EP2175042A1 - Corrosion-resistant aluminium extrusion profile and method for manufacturing a structure component - Google Patents

Corrosion-resistant aluminium extrusion profile and method for manufacturing a structure component Download PDF

Info

Publication number
EP2175042A1
EP2175042A1 EP09011984A EP09011984A EP2175042A1 EP 2175042 A1 EP2175042 A1 EP 2175042A1 EP 09011984 A EP09011984 A EP 09011984A EP 09011984 A EP09011984 A EP 09011984A EP 2175042 A1 EP2175042 A1 EP 2175042A1
Authority
EP
European Patent Office
Prior art keywords
corrosion
heat treatment
alloy
extrusion
extruded
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.)
Granted
Application number
EP09011984A
Other languages
German (de)
French (fr)
Other versions
EP2175042B1 (en
Inventor
Hubert Dr. Koch
Jana Dipl.-Ing. Ehrke
Marcel Dr. Rosefort
Dieter Dr. Bramhoff
Horst Gers
Dirk Schnapp
Thomas Dipl.-Ing. Köhler
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.)
Trimet Aluminium SE
Martinrea Honsel Germany GmbH
Original Assignee
Honsel AG
Trimet Aluminium SE
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 Honsel AG, Trimet Aluminium SE filed Critical Honsel AG
Publication of EP2175042A1 publication Critical patent/EP2175042A1/en
Application granted granted Critical
Publication of EP2175042B1 publication Critical patent/EP2175042B1/en
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
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—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 magnesium as the next major constituent

Definitions

  • the invention relates to a corrosion-resistant aluminum extruded profile of an ALSiMg alloy, preferably a multi-chamber hollow profile and method for
  • the strength of aluminum wrought alloys of the AlMgSi type (6xxxx alloys) is essentially set by the alloying process (D. Altenpohl: "Aluminum viewed from the inside", Aluminum-Verlag). In this case, foreign atoms or precipitates act as impurities in the lattice of the Al microstructure. In the AlMgSi alloy type, it is the Mg 2 Si intermetallic compound which increases strength.
  • Object of the present invention was to produce an extruded profile with which at least the previously known deformation and corrosion properties are achieved, but at higher strength properties and that Rp 0.2> 280
  • the H 2 content of the melt is adjusted in the usual way by chlorination, by nitrogen or argon rinsing treatment.
  • the alloy is characterized by an excess of Mg, with the preferred weight ratio of magnesium to silicon in the alloy composition ranging from 1 to 2 at an alloy content of Si 0.30-0.60%.
  • the deformation properties and the ductility can be significantly improved if the contents of Mn, Fe, Cu and optionally Ti and Cr are significantly limited (see claim 1).
  • Mn and Cr are added during homogenization form dispersoids which can prevent recrystallization of the microstructure. These dispersoids reduce the local stresses in the structure and thereby increase the ductility.
  • the optimum content for Mn is between 0.05 and 0.10 and for Cr between 0.01 and 0.12%.
  • Titanium also increases ductility, with the content being between 0.01-0.12%.
  • the alloy is cast in a continuous casting process and then homogenized in the temperature range between 450 and 600 ° C in 1-10h.
  • the extruded profile is subjected to an immediate heat treatment in the temperature range 160-250 ° C for 20-1800min.
  • Table 1 Heat treatment and technological properties for four types of alloys according to the invention and two comparative alloys
  • Table 2 Alloy composition of the alloys according to the invention and of the comparative alloys in% by weight
  • Image 1 Microstructure of a structural component produced according to the invention
  • Picture 2 Microstructure of a structural component according to the prior art
  • Picture 3 Profile cross-section of the examined structural component
  • test numbers I to VI Six different hollow profiles (test numbers I to VI) with the homogenization conditions specified in Table 1 were produced by extrusion and subsequently heat-treated.
  • test numbers III, IV, V and VI showed good deformation and corrosion properties with increased strength and acceptable elongation values.
  • the special properties are based on the fact that the intermetallic phases of the type Mg 2 Si, Al 3 Fe, Al 2 Cu were formed during the heat treatment, so that globulitic particles ⁇ 1 ⁇ were uniformly distributed. This is shown by the micrograph Figure 1 for a hollow profile of the invention produced according to the invention V1 according to Table 2.
  • the structural components produced by the process according to the invention showed an improvement in notched impact strength. This was especially true of the alloys of the experiment no. V and VI whose results in the notched-bar impact tests exceeded by more than 10% over the comparative values of tests III. and IV. and more than 20% above the values of experiments I. and II.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Extrusion Of Metal (AREA)
  • Continuous Casting (AREA)
  • Powder Metallurgy (AREA)

Abstract

The corrosion-resistant multi-chamber hollow profile made of alloy of aluminum, silicon and magnesium, comprises a microstructure with form intermetallic phases, whose particles are globulistically formed. The particles of intermetallic phase have a diameter of = 1 mu m. An independent claim is included for a method for the production of corrosion-resistant multi-chamber hollow profile.

