EP3072984B1 - Al-cu-mg-li alloy and alloy product produced from same - Google Patents

Al-cu-mg-li alloy and alloy product produced from same Download PDF

Info

Publication number
EP3072984B1
EP3072984B1 EP15161219.9A EP15161219A EP3072984B1 EP 3072984 B1 EP3072984 B1 EP 3072984B1 EP 15161219 A EP15161219 A EP 15161219A EP 3072984 B1 EP3072984 B1 EP 3072984B1
Authority
EP
European Patent Office
Prior art keywords
alloy
weight
content
strength
product
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
EP15161219.9A
Other languages
German (de)
French (fr)
Other versions
EP3072984A1 (en
EP3072984B2 (en
Inventor
Tina Schlingmann
Joachim Becker
Thomas Witulski
Abi D. Dehbozorgi
Mark Timko
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.)
Otto Fuchs KG
Original Assignee
Otto Fuchs KG
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
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=52807628&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP3072984(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Otto Fuchs KG filed Critical Otto Fuchs KG
Priority to EP15161219.9A priority Critical patent/EP3072984B2/en
Priority to ES15161219T priority patent/ES2642118T5/en
Publication of EP3072984A1 publication Critical patent/EP3072984A1/en
Application granted granted Critical
Publication of EP3072984B1 publication Critical patent/EP3072984B1/en
Publication of EP3072984B2 publication Critical patent/EP3072984B2/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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22F1/057—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 copper as the next major constituent

