intention to grant announced

Effective date: 20181120

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

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

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602016012909

Country of ref document: DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1124235

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190515

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: FRENCH

REG Reference to a national code

Ref country code: CH

Ref legal event code: NV

Representative=s name: RENTSCH PARTNER AG, CH

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20190424

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190424

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

Ref country code: FI

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: 20190424

Ref country code: LT

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: 20190424

Ref country code: AL

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: 20190424

Ref country code: PT

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: 20190824

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: 20190424

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: 20190424

Ref country code: NO

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: 20190724

Ref country code: HR

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: 20190424

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

Ref country code: GR

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: 20190725

Ref country code: LV

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: 20190424

Ref country code: PL

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: 20190424

Ref country code: BG

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: 20190724

Ref country code: RS

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: 20190424

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

Ref country code: IS

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: 20190824

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602016012909

Country of ref document: DE

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

Ref country code: EE

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: 20190424

Ref country code: CZ

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: 20190424

Ref country code: RO

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: 20190424

Ref country code: MC

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: 20190424

Ref country code: DK

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: 20190424

Ref country code: SK

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: 20190424

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

Ref country code: SM

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: 20190424

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

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

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20200127

REG Reference to a national code

Ref country code: AT

Ref legal event code: UEP

Ref document number: 1124235

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190424

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

Ref country code: IE

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

Effective date: 20190603

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

Ref country code: SI

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: 20190424

Ref country code: LU

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

Effective date: 20190603

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

Ref country code: TR

Payment date: 20200527

Year of fee payment: 5

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

Ref country code: GB

Payment date: 20200629

Year of fee payment: 5

Ref country code: IT

Payment date: 20200619

Year of fee payment: 5

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

Ref country code: CY

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: 20190424

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

Ref country code: HU

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

Effective date: 20160603

Ref country code: MT

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: 20190424

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20210603

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 NON-PAYMENT OF DUE FEES

Effective date: 20210603

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

Ref country code: MK

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: 20190424

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

Ref country code: IT

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

Effective date: 20210603

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230411

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

Ref country code: FR

Payment date: 20230626

Year of fee payment: 8

Ref country code: DE

Payment date: 20230626

Year of fee payment: 8

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

Ref country code: AT

Payment date: 20230519

Year of fee payment: 8

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

Ref country code: BE

Payment date: 20230627

Year of fee payment: 8

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

Ref country code: CH

Payment date: 20230702

Year of fee payment: 8