Description

Die Erfindung betrifft ein korrosionsbeständiges Aluminiumstrangpressprofil aus einer ALSiMg-Legierung, vorzugsweise ein Mehrkammerhohlprofil und Verfahren zurThe invention relates to a corrosion-resistant aluminum extruded profile of an ALSiMg alloy, preferably a multi-chamber hollow profile and method for

Herstellung eines Strangpressprofils.Production of an extruded profile.

Stand der Technik:State of the art:

Die Festigkeit bei Aluminium-Knetlegierungen vom Typ AlMgSi (6xxxx-Legierungen) wird im Wesentlichen durch die Legierungsverfestigung eingestellt (D. Altenpohl: "Aluminium von innen betrachtet", Aluminium-Verlag). Dabei wirken Fremdatome oder Ausscheidungen wie Störstellen im Gitter des Al-Gefüges. Bei dem Legierungstyp AlMgSi ist es die intermetallische Verbindung Mg2Si, die festigkeitssteigernd wirkt.The strength of aluminum wrought alloys of the AlMgSi type (6xxxx alloys) is essentially set by the alloying process (D. Altenpohl: "Aluminum viewed from the inside", Aluminum-Verlag). In this case, foreign atoms or precipitates act as impurities in the lattice of the Al microstructure. In the AlMgSi alloy type, it is the Mg 2 Si intermetallic compound which increases strength.

Viele der derzeit in Europa etablierten Al-Mg-Si-Knetlegierungen orientieren sich daher an der Mg2Si-Gleichgewichtsphase, besitzen aber zusätzlich einen Si-Überschuss. Das frei verfügbare Si bewirkt durch die Mischkristallbildung eine weitere Festigkeitssteigerung. Diese ist mit einem Si-Überschuss effektiver als bei einem gleichgroßen Mg-Überschuss (F. Ostermann: "Anwendungstechnologie Aluminium", Springer-Verlag).Many of the currently established in Europe Al-Mg-Si wrought alloys are therefore oriented to the Mg 2 Si equilibrium phase, but additionally have an excess of Si. The freely available Si causes by the formation of mixed crystals, a further increase in strength. This is more effective with an excess of Si than with an equally large excess of Mg (F. Ostermann: "Application Technology Aluminum", Springer-Verlag).

Ein Si-Überschuss erhöht jedoch die Abschreckempfindlichkeit der Legierung. Weiterhin neigen diese Legierungen zur Bildung von Korngrenzenausscheidungen, die die Duktilität negativ beeinflussen ( F. Ostermann: "Anwendungstechnologie Aluminium", Springer-Verlag ). Das Si/Mg-Verhältnis besitzt ferner einen Einfluss auf das Verformungsverhalten ( J. Roysted et. al.: "AIMgSi-alloys with improved Crush Properties", Extrusion Technologie 2008, Orlando ). Mit steigendem Si/Mg-Verhältnis bis 1,1 verbessert sich auch das Verformungsverhalten. Zugaben von Cu als Legierungselement erhöhen ebenfalls die Festigkeit, allerdings auf Kosten derHowever, an excess of Si increases the quench sensitivity of the alloy. Furthermore, these alloys tend to form grain boundary precipitates that adversely affect ductility ( F. Ostermann: "Application Technology Aluminum", Springer-Verlag ). The Si / Mg ratio also has an influence on the deformation behavior ( J. Roysted et. al .: "AIMgSi-alloys with improved Crush Properties", Extrusion Technology 2008, Orlando ). As the Si / Mg ratio increases to 1.1, the deformation behavior also improves. Additions of Cu as an alloying element also increase the strength, but at the expense of

Duktilität ( J. Roysted et. al.: "AIMgSi-alloys with improved Crush Properties", Extrusion Technologie 2008, Orlando ).Ductility ( J. Roysted et. al .: "AIMgSi-alloys with improved Crush Properties", Extrusion Technology 2008, Orlando ).

Aufgabe der vorliegenden Erfindung war es, ein Strangpressprofil zu erzeugen, mit dem zumindest die bisher bekannten Verformungs- und Korrosionseigenschaften erreicht werden, jedoch bei höheren Festigkeitseigenschaften und zwar Rp 0,2 > 280Object of the present invention was to produce an extruded profile with which at least the previously known deformation and corrosion properties are achieved, but at higher strength properties and that Rp 0.2> 280

MPa, Rm ≥ 300MPa und A ≥ 10%.MPa, Rm ≥ 300MPa and A ≥ 10%.

Die Aufgabe wird erfindungsgemäß gelöst durch ein Strangpressprofil aus der Aluminiumlegierung:

Si
0,3 - 0,6%
Mg
0,8-1,2%
Mn
0,03-0,1%
Fe
0,1-0,3%
Cu
0,1-0,3%
The object is achieved by an extruded profile of the aluminum alloy:
Si
0.3 - 0.6%
mg
0.8-1.2%
Mn
0.03-0.1%
Fe
0.1-0.3%
Cu
0.1-0.3%

Rest Reinaluminium mit den üblichen Verunreinigungen, dem wahlweise ein Gehalt an

Ti
0,01-0,12%
Cr
0,01-0,12%
Remaining pure aluminum with the usual impurities, the optional content of
Ti
0.01-0.12%
Cr
0.01-0.12%

zugesetzt werden kann.can be added.