Definitions

  • the invention relates to an Al-Cu-Mg-Li alloy and an alloy product produced therefrom.
  • High-performance aluminum alloy components are an indispensable component of aircraft design in many cases. Components of such high-performance aluminum alloys are used among other things in the fuselage and in the wing as structural components. These parts are forged, extruded parts. These must meet the necessary combination of static and dynamic strength and have certain requirements in terms of tensile strength, yield strength, elongation at break and crack toughness (K 1C and stress corrosion cracking). In addition, the weight plays a not insignificant role in components used in the aerospace industry. Thus, the specific gravity (density) of the high performance alloy used is also relevant.
  • Al-Cu-Mg-Li alloy meeting these requirements is the aluminum alloy AA 2195.
  • This alloy has a composition of 3.7-4.3% by weight of Cu, 0.25%. 0.8% by weight of Mg, 0.8-1.2% by weight of Li, 0.25-0.6% by weight of Ag, max. 0.25% by weight of Zn, max. 0.25% by weight of Mn, max. 0.12% by weight of Si, max. 0.15 wt.% Fe, max. 0.1% by weight of Ti and 0.08-0.16% by weight of Zr.
  • the components made from this alloy have a density of about 2.7 g / cm 3.
  • the aluminum alloy AA 2050 is an example of such a high-performance alloy, which replaced the alloy 2195, from which often components were previously made in the aviation sector in the meantime.
  • the alloy AA 2050 has a Cu content of 3.2-3.9% by weight, a Li content from 0.7 to 1.3 wt%, an Mn content of 0.2 to 0.8 wt%, and a Mg content of 0.1 to 0.5 wt%.
  • Zn is usually involved in the construction of the alloy with up to 0.25 wt .-%.
  • silver is alloyed in this alloy in amounts of 0.2-0.7% by weight. This measure accounts for the prevailing opinion that silver is a necessary alloying component especially in lithium-containing Al-Cu alloys for achieving high strengths of components made therefrom.
  • An alloy with an even higher Li content similar to the AA 2050 alloy, is the alloy AA 2196 with a Li content of 1.4-2.1% by weight.
  • the Cu content of this alloy is slightly reduced compared to the Cu content in the 2050 alloy. From this alloy, however, only components with a lower strength can be produced compared to components that can be made of the AA 2050 alloy.
  • Previously known Ag-containing high-performance aluminum alloys such as the AA 2050 alloy, contain Mn as a necessary alloying element.
  • the AA 2050 alloy requires a Mn content of 0.2-0.5 wt%.
  • Mn in a recrystallization inhibitor Mainly due to the latter property, Mn is an element necessary for achieving the desired strength properties.
  • This also corresponds to the prevailing opinion that in Ag-containing Al-Cu-Mg-Li alloys at least 0.2 wt .-% Mn, if not significantly more involved in the construction of the alloy must be.
  • care must be taken to ensure that the Mn content is not so high that coarse primary solidification does not form in the microstructure, which in particular adversely affects the fatigue behavior.
  • Such a high-performance aluminum alloy must contain enough Mn to fulfill the desired property as a recrystallization inhibitor. These requirements meet the previously known alloys with Mn contents, such as in the AA 2050 between 0.2 and 0.5 wt .-%.
  • the Mn content information given in the prior art high-performance aluminum alloys containing Ag and Li has a relatively large margin. It depends largely on the participation of others Alloy elements Cu, Li, Mg, Mn, Ti, Zr, Si, Fe and Ag from whether a selected Mn content from the specified range can actually be melted an alloy from which components can be produced that meet the specified strength requirements and fatigue and toughness are sufficient.
  • the invention is based on the above-appreciated prior art, the task of proposing an Ag and Li-containing Al-Cu alloy, which is not only simplified in terms of their construction compared to prior art alloys, but in which is also ensured that within the specified spectrum of the alloying elements components produced therefrom after appropriate heat treatment satisfy the desired combination of mechanical properties.
  • All alloy compositions described in this embodiment may contain unavoidable impurities per element of 0.05% by weight, the total amount of impurities should not exceed 0.15% by weight. However, it is preferable to keep the impurity as low as possible and not to exceed 0.03 wt% per element at a total amount of 0.08 wt%.
  • This Ag and Li-containing high-performance aluminum alloy has a particularly narrow range of its alloying elements. This is especially true for the alloying element Mn, which not only in A very narrow spectrum, but also with surprisingly small proportions in the structure of the alloy is involved and fulfills the functions intended for this element. It should be pointed out in this context that this alloy is Zn-free. It was surprising to find that in this alloy having an Mn content as small as that required in the AA 2050 alloy, it is sufficient to effectively prevent recrystallization. In addition, care is taken within the stated range of 0.01% by weight to ⁇ 0.2% by weight that no or only to a significant extent primary phases are formed which would impair fatigue and toughness.
  • a component has extremely strong properties if the yield strength R p0.2 is at least 600 MPa.
  • a component is said to have high strength properties if the yield strength R p0.2 is at least 500 MPa.
  • the necessary strength does not appear in combination with the other alloying elements. Copper contents above 3.9 wt.% In the alloy are unable to further increase the strength of a component made from the alloy. On the contrary, it is to be expected that at higher Cu contents property-damaging phases form.
  • Lithium is included to reduce the density (specific gravity) in the alloy.
  • the lithium content is adapted to the Cu and Mg contents of the alloy in such a way that as much as possible Lithium is incorporated into the alloy, but only so much that this can be brought into solution and no unwanted Li-containing phases. Therefore, the Li content of the alloy is limited to the narrow range between 0.9 and 1.3 wt%.
  • Magnesium contributes to the desired properties of a component made of the alloy, but is only permitted with one share, so that no undesirable phases (such as an S phase Al 2 CuMg) form. Taking into account the further alloying elements, the Mg content should not exceed 0.45% by weight.
  • Titanium acts as a grain refiner in the cast structure and zirconium as a dispersoid former and thus contributes to the inhibition of recrystallization.
  • an Mn content of between 0.10 and 0.18 wt .-% is sufficient to effectively prevent recrystallization. This is attributed to the specific and targeted selection of the share and the range of Mn as well as the very limited Mn content. This ensures that within these limits can be consistently set the desired combination of mechanical properties in a made of the alloy component. If the Mn content exceeds 0.18% by weight, taking into account the other alloying elements, this may already lead to coarser primary solidifications in the microstructure, which in turn was not to be expected in accordance with prevailing opinion. Finally, in the alloy AA 2050, an Mn content of 0.2-0.8 wt% is proposed.
  • the Mn content of the claimed alloy is limited to a maximum amount of 0.18 wt%. If no primary solidification in the microstructure is to be accepted, the Mn content is limited to a range of 0.10-0.15% by weight at the top. Particularly good results can be achieved if the Mn content is between 0.10 and 0.12 wt .-%.
  • the Ag content is included to increase the strength in this alloy.
  • the Ag content is chosen to be slightly lower or slightly more within the claimed limit of between 0.2 and 0.45 wt%.
  • the Ag content should be more than 0.35 wt .-%.
  • a preferred contribution of the Ag content to the construction of the alloy is from 0.38 to 0.43 wt%.
  • the alloy is preferably Fe-free.
  • dispersion-forming elements have Mn + Fe + Si ⁇ 0.3% by weight.
  • alloys according to the invention were melted as reference alloy on a laboratory scale by casting into random billets.
  • the molten alloys have the following composition, wherein the alloy XL33 is the alloy according to the invention, while the alloy AA 2050 has been melted as a reference alloy: alloy Cu Li mg Mn Ti Zr Si Fe Ag XL33 3.78 0.90 0.35 0.11 0,052 0.112 0.02 0.02 0.404 AA 2050 3.72 0.94 0.31 0.38 0.40 0.092 0.04 0.063 0.491
  • the cast billets were homogenized, extruded and solution annealed as profiles and then stretched longitudinally by about 2-4%.
  • the hot aging was carried out at 153 ° C for 48 hours.
  • studies have been carried out to determine the yield strength R p0,2, the tensile strength R m, the elongation at break A 5 as well as the fracture toughness. The tests were carried out on the specimens in the same places.
  • a component made of this alloy is suitable as a component for use in the aerospace industry, especially for structural components, due to the properties described above.
  • components made of this alloy can also be made and used for other applications, especially if a low density should also play a role.

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)
  • Conductive Materials (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Powder Metallurgy (AREA)

Description

Die Erfindung betrifft eine Al-Cu-Mg-Li-Legierung sowie ein daraus hergestelltes Legierungsprodukt.The invention relates to an Al-Cu-Mg-Li alloy and an alloy product produced therefrom.