Vorzugsweise beträgt der H2-Gehalt der Schmelze <=0,15ccm/100gr. Al. Der H2-Gehalt der Schmelze wird in üblicher Weise durch Chlorieren, durch Stickstoff- oder Argon-Spülbehandlung eingestellt.Preferably, the H 2 content of the melt is <= 0.15 ccm / 100gr. Al. The H 2 content of the melt is adjusted in the usual way by chlorination, by nitrogen or argon rinsing treatment.

Die Legierung zeichnet sich durch einen Mg-Überschuss aus, wobei das bevorzugte Gew-Verhältnis von Magnesium zu Silizium in der Legierungszusammensetzung im Bereich von 1 bis 2 bei einem Legierungsgehalt von Si 0,30 - 0,60% liegt.The alloy is characterized by an excess of Mg, with the preferred weight ratio of magnesium to silicon in the alloy composition ranging from 1 to 2 at an alloy content of Si 0.30-0.60%.

Neuere Untersuchungen zeigen, dass mit einem Mg/Si-Verhältnis von nahezu 1 gute Festigkeitsergebnisse erzielt werden können, wobei eine Steigerung der Produktivität dieser Legierungen z.B. durch höhere Pressgeschwindigkeit, niedrigerem Anpressdruck und besserer Oberflächenqualität besonders herausgestellt wird (Comalco Aluminium Ltd.: "6xxx series aluminium alloys", EP 1 840 234 A1 ).Recent studies show that with a Mg / Si ratio of nearly 1, good strength results can be achieved, with an increase in the productivity of these alloys, for example, by higher press speed, lower contact pressure and better surface quality is particularly highlighted (Comalco Aluminum Ltd .: "6xxx series aluminum alloys ", EP 1 840 234 A1 ).

Allerdings lassen sich die Verformungseigenschaften und die Duktivität wesentlich verbessern, wenn die Gehalte an Mn, Fe, Cu sowie ggf. Ti und Cr deutlich eingeschränkt werden (siehe Anspruch 1).However, the deformation properties and the ductility can be significantly improved if the contents of Mn, Fe, Cu and optionally Ti and Cr are significantly limited (see claim 1).

Es wurde beobachtet, dass Zusätze von Mn und Cr während der Homogenisierung Dispersoide bilden, die eine Rekristallisation des Gefüges verhindern können. Diese Dispersoide verringern die lokalen Spannungen im Gefüge und erhöhen dabei die Duktilität. Der optimale Gehalt für Mn liegt dabei zwischen 0,05 und 0,10 und bei Cr zwischen 0,01 und 0,12 %.It has been observed that additions of Mn and Cr during homogenization form dispersoids which can prevent recrystallization of the microstructure. These dispersoids reduce the local stresses in the structure and thereby increase the ductility. The optimum content for Mn is between 0.05 and 0.10 and for Cr between 0.01 and 0.12%.

Titan erhöht auch die Duktilität, wobei der Gehalt zwischen 0,01 - 0,12 % liegt.Titanium also increases ductility, with the content being between 0.01-0.12%.

Die Legierung wird im Stranggussverfahren vergossen und anschließend homogenisiert im Temperaturbereich zwischen 450 und 600°C in 1-10h. Das Strangpressprofil wird einer sofortigen Wärmebehandlung im Temperaturbereich 160-250°C für 20-1800min unterzogen.The alloy is cast in a continuous casting process and then homogenized in the temperature range between 450 and 600 ° C in 1-10h. The extruded profile is subjected to an immediate heat treatment in the temperature range 160-250 ° C for 20-1800min.

Im Folgenden wird die Erfindung anhand mehrerer Ausführungsbeispiele näher erläutert.In the following the invention will be explained in more detail with reference to several embodiments.

Es zeigen: Tabelle 1: Wärmebehandlung und technologische Eigenschaften bei vier Legierungstypen nach der Erfindung und zwei Vergleichslegierungen Tabelle 2: Legierungszusammensetzung der erfindungsgemäßen Legierungen und der Vergleichslegierungen in Gew. % Bild 1: Gefügeaufnahme eines erfindungsgemäß hergestellten Strukturbauteils Bild 2: Gefügeaufnahme eines Strukturbauteils nach dem Stand der Technik Bild 3: Profilquerschnitt des untersuchten Strukturbauteils Show it: Table 1: Heat treatment and technological properties for four types of alloys according to the invention and two comparative alloys Table 2: Alloy composition of the alloys according to the invention and of the comparative alloys in% by weight Image 1: Microstructure of a structural component produced according to the invention Picture 2: Microstructure of a structural component according to the prior art Picture 3: Profile cross-section of the examined structural component

Es wurden sechs verschiedene Hohlprofile (Versuchsnummer I bis VI) mit den in Tabelle 1 angegebenen Homogenisierungsbedingungen durch Strangpressen hergestellt und anschließend wärmebehandelt.Six different hollow profiles (test numbers I to VI) with the homogenization conditions specified in Table 1 were produced by extrusion and subsequently heat-treated.