Bauteile aus Hochleistungsaluminiumlegierungen sind in vielen Fällen unverzichtbarer Bestandteil bei der Konstruktion von Flugzeugen. Bauteile aus derartigen Hochleistungsaluminiumlegierungen werden unter anderem im Rumpf und im Flügel als Strukturbauteile eingesetzt. Bei diesen Teilen handelt es sich um geschmiedete, stranggepresste Teile. Diese müssen der notwendigen Kombination aus statischer und dynamischer Festigkeit genügen und bestimmte Anforderungen in Bezug auf Zugfestigkeit, Dehngrenze, Bruchdehnung und Risszähigkeit (K1C und Spannungsrisskorrosion) aufweisen. Zudem spielt das Gewicht bei Bauteilen, die für die Luft- und Raumfahrtindustrie eingesetzt werden, eine nicht unbedeutende Rolle. Somit ist auch das spezifische Gewicht (die Dichte) der verwendeten Hochleistungslegierung von Relevanz.High-performance aluminum alloy components are an indispensable component of aircraft design in many cases. Components of such high-performance aluminum alloys are used among other things in the fuselage and in the wing as structural components. These parts are forged, extruded parts. These must meet the necessary combination of static and dynamic strength and have certain requirements in terms of tensile strength, yield strength, elongation at break and crack toughness (K 1C and stress corrosion cracking). In addition, the weight plays a not insignificant role in components used in the aerospace industry. Thus, the specific gravity (density) of the high performance alloy used is also relevant.

Eine am Markt eingeführte Al-Cu-Mg-Li-Legierung, die diesen Anforderungen genügt, ist die Aluminium-Legierung AA 2195. Diese Legierung hat eine Zusammensetzung von 3,7 - 4,3 Gew.-% Cu, 0,25 - 0,8 Gew.-% Mg, 0,8 - 1,2 Gew.% Li, 0,25 - 0,6 Gew.% Ag, max. 0,25 Gew.-% Zn, max. 0,25 Gew.-% Mn, max. 0,12 Gew.-% Si, max. 0,15 Gew.-% Fe, max. 0,1 Gew.-% Ti und 0,08 - 0,16 Gew.% Zr. Die aus dieser Legierung hergestellten Bauteile haben eine Dichte von etwa 2,7 g/cm3.A marketed Al-Cu-Mg-Li alloy meeting these requirements is the aluminum alloy AA 2195. This alloy has a composition of 3.7-4.3% by weight of Cu, 0.25%. 0.8% by weight of Mg, 0.8-1.2% by weight of Li, 0.25-0.6% by weight of Ag, max. 0.25% by weight of Zn, max. 0.25% by weight of Mn, max. 0.12% by weight of Si, max. 0.15 wt.% Fe, max. 0.1% by weight of Ti and 0.08-0.16% by weight of Zr. The components made from this alloy have a density of about 2.7 g / cm 3.

Mit zunehmender Größe der Flugzeuge geht das Bestreben einher, in Ergänzung zu einer hohen Festigkeit die Bauteile mit einem besseren damage tolerant Verhalten zu versehen. Entwickelt worden sind, um dieser Anforderung zu genügen, ausgehend von der Legierung AA 2195, Al-Cu-Mg-Li-Legierungen mit verbesserter Zähigkeit und Schwingfestigkeit. Die Aluminiumlegierung AA 2050 ist ein Beispiel für eine solche Hochleistungslegierung, die die Legierung 2195, aus der zuvor oftmals Bauteile gefertigt wurden, im Luftfahrtbereich zwischenzeitlich ersetzt. Die Legierung AA 2050 weist einen Cu-Anteil von 3,2 - 3,9 Gew.-%, einen Li-Gehalt von 0,7 - 1,3 Gew.-%, einen Mn-Gehalt von 0,2 - 0,8 Gew.-% und einen Mg-Gehalt von 0,1 - 0,5 Gew.-% auf. Zn ist üblicherweise am Aufbau der Legierung mit bis zu 0,25 Gew.-% beteiligt. Um die notwendigen Festigkeitseigenschaften zu erzielen, wird bei dieser Legierung Silber zulegiert, und zwar in Gehalten von 0,2 - 0,7 Gew.-%. Durch diese Maßnahme wird der herrschenden Meinung Rechenschaft getragen, dass Silber, gerade bei Lithium-haltigen Al-Cu-Legierungen zum Erzielen hoher Festigkeiten daraus hergestellter Bauteile notwendiger Legierungsbestandteil ist.As the size of the aircraft increases, there is a desire to provide components with better damage tolerant behavior in addition to high strength. Developed to meet this requirement, based on the alloy AA 2195, Al-Cu-Mg-Li alloys with improved toughness and fatigue strength. The aluminum alloy AA 2050 is an example of such a high-performance alloy, which replaced the alloy 2195, from which often components were previously made in the aviation sector in the meantime. The alloy AA 2050 has a Cu content of 3.2-3.9% by weight, a Li content from 0.7 to 1.3 wt%, an Mn content of 0.2 to 0.8 wt%, and a Mg content of 0.1 to 0.5 wt%. Zn is usually involved in the construction of the alloy with up to 0.25 wt .-%. In order to obtain the necessary strength properties, silver is alloyed in this alloy in amounts of 0.2-0.7% by weight. This measure accounts for the prevailing opinion that silver is a necessary alloying component especially in lithium-containing Al-Cu alloys for achieving high strengths of components made therefrom.

Eine der Legierung AA 2050 ähnliche Legierung mit einem noch höheren Li-Anteil ist die Legierung AA 2196 mit einem Li-Anteil von 1,4 - 2.1 Gew.-%. Der Cu-Anteil dieser Legierung ist gegenüber dem Cu-Anteil in der Legierung 2050 geringfügig reduziert. Aus dieser Legierung können jedoch nur Bauteile mit einer geringeren Festigkeit hergestellt werden, verglichen mit Bauteilen, die aus der Legierung AA 2050 hergestellt werden können.An alloy with an even higher Li content, similar to the AA 2050 alloy, is the alloy AA 2196 with a Li content of 1.4-2.1% by weight. The Cu content of this alloy is slightly reduced compared to the Cu content in the 2050 alloy. From this alloy, however, only components with a lower strength can be produced compared to components that can be made of the AA 2050 alloy.