Die technologischen Eigenschaften wurden an Probenstäben gemessen und in Tabelle 1 aufgelistet.The technological properties were measured on specimen rods and listed in Table 1.

Die erfindungsgemäßen Hohlprofile (Versuchsnummern III, IV, V und VI) zeigten gute Verformungs- und Korrosionseigenschaften bei erhöhter Festigkeit und akzeptablen Dehnungswerten.The hollow sections according to the invention (test numbers III, IV, V and VI) showed good deformation and corrosion properties with increased strength and acceptable elongation values.

Die besonderen Eigenschaften beruhen darauf, dass während der Wärmebehandlung die intermetallischen Phasen des Typs Mg2Si, Al3Fe, Al2Cu eingeformt wurden, so dass globulitisch geformte Partikel ≤ 1µ in gleichmäßiger Verteilung vorlagen. Dies zeigt die Gefügeaufnahme Bild 1 für ein erfindungsgemäß hergestelltes Hohlprofil der Legierung V1 gemäß Tabelle 2.The special properties are based on the fact that the intermetallic phases of the type Mg 2 Si, Al 3 Fe, Al 2 Cu were formed during the heat treatment, so that globulitic particles ≤ 1μ were uniformly distributed. This is shown by the micrograph Figure 1 for a hollow profile of the invention produced according to the invention V1 according to Table 2.

Im Vergleich dazu wurde ein Hohlprofil nach dem Stand der Technik hergestellt, wobei die Legierung B1 einen Mg-Unterschuss aufwies. Die genaue Zusammensetzung der Legierungsbeispiele ist Tabelle 2 zu entnehmen.In comparison, a hollow profile according to the prior art was produced, wherein the alloy B1 had a Mg deficit. The exact composition of the alloy examples is shown in Table 2.

Das nach dem Stand der Technik durch Wärmebehandlung auf den Zustand T6 hergestellte Hohlprofil mit Mg-Unterschuss nach Versuchsnummer I zeigt ein deutlich schlechteres Verformungsverhalten. Die Ursache hierfür liegt in den nadelförmigen bis plattenförmigen Strukturen der intermetallischen Verbindungen, wie die Gefügeaufnahme Bild 2 erkennen lässt.The hollow profile produced according to the prior art by heat treatment to the state T6 with Mg deficit according to test number I shows a significantly poorer deformation behavior. The reason for this lies in the needle-shaped to plate-shaped structures of the intermetallic compounds, as the micrograph of Figure 2 shows.

Zusammenfassend lässt sich feststellen, dass nur durch die Kombination der erfindungsgemäßen Legierungsvarianten V1 - V4 mit den Verfahrensmaßnahmen gemäß Patentanspruch 4, die Lösung der vorliegenden Aufgabenstellung möglich ist. Wie die Versuchsauswertung zeigt, ist es gelungen, die Zugfestigkeiten oberhalb von 300 MPa einzustellen. Dies ist in erster Linie durch entsprechende Gehalte an den Legierungselementen Si, Mg und Cu zu erklären. Mit steigendem Si- und Mg-Gehalt verschlechtert sich das Verformungsverhalten. Durch die Zugabe von Cu und der Temperaturführung während des Fertigungsprozesses konnte gutes Stauchverhalten des Materials beibehalten werden. Tabelle 1: Wärmebehandlung und technologische Eigenschaften Hohlprofil Versuchs Nr. Legierung HO Wärme- behandlung Rm* [MPa] Rp0,2 [MPa] A [%] Stauchverhalten** Korrosions- verhalten*** I B1 **** **** 260 220 11 10 i.O. II C1 580°C/3h 190°C/340min 280 270 14 10 i.O. III Leg. V1 580°C/3h 160°C/1700min 318 286 14 6 i.O. IV Leg. V2 560°C/10h 160°C/1700min 322 290 16 6 i.O. V Leg. V3 580°C/3h 240°C/190min 320 290 12 9 i.O. VI Leg. V4 560°C/10h 240°C/190min 310 305 10 9 i.O. * Technologische Eigenschaften gemessen an Probenstäben entnommen aus Mehrkammerhohlprofilen gemäß Bild 4.
** Bewertung 1 bis 10 des Stauchverhaltens nach J. Roysted et. al.: "AIMgSi-alloys with improved Crush Properties", Extrusion Technologie 2008, Orlando.
1 : starke Rissbildung, Abfallen einzelner Profilteile 10: keine Risse, keine Orangenhaut
*** Korrosionstest analog zu DIN 50 905 (Prüfvorschrift nach Fa.Honsel)
**** wärmebehandelt auf den Zustand T6 Tabelle 2: Legierungszusammensetzung in Gew.% Si Mg Mn Fe Cu Ti Cr B1 0,57 0,39 0,15 0,20 - 0,01 - C1 0,48 0,47 0,03 0,19 0,20 0,013 - Leg. V1 0,41 0,86 0,07 0,22 0,16 0,016 0,015 Leg. V2 0,48 0,81 0,06 0,27 0,22 0,015 - Leg. V3 0,51 0,85 0,09 0,12 0,18 0,014 - Leg. V4 0,45 0,84 0,07 0,21 0,24 0,06 - In summary, it can be stated that only by combining the inventive alloy variants V1-V4 with the method measures according to claim 4, the solution of the present task is possible. As the test evaluation shows, it has been possible to set the tensile strengths above 300 MPa. This can be explained primarily by corresponding contents of the alloying elements Si, Mg and Cu. With increasing Si and Mg content, the deformation behavior deteriorates. Through the addition of Cu and the temperature control during the manufacturing process, good compression behavior of the material could be maintained. Table 1: Heat treatment and technological properties Hollow profile experiment no. alloy HO Heat treatment Rm * [MPa] Rp0.2 [MPa] A [%] Crushing performance ** Corrosive behavior *** I B1 **** **** 260 220 11 10 iO II C1 580 ° C / 3h 190 ° C / 340min 280 270 14 10 iO III Leg. V1 580 ° C / 3h 160 ° C / 1700min 318 286 14 6 iO IV Leg. V2 560 ° C / 10h 160 ° C / 1700min 322 290 16 6 iO V Leg. V3 580 ° C / 3h 240 ° C / 190min 320 290 12 9 iO VI Leg. V4 560 ° C / 10h 240 ° C / 190min 310 305 10 9 iO * Technological properties measured on specimen rods taken from multi-chamber hollow profiles according to Fig. 4.
** Rating 1 to 10 of the compression behavior according to J. Roysted et. al .: "AIMgSi-alloys with improved Crush Properties", Extrusion Technology 2008, Orlando.
1: severe cracking, falling off of individual profile parts 10: no cracks, no orange peel
*** Corrosion test analogous to DIN 50 905 (test specification according to the company Honsel)
**** heat treated to the state T6 Si mg Mn Fe Cu Ti Cr B1 0.57 0.39 0.15 0.20 - 0.01 - C1 0.48 0.47 0.03 0.19 0.20 0,013 - Leg. V1 0.41 0.86 0.07 0.22 0.16 0.016 0,015 Leg. V2 0.48 0.81 0.06 0.27 0.22 0,015 - Leg. V3 0.51 0.85 0.09 0.12 0.18 0,014 - Leg. V4 0.45 0.84 0.07 0.21 0.24 0.06 -