Vorbekannte Ag-haltige Hochleistungsaluminiumlegierungen wie die Legierung AA 2050 beinhalten als notwendiges Legierungselement Mn. Bei der Legierung AA 2050 ist ein Mn-Gehalt von 0,2 - 0,5 Gew.-% erforderlich. Mn in ein Rekristallisationshemmer. Vor allem aufgrund letzterer Eigenschaft ist Mn ein für die Erzielung der gewünschten Festigkeitseigenschaften notwendiges Element. Dieses entspricht auch der herrschenden Meinung, dass bei Ag-haltigen Al-Cu-Mg-Li-Legierungen zumindest 0,2 Gew.-% Mn, wenn nicht deutlich mehr am Aufbau der Legierung beteiligt sein muss. Allerdings ist darauf zu achten, dass der Mn-Gehalt nicht so hoch ist, damit sich keine groben Primärerstarrungen im Mikrogefüge ausbilden, die insbesondere das Ermüdungsverhalten negativ beeinflussen. Insofern darf ein gewisses Maximum nicht überschritten werden. Auf der anderen Seite muss eine solche Hochleistungsaluminiumlegierung genügend Mn enthalten, um die gewünschte Eigenschaft als Rekristallisationshemmer erfüllen zu können. Diesen Anforderungen genügen die vorbekannten Legierungen mit Mn-Gehalten, wie beispielsweise bei der AA 2050 zwischen 0,2 und 0,5 Gew.-%.Previously known Ag-containing high-performance aluminum alloys, such as the AA 2050 alloy, contain Mn as a necessary alloying element. The AA 2050 alloy requires a Mn content of 0.2-0.5 wt%. Mn in a recrystallization inhibitor. Mainly due to the latter property, Mn is an element necessary for achieving the desired strength properties. This also corresponds to the prevailing opinion that in Ag-containing Al-Cu-Mg-Li alloys at least 0.2 wt .-% Mn, if not significantly more involved in the construction of the alloy must be. However, care must be taken to ensure that the Mn content is not so high that coarse primary solidification does not form in the microstructure, which in particular adversely affects the fatigue behavior. In this respect, a certain maximum may not be exceeded. On the other hand, such a high-performance aluminum alloy must contain enough Mn to fulfill the desired property as a recrystallization inhibitor. These requirements meet the previously known alloys with Mn contents, such as in the AA 2050 between 0.2 and 0.5 wt .-%.

Die zu den vorbekannten Hochleistungsaluminiumlegierungen, die Ag und Li enthalten, gemachten Angaben zu dem Mn-Gehalt weisen eine relativ große Spanne auf. Es hängt maßgeblich von der Beteiligung der anderen Legierungselemente Cu, Li, Mg, Mn, Ti, Zr, Si, Fe und Ag ab, ob mit einem ausgewählten Mn-Gehalt aus dem angegebenen Bereich tatsächlich eine Legierung erschmolzen werden kann, aus der Bauteile hergestellt werden können, die den gestellten Festigkeitsanforderungen sowie der Ermüdung und Zähigkeit genügen.The Mn content information given in the prior art high-performance aluminum alloys containing Ag and Li has a relatively large margin. It depends largely on the participation of others Alloy elements Cu, Li, Mg, Mn, Ti, Zr, Si, Fe and Ag from whether a selected Mn content from the specified range can actually be melted an alloy from which components can be produced that meet the specified strength requirements and fatigue and toughness are sufficient.

Der Erfindung liegt ausgehend von dem vorstehend gewürdigten Stand der Technik die Aufgabe zugrunde, eine Ag- und Li-haltige Al-Cu-Legierung vorzuschlagen, die nicht nur hinsichtlich ihres Aufbaus im Vergleich zu vorbekannten Legierungen vereinfacht ist, sondern bei der auch gewährleistet ist, dass innerhalb des angegebenen Spektrums der Legierungselemente daraus hergestellte Bauteile nach entsprechender Wärmebehandlung der gewünschten Kombination mechanischer Eigenschaften genügen.The invention is based on the above-appreciated prior art, the task of proposing an Ag and Li-containing Al-Cu alloy, which is not only simplified in terms of their construction compared to prior art alloys, but in which is also ensured that within the specified spectrum of the alloying elements components produced therefrom after appropriate heat treatment satisfy the desired combination of mechanical properties.

Gelöst wird diese Aufgabe durch eine Al-Cu-Mg-Li-Legierung mit

  • 3,7 - 3,9 Gew.-% Cu,
  • 0,9 - 1,3 Gew.-% Li,
  • 0,30 - 0,45 Gew.-% Mg,
  • 0,10 - < 0,2 Gew.-% Mn,
  • 0,2 - 0,45 Gew.-% Ag,
  • 0,09 - 0,13 Gew.-% Zr,
  • max. 0,07 Gew.-% Ti, wobei das Ti als TiB2 oder TiC vorliegt,
  • Rest Al nebst unvermeidbaren Verunreinigungen.
This object is achieved by an Al-Cu-Mg-Li alloy with
  • 3.7-3.9% by weight of Cu,
  • 0.9-1.3% by weight of Li,
  • 0.30-0.45% by weight Mg,
  • 0.10 - <0.2 wt% Mn,
  • 0.2-0.45% by weight of Ag,
  • 0.09 - 0.13 wt.% Zr,
  • Max. 0.07% by weight of Ti, where the Ti is present as TiB 2 or TiC,
  • Rest Al plus unavoidable impurities.