Überraschender Weise zeigten die nach dem erfindungsgemäßen Verfahren hergestellten Strukturbauteile eine Verbesserung der Kerbschlagzähigkeit. Dies wurde insbesondere an den Legierungen der Versuchs-Nr. V und VI festgestellt, deren Ergebnisse bei den Kerbschlagversuchen um mehr als 10% über den Vergleichswerten der Versuche III. und IV. und um mehr als 20% über den Werten der Versuche I. und II. lagen.Surprisingly, the structural components produced by the process according to the invention showed an improvement in notched impact strength. This was especially true of the alloys of the experiment no. V and VI whose results in the notched-bar impact tests exceeded by more than 10% over the comparative values of tests III. and IV. and more than 20% above the values of experiments I. and II.

Claims (7)

Korrosionsbeständiges Strangpressprofil aus einer AISiMg-Legierung, vorzugsweise Mehrkammerhohlprofil, gekennzeichnet durch folgende Legierungszusammensetzung in Gew.% Si 0,3 - 0,6% Mg 0,8 - 1,2% Mn 0,03 - 0,1% Fe 0,1 - 0,3% Cu 0,1 - 0,3%
sowie wahlweise Ti 0,01 - 0,12% Cr 0,01 - 0,12%
Rest Reinaluminium mit den herstellungsbedingten Verunreinigungen.Corrosion-resistant extruded profile of an AISiMg alloy, preferably multi-chamber hollow profile, characterized by the following alloy composition in% by weight Si 0.3 - 0.6% mg 0.8 - 1.2% Mn 0.03 - 0.1% Fe 0.1 - 0.3% Cu 0.1 - 0.3%
as well as optional Ti 0.01 - 0.12% Cr 0.01 - 0.12%
Remaining pure aluminum with the production-related impurities. Strangpressprofil nach Anspruch 1, gekennzeichnet durch Si 0,40 - 0,60% Mg 0,82 - 0,90% Cu 0,15 - 0,25%.
Extruded profile according to claim 1, characterized by Si 0.40 - 0.60% mg 0.82 - 0.90% Cu 0.15-0.25%.
Strangpressprofil nach einem der vorhergehenden Ansprüche, gekennzeichnet durch eine Gefügestruktur mit eingeformten intermetallischen Phasen des Typs alpha-AlFeSi, beta-AlFeSi, Al15FeMn3Si2, Mg2Si, theta-AlCu, wobei die Partikel aus intermetallischen Phasen globulistisch geformt sind und einen Durchmesser ≤ 1µm aufweisen.Extruded section according to one of the preceding claims, characterized by a microstructure with molded intermetallic phases of the type alpha-AlFeSi, beta-AlFeSi, Al15FeMn 3 Si 2 , Mg 2 Si, theta-AlCu, wherein the particles of intermetallic phases are globulistically shaped and have a diameter Have ≤ 1μm. Strangpressprofil nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass das Gew.-Verhältnis von Magnesium zu Silizium in der Legierungszusammensetzung im Bereich von 1 bis 2 liegt.Extruded section according to one of the preceding claims, characterized in that the weight ratio of magnesium to silicon in the alloy composition is in the range of 1 to 2. Verfahren zur Herstellung eines Strangpressprofils gemäß einem der vorhergehenden Ansprüche durch Stranggießen, Homogenisierung und einer dem Strangpressen unmittelbar anschließenden Wärmebehandlung, dadurch gekennzeichnet, dass die Homogenisierung zwischen 450°C und 600°C für 1 bis 10 Stunden durchgeführt wird und dann nach dem Strangpressen eine Wärmebehandlung im Bereich von 160°C bis 260°C für 20 bis 1800 Minuten erfolgt.A method for producing an extruded profile according to any one of the preceding claims by continuous casting, homogenization and a heat treatment immediately following the extrusion, characterized in that the homogenization between 450 ° C and 600 ° C is carried out for 1 to 10 hours and then after extrusion a heat treatment in the range of 160 ° C to 260 ° C for 20 to 1800 minutes. Verfahren nach den vorhergehenden Ansprüchen, dadurch gekennzeichnet, dass die Wärmebehandlung nach dem Strangpressen bei einer Temperatur von 180°C bis 250°C für 100 bis 1000 Minuten erfolgt.Method according to the preceding claims, characterized in that the heat treatment after extrusion at a temperature of 180 ° C to 250 ° C for 100 to 1000 minutes. Verfahren nach den vorhergehenden Ansprüchen, dadurch gekennzeichnet, dass vor dem Stranggießen die Schmelze einen H2-Gehalt < 0,15 ccm/100gr. AI aufweist.Process according to the preceding claims, characterized in that before the continuous casting, the melt has an H 2 content <0.15 ccm / 100gr. AI has.
EP20090011984 2008-09-22 2009-09-21 Corrosion-resistant aluminium extrusion profile and method for manufacturing a structure component Active EP2175042B1 (en)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
DE200810048374 DE102008048374B3 (en) 2008-09-22 2008-09-22 Corrosion-resistant extruded aluminum profile and method for producing a structural component