Bei allen Legierungszusammensetzungen, die im Rahmen dieser Ausführung beschrieben sind, können unvermeidbare Verunreinigungen je Element von 0,05 Gew.-% enthalten sein, wobei die Gesamtmenge an Verunreinigungen 0,15 Gew.-% nicht überschreiten sollte. Es ist jedoch bevorzugt, die Verunreinigung möglichst gering zu halten und einen Anteil von 0,03 Gew.-% je Element bei einer Gesamtmenge von 0,08 Gew.-% nicht zu überschreiten.All alloy compositions described in this embodiment may contain unavoidable impurities per element of 0.05% by weight, the total amount of impurities should not exceed 0.15% by weight. However, it is preferable to keep the impurity as low as possible and not to exceed 0.03 wt% per element at a total amount of 0.08 wt%.

Diese Ag- und Li-haltige Hochleistungsaluminiumlegierung weist eine besonders enge Bandbreite seiner Legierungselemente auf. Dieses gilt in besonderem Maße für das Legierungselement Mn, welches nicht nur in einem sehr engen Spektrum, sondern auch mit erstaunlich geringen Anteilen am Aufbau der Legierung beteiligt ist und den diesem Element zugedachten Funktionen erfüllt. Herauszustellen ist in diesem Zusammenhang, dass diese Legierung Zn-frei ist. Es war überraschend festzustellen, dass bei dieser Legierung mit einem Mn-Gehalt, der sogar nur halb so groß sein kann wie der in der Legierung AA 2050 benötigte, ausreicht, um eine Rekristallisation wirksam zu verhindern. Zudem ist innerhalb der angegebenen Spanne von 0,01 Gew.-% bis < 0,2 Gew.-% Mn Sorge dafür getragen, dass keine oder nur in einem nicht nennenswerten Maße Primärphasen entstehen, die die Ermüdung und Zähigkeit verschlechtern würden. Untersuchungen haben gezeigt, dass sich bei dieser besonderen Legierungszusammensetzung ungewollte, plattenförmige Al6Mn-Phasen nicht oder allenfalls nur sehr untergeordnet bilden. In aller Regel ist Fe als Begleitelement nicht auszuschließen. Die sich mit Fe bildenden Phasen Al7Cu2Fe beeinträchtigen aufgrund ihrer kompakten Morphologie die mechanischen Eigenschaften eines aus dieser Legierung hergestellten Bauteils hingegen deutlich weniger. Insofern war es überraschend festzustellen, dass bei eine Al-Cu-Mg-Li-Legierung mit der vorbeschriebenen Zusammensetzung und ihrem besonders geringen Mn-Gehalt davon auszugehen ist, dass Bauteile mit der gewünschten Kombination aus Eigenschaften, die nicht nur hochfest, sondern auch zäh und ermüdungsbeständig sind, hergestellt werden konnten, die sogar höchstfesten Anforderungen genügen. Zur Definition hochfest und höchstfest: Ein Bauteil weist höchstfeste Eigenschaften auf, wenn die Dehngrenze R p0,2 zumindest 600 MPa beträgt. Einem Bauteil werden hochfeste Eigenschaften zugesprochen, wenn die Dehngrenze R p0,2 zumindest 500 MPa beträgt.This Ag and Li-containing high-performance aluminum alloy has a particularly narrow range of its alloying elements. This is especially true for the alloying element Mn, which not only in A very narrow spectrum, but also with surprisingly small proportions in the structure of the alloy is involved and fulfills the functions intended for this element. It should be pointed out in this context that this alloy is Zn-free. It was surprising to find that in this alloy having an Mn content as small as that required in the AA 2050 alloy, it is sufficient to effectively prevent recrystallization. In addition, care is taken within the stated range of 0.01% by weight to <0.2% by weight that no or only to a significant extent primary phases are formed which would impair fatigue and toughness. Investigations have shown that unintentional, plate-like Al 6 Mn phases do not form or at least only very subordinately form in this particular alloy composition. As a rule, Fe can not be excluded as a companion element. On the other hand, due to their compact morphology, the Fe-forming phases Al 7 Cu 2 Fe significantly impair the mechanical properties of a component made from this alloy. In this respect, it has surprisingly been found that in the case of an Al-Cu-Mg-Li alloy having the above-described composition and its particularly low Mn content, it can be assumed that components having the desired combination of properties that are not only high-strength but also tough and fatigue resistant, could be manufactured that meet even the highest strength requirements. For the definition of high-strength and highest-strength: A component has extremely strong properties if the yield strength R p0.2 is at least 600 MPa. A component is said to have high strength properties if the yield strength R p0.2 is at least 500 MPa.

Liegt der Cu-Anteil unter 3,7 Gew.-% stellt sich in Kombination mit den anderen Legierungselementen nicht die notwendige Festigkeit ein. Kupfergehalte über 3,9 Gew.-% in der Legierung vermögen die Festigkeit eines aus der Legierung hergestellten Bauteils nicht weiter zu erhöhen. Vielmehr ist damit zu rechnen, dass sich bei höheren Cu-Gehalten eigenschaftsschädigende Phasen bilden.If the Cu content is less than 3.7% by weight, the necessary strength does not appear in combination with the other alloying elements. Copper contents above 3.9 wt.% In the alloy are unable to further increase the strength of a component made from the alloy. On the contrary, it is to be expected that at higher Cu contents property-damaging phases form.