Publications (2)

Publication Number Publication Date
EP2175042A1 true EP2175042A1 (en) 2010-04-14
EP2175042B1 EP2175042B1 (en) 2015-03-04

Family

ID=41557521

Family Applications (1)

Application Number Title Priority Date Filing Date
EP20090011984 Active EP2175042B1 (en) 2008-09-22 2009-09-21 Corrosion-resistant aluminium extrusion profile and method for manufacturing a structure component

Country Status (3)

Country Link
EP (1) EP2175042B1 (en)
DE (1) DE102008048374B3 (en)
ES (1) ES2537781T3 (en)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103060634A (en) * 2012-12-31 2013-04-24 张家港市金邦铝业有限公司 Light high-strength aluminum ladder section
US9970090B2 (en) 2012-05-31 2018-05-15 Rio Tinto Alcan International Limited Aluminum alloy combining high strength, elongation and extrudability
US10661338B2 (en) 2010-04-26 2020-05-26 Hydro Extruded Solutions Ab Damage tolerant aluminium material having a layered microstructure
US11345980B2 (en) 2018-08-09 2022-05-31 Apple Inc. Recycled aluminum alloys from manufacturing scrap with cosmetic appeal
EP3938554B1 (en) 2019-03-13 2023-09-06 Novelis, Inc. Age-hardenable and highly formable aluminum alloys, monolithic sheet made therof and clad aluminum alloy product comprising it
WO2024099379A1 (en) * 2022-11-09 2024-05-16 北京车和家汽车科技有限公司 Aluminum alloy material, and preparation method therefor and use thereof

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2841611B1 (en) 2012-04-25 2018-04-04 Norsk Hydro ASA Extruded profile of Al-Mg-Si aluminium alloy with improved properties

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3104189A (en) * 1960-10-17 1963-09-17 Reynolds Metals Co Aluminum alloy system
US5223050A (en) * 1985-09-30 1993-06-29 Alcan International Limited Al-Mg-Si extrusion alloy
JPH11181539A (en) 1997-12-22 1999-07-06 Sumitomo Light Metal Ind Ltd Aluminum alloy extruded material excellent in intergranular corrosion resistance, and its production
CA2266193A1 (en) 1998-03-20 1999-09-20 Alcan International Limited Extrudable aluminum alloys
JP2000282162A (en) 1999-03-30 2000-10-10 Nippon Steel Corp Aluminum alloy extruded material excellent in corrosion fatigue strength
WO2002038821A1 (en) * 2000-11-08 2002-05-16 Norsk Hydro Asa A method for producing formed products of an aluminium alloy and the use of such products
US6565984B1 (en) * 2002-05-28 2003-05-20 Applied Materials Inc. Clean aluminum alloy for semiconductor processing equipment
EP1808240A1 (en) * 2004-10-25 2007-07-18 Showa Denko Kabushiki Kaisha Continuous casting apparatus, continuous casting method, and aluminum aloy cast rod

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3370943A (en) * 1965-11-04 1968-02-27 Kaiser Aluminium Chem Corp Aluminum alloy
DE69907032T2 (en) * 1999-02-12 2003-12-24 Norsk Hydro As ALUMINUM ALLOY CONTAINING MAGNESIUM AND SILICON
DE102004030021B4 (en) * 2003-07-09 2009-11-26 Aleris Aluminum Duffel Bvba Rolled product

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3104189A (en) * 1960-10-17 1963-09-17 Reynolds Metals Co Aluminum alloy system
US5223050A (en) * 1985-09-30 1993-06-29 Alcan International Limited Al-Mg-Si extrusion alloy
JPH11181539A (en) 1997-12-22 1999-07-06 Sumitomo Light Metal Ind Ltd Aluminum alloy extruded material excellent in intergranular corrosion resistance, and its production
CA2266193A1 (en) 1998-03-20 1999-09-20 Alcan International Limited Extrudable aluminum alloys
CA2266193C (en) * 1998-03-20 2005-02-15 Alcan International Limited Extrudable aluminum alloys
JP2000282162A (en) 1999-03-30 2000-10-10 Nippon Steel Corp Aluminum alloy extruded material excellent in corrosion fatigue strength
WO2002038821A1 (en) * 2000-11-08 2002-05-16 Norsk Hydro Asa A method for producing formed products of an aluminium alloy and the use of such products
US6565984B1 (en) * 2002-05-28 2003-05-20 Applied Materials Inc. Clean aluminum alloy for semiconductor processing equipment
EP1808240A1 (en) * 2004-10-25 2007-07-18 Showa Denko Kabushiki Kaisha Continuous casting apparatus, continuous casting method, and aluminum aloy cast rod

Non-Patent Citations (5)

* Cited by examiner, † Cited by third party
Title
CHOU C Y ET AL: "Effects of heat treatments on AA6061 aluminum alloy deformed by cross-channel extrusion", JOURNAL OF MATERIALS PROCESSING TECHNOLOGY, ELSEVIER, NL, vol. 202, no. 1-3, 20 June 2008 (2008-06-20), pages 1 - 6, XP022639866, ISSN: 0924-0136, [retrieved on 20071123] *
COUPER, M. J. ET AL: "Effect of homogenization temperature and time on billet microstructure and extruded properties of alloy 6061", ALUMINIUM CAST HOUSE TECHNOLOGY, AUSTRALIAN ASIAN PACIFIC CONFERENCE, 7TH, HOBART, AUSTRALIA, SEPT. 23-26, 2001 , 287-296. EDITOR(S): WHITELEY, PETER R. PUBLISHER: MINERALS, METALS & MATERIALS SOCIETY, WARRENDALE, PA. CODEN: 69BVQJ, 2001, XP009128629 *
M. J. COUPER ET AL., EFFECT OF HOMOGENISATION TEMPERATURE AND TIME ON BILLET MICROSTRUCTURE AND EXTRUDED PROPERTIES OF ALLOY 6061
N.C. PARSON ET AL., THE EFFECT OF HEAT TREATMENT ON THE MICROSTRUCTURE AND PROPERTIES OF 6000 SERIES ALLOY EXTRUSION INGOTS
PARSON, N. C. ET AL: "The effect of heat treatment on the microstructure and properties of 6000 series alloy extrusion ingots", LIGHT METALS (WARRENDALE, PA, UNITED STATES) 713-24 CODEN: LMPMDF; ISSN: 0147-0809, 1989, XP009128616 *

Cited By (6)

* 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
US9970090B2 (en) 2012-05-31 2018-05-15 Rio Tinto Alcan International Limited Aluminum alloy combining high strength, elongation and extrudability
CN103060634A (en) * 2012-12-31 2013-04-24 张家港市金邦铝业有限公司 Light high-strength aluminum ladder section
US11345980B2 (en) 2018-08-09 2022-05-31 Apple Inc. Recycled aluminum alloys from manufacturing scrap with cosmetic appeal
EP3938554B1 (en) 2019-03-13 2023-09-06 Novelis, Inc. Age-hardenable and highly formable aluminum alloys, monolithic sheet made therof and clad aluminum alloy product comprising it
WO2024099379A1 (en) * 2022-11-09 2024-05-16 北京车和家汽车科技有限公司 Aluminum alloy material, and preparation method therefor and use thereof

Also Published As

Publication number Publication date
EP2175042B1 (en) 2015-03-04
DE102008048374B3 (en) 2010-04-15
ES2537781T3 (en) 2015-06-12