Lithium ist zur Reduzierung der Dichte (des spezifischen Gewichtes) in der Legierung enthalten. Der Lithium-Gehalt ist an die Cu- und Mg-Gehalte der Legierung angepasst, und zwar dergestalt, dass zwar möglichst viel Lithium in die Legierung eingebaut wird, jedoch nur so viel, dass dieses in Lösung gebracht werden kann und keine unerwünschten Li-haltigen Phasen entstehen. Daher ist der Li-Gehalt der Legierung auf den engen Bereich zwischen 0,9 und 1,3 Gew.-% begrenzt.Lithium is included to reduce the density (specific gravity) in the alloy. The lithium content is adapted to the Cu and Mg contents of the alloy in such a way that as much as possible Lithium is incorporated into the alloy, but only so much that this can be brought into solution and no unwanted Li-containing phases. Therefore, the Li content of the alloy is limited to the narrow range between 0.9 and 1.3 wt%.

Magnesium trägt zu den gewünschten Eigenschaften eines aus der Legierung hergestellten Bauteils bei, ist jedoch nur mit einem Anteil zugelassen, damit sich keine unerwünschten Phasen (wie z.B. eine S-Phase Al2CuMg) ausbilden. Unter Berücksichtigung der weiteren Legierungselemente soll der Mg-Anteil 0,45 Gew.-% nicht überschreiten.Magnesium contributes to the desired properties of a component made of the alloy, but is only permitted with one share, so that no undesirable phases (such as an S phase Al 2 CuMg) form. Taking into account the further alloying elements, the Mg content should not exceed 0.45% by weight.

Titan wirkt als Kornfeiner im Gussgefüge und Zirkon als Dispersoidbildner und trägt somit zur Hemmung der Rekristallisation bei.Titanium acts as a grain refiner in the cast structure and zirconium as a dispersoid former and thus contributes to the inhibition of recrystallization.

Überraschend hat sich gezeigt, dass unter Berücksichtigung der anderen Legierungselemente und deren Gehalte ein Mn-Gehalt zwischen 0,10 und 0,18 Gew.-% ausreicht, um wirksam eine Rekristallisation zu verhindern. Zugeschrieben wird dieses der speziellen und gezielten Auswahl des Anteils und der Bandbreite von Mn als auch der sehr eng begrenzte Mn-Gehalt. Dies gewährleistet, dass sich innerhalb dieser Grenzen durchweg die gewünschten Kombination an mechanischen Eigenschaften bei einem aus der Legierung hergestellten Bauteil einstellen lassen. Überschreitet der Mn-Gehalt 0,18 Gew.-% kann dieses unter Berücksichtigung der anderen Legierungselemente bereits zu gröberen Primärerstarrungen im Mikrogefüge führen, was wiederum der herrschenden Meinung entsprechend nicht zu erwarten war. Schließlich wird in der Legierung AA 2050 ein Mn-Gehalt von 0,2 - 0,8 Gew.-% vorgeschlagen. Daher ist der Mn-Gehalt der beanspruchten Legierung auf einen Maximalanteil von 0,18 Gew.-% begrenzt. Sollen keinerlei Primärerstarrungen im Mikrogefüge in Kauf genommen werden, wird der Mn-Gehalt auf eine Spanne von 0,10 - 0,15 Gew.-% nach oben hin begrenzt. Besonders gute Ergebnisse lassen sich erzielen, wenn der Mn-Gehalt zwischen 0,10 und 0,12 Gew.-% liegt.Surprisingly, it has been found that taking into account the other alloying elements and their contents, an Mn content of between 0.10 and 0.18 wt .-% is sufficient to effectively prevent recrystallization. This is attributed to the specific and targeted selection of the share and the range of Mn as well as the very limited Mn content. This ensures that within these limits can be consistently set the desired combination of mechanical properties in a made of the alloy component. If the Mn content exceeds 0.18% by weight, taking into account the other alloying elements, this may already lead to coarser primary solidifications in the microstructure, which in turn was not to be expected in accordance with prevailing opinion. Finally, in the alloy AA 2050, an Mn content of 0.2-0.8 wt% is proposed. Therefore, the Mn content of the claimed alloy is limited to a maximum amount of 0.18 wt%. If no primary solidification in the microstructure is to be accepted, the Mn content is limited to a range of 0.10-0.15% by weight at the top. Particularly good results can be achieved if the Mn content is between 0.10 and 0.12 wt .-%.

Ag ist zur Erhöhung der Festigkeit in dieser Legierung enthalten. In Abhängigkeit von der in dem Bauteil einzustellenden gewünschten Festigkeit wird der Ag-Gehalt etwas geringer oder etwas mehr innerhalb der beanspruchten Grenze zwischen 0,2 und 0,45 Gew.-% gewählt. Zur Erzielung eines Bauteiles, welches den Anforderungen an ein höchstfestes Bauteil genügen soll, sollte der Ag-Gehalt mehr als 0,35 Gew.-% betragen. Eine bevorzugte Beteiligung des Ag-Anteils am Aufbau der Legierung erstreckt sich von 0,38 - 0,43 Gew.-%.Ag is included to increase the strength in this alloy. Depending on the desired strength to be set in the component, the Ag content is chosen to be slightly lower or slightly more within the claimed limit of between 0.2 and 0.45 wt%. To achieve of a component which is to meet the requirements of a very high-strength component, the Ag content should be more than 0.35 wt .-%. A preferred contribution of the Ag content to the construction of the alloy is from 0.38 to 0.43 wt%.

Bemerkenswert ist auch, dass die Legierung vorzugsweise Fe-frei ist.It is also noteworthy that the alloy is preferably Fe-free.

Bevorzugt ist eine Ausgestaltung dieser Erfindung, bei der die dispersionsbildenden Elemente Mn+Fe+Si < 0,3 Gew.-% aufweisen.An embodiment of this invention is preferred in which the dispersion-forming elements have Mn + Fe + Si <0.3% by weight.

Es hat sich gezeigt, dass ein Cu/Mg-Verhältnis zwischen 8,22 und 12 besonders zweckmäßig ist, um die gewünschten Legierungseigenschaften zu erhalten.It has been found that a Cu / Mg ratio between 8.22 and 12 is particularly useful to obtain the desired alloy properties.

Für Untersuchungen der Legierungszusammensetzung und der sich einstellenden Kombination der gewünschten Eigenschaften von daraus hergestellten Bauteilen wurden erfindungsgemäße Legierungen sowie solche gemäß AA 2050 als Vergleichslegierung erschmolzen im Labormaßstab durch Kokillenguss zu Versuchsbarren gegossen.For investigations of the alloy composition and the adjusting combination of the desired properties of components produced therefrom, alloys according to the invention as well as those according to AA 2050 were melted as reference alloy on a laboratory scale by casting into random billets.

Die erschmolzenen Legierungen haben folgende Zusammensetzung, wobei die Legierung XL33 die erfindungsgemäße Legierung ist, während die Legierung AA 2050 als Vergleichslegierung erschmolzen worden ist: Legierung Cu Li Mg Mn Ti Zr Si Fe Ag XL33 3,78 0,90 0,35 0,11 0,052 0,112 0,02 0,02 0,404 AA 2050 3,72 0,94 0,31 0,38 0,40 0,092 0,04 0,063 0,491 The molten alloys have the following composition, wherein the alloy XL33 is the alloy according to the invention, while the alloy AA 2050 has been melted as a reference alloy: alloy Cu Li mg Mn Ti Zr Si Fe Ag XL33 3.78 0.90 0.35 0.11 0,052 0.112 0.02 0.02 0.404 AA 2050 3.72 0.94 0.31 0.38 0.40 0.092 0.04 0.063 0.491

Die gegossenen Barren wurden homogenisiert, stranggepresst und als Profile lösungsgeglüht und anschließend in Längsrichtung gereckt, und zwar um etwa 2 - 4 %. Die Warmauslagerung wurde für 48 Stunden bei 153 °C durchgeführt. Nachfolgend sind Untersuchungen durchgeführt worden, um die Dehngrenze R p0,2 , die Zugfestigkeit R m , die Bruchdehnung A 5 sowie die Risszähigkeit zu ermitteln. Die Untersuchungen sind an den Probenstücken an jeweils gleichen Stellen vorgenommen worden. Die Untersuchungen ergaben folgende Ergebnisse: Probe Dichte [g/cm3] Rp0,2 [MPa] Rm [MPa] A5 [%] K1C [MPa√m] XL33 L 2,7 653 668 9,8 L-T 37,3 T-L 25,9 AA 2050 L 2,7 615 638 11,2 L-T 42,1 T-L 31,6 The cast billets were homogenized, extruded and solution annealed as profiles and then stretched longitudinally by about 2-4%. The hot aging was carried out at 153 ° C for 48 hours. Subsequently, studies have been carried out to determine the yield strength R p0,2, the tensile strength R m, the elongation at break A 5 as well as the fracture toughness. The tests were carried out on the specimens in the same places. The investigations gave the following results: sample Density [g / cm 3 ] R p0.2 [MPa] Rm [MPa] A 5 [%] K 1 C [MPa√m] XL33 L 2.7 653 668 9.8 LT 37.3 TL 25.9 AA 2050 L 2.7 615 638 11.2 LT 42.1 TL 31.6

Parallel zu den vorbeschriebenen Probenstücken wurden solche hergestellt, deren Warmauslagerung für 48 Stunden bei etwa 160° C durchgeführt worden ist. Die Ergebnisse sind insofern von Interesse, da diese die Unempfindlichkeit der erfindungsgemäßen Legierung und somit die Wirksamkeit des speziellen Mn-Gehaltes belegen. Die Ergebnisse dieser Untersuchungen entsprechen bei der erfindungsgemäßen Legierung den Festigkeitswerten, die auch zu der Probe ermittelt worden sind, deren Warmauslagerung bei 153° C stattgefunden hat. Die Festigkeitswerte der Proben mit einer Warmauslagerung über 48 Stunden bei 160 °C sind nachfolgend wiedergegeben: Probe Dichte [g/cm3] Rp0,2 [MPa] Rm [MPa] A5 [%] K1C [MPa√m] XL33 L 2,7 642 663 9,7 L-T 36,9 T-L 25,2 AA 2050 L 2,7 597 629 9,5 L-T 41,1 T-L 30,5 In parallel with the above-described specimens, those were prepared whose thermal aging was carried out for 48 hours at about 160 ° C. The results are of interest in that they demonstrate the insensitivity of the alloy of the invention and thus the effectiveness of the particular Mn content. The results of these investigations in the case of the alloy according to the invention correspond to the strength values which have also been determined for the sample whose thermal aging took place at 153 ° C. The strength values of the samples aged 48 hours at 160 ° C are given below: sample Density [g / cm 3 ] R p0.2 [MPa] R m [MPa] A 5 [%] K 1 C [MPa√m] XL33 L 2.7 642 663 9.7 LT 36.9 TL 25.2 AA 2050 L 2.7 597 629 9.5 LT 41.1 TL 30.5