Similar Documents

Publication Publication Date Title
EP2770071B9 (en) Aluminium alloy for the production of semi-finished products or components for motor vehicles, method for producing an aluminium alloy strip from this aluminium alloy and aluminium alloy strip and uses thereof
DE69703441T3 (en) SURFACE OR STRUCTURED PART OF ALUMINUM MAGNESIUM ALLOY
EP3314031B1 (en) High strength and easily reformable almg tape and method for producing the same
AT502294B1 (en) AL-ZN KNET ALLOY AND USE OF SUCH ALLOY
EP2829624B1 (en) Aluminium material with improved precipitation hardening
EP2175042B1 (en) Corrosion-resistant aluminium extrusion profile and method for manufacturing a structure component
EP2449145B1 (en) AlMgSi-sheet for applications with high shaping requirements
EP1718778B1 (en) Material based on an aluminum alloy, method for the production thereof and its use
EP2570509B1 (en) Production method for AlMgSi-aluminium strip
DE69825414T2 (en) Aluminum alloy and process for its preparation
DE112015000499T5 (en) Plastic deformed aluminum alloy product, process for producing the same and automobile component
DE10329899B3 (en) Beta titanium alloy, process for producing a hot rolled product from such alloy and its uses
DE102011112005A1 (en) Alloy, preferably aluminum casting alloy, useful e.g. as a sand or die casting alloy, comprises a specified range of silicon, zinc, iron, copper, magnesium, strontium, sodium, antimony and aluminum
EP1458898A1 (en) Hot- and cold-formed aluminium alloy
DE10231437B4 (en) Process for producing an aluminum wrought alloy product
DE3486352T2 (en) Aluminum-lithium alloy.
DE2510087C2 (en) Use of a cold-deformable aluminum-magnesium-zinc alloy
EP1748088B1 (en) Process for producing a semi-finished product or component for chassis or structural automotive applications
EP0517087B1 (en) Method for manufacturing copper alloys
DE19832489A1 (en) Wrought aluminium-magnesium-silicon alloy
AT512120B1 (en) ALUMINUM ALLOY WITH TANTAL
EP3970964A1 (en) Aluminum composite for crash applications
EP3981893A1 (en) Plate made of a rolled aluminium alloy and production of such a plate
DE102021131935A1 (en) Die-cast aluminum alloy
DE10310453A1 (en) Die-cast component and process for its manufacture

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

17P Request for examination filed

Effective date: 20090921

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): 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 SE SI SK SM TR

AX Request for extension of the european patent

Extension state: AL BA RS

17Q First examination report despatched

Effective date: 20100616

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: HONSEL AG

Owner name: TRIMET ALUMINIUM SE

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: MARTINREA HONSEL GERMANY GMBH

Owner name: TRIMET ALUMINIUM SE

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20140922

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): 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 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: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 713981

Country of ref document: AT

Kind code of ref document: T

Effective date: 20150415

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502009010690

Country of ref document: DE

Effective date: 20150416

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2537781

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20150612

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20150304

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

Ref country code: SE

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

Effective date: 20150304

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: 20150604

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: 20150304

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: 20150304

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: 20150304

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: 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: 20150304

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: 20150605

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 7

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: 20150304

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

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: 20150706

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: 20150304

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: 20150304

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: 20150304

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

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: 20150304

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: 20150704

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502009010690

Country of ref document: DE

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

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

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: 20150304

26N No opposition filed

Effective date: 20151207

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: 20150304

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

Ref country code: LU

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: 20150921

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: 20150304

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

REG Reference to a national code

Ref country code: DE

Ref legal event code: R081

Ref document number: 502009010690

Country of ref document: DE

Owner name: TRIMET ALUMINIUM SE, DE

Free format text: FORMER OWNERS: MARTINREA HONSEL GERMANY GMBH, 59872 MESCHEDE, DE; TRIMET ALUMINIUM SE, 45356 ESSEN, DE

Ref country code: DE

Ref legal event code: R082

Ref document number: 502009010690

Country of ref document: DE

Representative=s name: FLACCUS MUELLER-WOLFF, DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

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

Ref country code: LI

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

Effective date: 20150930

Ref country code: IE

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

Effective date: 20150921

Ref country code: CH

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

Effective date: 20150930

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 8

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

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: 20150304

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

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: 20150304

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: 20150304

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: 20090921

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: 20150304

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

Ref country code: BE

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

Effective date: 20150930

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

Ref country code: TR

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: 20150304

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 9

REG Reference to a national code

Ref country code: AT

Ref legal event code: PC

Ref document number: 713981

Country of ref document: AT

Kind code of ref document: T

Owner name: TRIMET ALUMINIUM SE, DE

Effective date: 20170907

REG Reference to a national code

Ref country code: ES

Ref legal event code: PC2A

Owner name: TRIMET ALUMINIUM SE

Effective date: 20171017

REG Reference to a national code

Ref country code: GB

Ref legal event code: 732E

Free format text: REGISTERED BETWEEN 20171109 AND 20171115

REG Reference to a national code

Ref country code: FR

Ref legal event code: TP

Owner name: TRIMET ALUMINIUM SE, DE

Effective date: 20171207

Ref country code: FR

Ref legal event code: TQ

Owner name: TRIMET ALUMINIUM SE, DE

Effective date: 20171207

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: 20150304

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 10

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

Ref country code: GB

Payment date: 20230920

Year of fee payment: 15

Ref country code: CZ

Payment date: 20230912

Year of fee payment: 15

Ref country code: AT

Payment date: 20230921

Year of fee payment: 15

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

Ref country code: FR

Payment date: 20230928

Year of fee payment: 15

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

Ref country code: ES

Payment date: 20231123

Year of fee payment: 15

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

Ref country code: IT

Payment date: 20230927

Year of fee payment: 15

Ref country code: DE

Payment date: 20231115

Year of fee payment: 15