Die vorstehenden Untersuchungsergebnisse machen deutlich, dass Bauteile, die aus der erfindungsgemäßen Legierung hergestellt sind, sogar höchstfesten Ansprüchen genügen, die auch besser sind als die Festigkeitswerte, die an der Vergleichsprobe aus der Legierung AA 2050 ermittelt wurden. Zugeschrieben wird diese Steigerung in den Festigkeitswerten dem speziellen, gegenüber vorbekannten Legierungen sehr geringen Mn-Anteil. Die Festigkeitswerte zeigen zudem, dass auch bei derart niedrigen Mn-Gehalten in der speziellen Zusammensetzung der beanspruchten Legierung in Bezug auf die übrigen Legierungselemente Rekristallisationen wirksam gehemmt sind.The above test results make it clear that components made of the alloy according to the invention meet even very high-strength requirements, which are also better than the strength values which were determined on the comparative sample of the AA 2050 alloy. This increase in strength values is attributed to the special Mn content, which is very low compared with previously known alloys. The strength values also show that even with such low Mn contents in the specific composition of the claimed alloy, recrystallizations are effectively inhibited with respect to the other alloying elements.

Die vorstehenden mechanischen Eigenschaften konnten anhand etlicher Paralleluntersuchungen mit Variationen in der erfindungsgemäßen Legierungszusammensetzung im Rahmen der durch den Anspruch 1 gesetzten Grenzen bestätigt werden.

  • Figur 1 zeigt ein Gefügebild einer Probe aus der erfindungsgemäßen Legierung mit einem Cu-Gehalt von 3,3 Gew.-% und einem Mn-Gehalt von 0,11 Gew.-%. Bei den in Figur 1 erkennbaren Phasen handelt es sich ausschließlich um Al7Cu2Fe-Phasen.
  • Figur 2 zeigt ein Gefügebild einer Vergleichsprobe mit einer Legierungszusammensetzung entsprechend AA 2050 (s. Figur 2). Diese Legierung weist einen Cu-Gehalt von 3,7 Gew.-% und einen Mn-Gehalt von 0,37 Gew.-% auf. Das Gefügebild zeigt deutlich, dass in dieser Legierung neben den Al7Cu2Fe-Phasen die aufgrund ihrer Morphologie unerwünschten Al6Mn-Phasen vorhanden sind. Diese sind, wie in Figur 2 erkennbar, als lagig in der untersuchten Probe angeordnet, welche lagige Anordnung sich in der Al6Mn-Partikel-Zeile zeigt.
The above mechanical properties could be confirmed by several parallel investigations with variations in the alloy composition according to the invention within the limits set by claim 1.
  • FIG. 1 shows a micrograph of a sample of the alloy according to the invention with a Cu content of 3.3 wt .-% and a Mn content of 0.11 wt .-%. At the in FIG. 1 identifiable phases are exclusively Al 7 Cu 2 Fe phases.
  • FIG. 2 shows a micrograph of a comparative sample with an alloy composition corresponding to AA 2050 (s. FIG. 2 ). This alloy has a Cu content of 3.7% by weight and an Mn content of 0.37% by weight. The micrograph clearly shows that in addition to the Al 7 Cu 2 Fe phases, this alloy contains the undesirable Al 6 Mn phases due to their morphology. These are as in FIG. 2 recognizable, as a layered arranged in the examined sample, which shows layered arrangement in the Al 6 Mn particle line.

Ein aus dieser Legierung hergestelltes Bauteil eignet sich aufgrund der vorbeschriebenen Eigenschaften als Bauteil zur Verwendung in der Luft- und Raumfahrtindustrie, vor allem für Strukturbauteile. Gleichwohl können Bauteile aus dieser Legierung auch für andere Anwendungen hergestellt und eingesetzt werden, vor allem dann, wenn auch eine geringe Dichte eine Rolle spielen sollte.A component made of this alloy is suitable as a component for use in the aerospace industry, especially for structural components, due to the properties described above. However, components made of this alloy can also be made and used for other applications, especially if a low density should also play a role.

Claims (9)

  1. Al-Cu-Mg-Li alloy with
    3.7 - 3.9 % by weight Cu,
    0.9 - 1.3 % by weight Li,
    0.30 - 0.45 % by weight Mg,
    0.10 - < 0.2 by weight Mn,
    0.2 - 0.45 % by weight Ag,
    0.09 - 0.13 % by weight Zr
    max. 0.07 % by weight Ti, wherein the Ti is present as TiB2 or TiC,
    remainder Al, together with unavoidable impurities.
  2. Al-Cu-Mg-Li alloy according to claim 1, with
    3.7 - 3.9 % by weight Cu,
    0.95 - 1.2 % by weight Li,
    0.35 - 0.45 % by weight Mg,
    0.10- 0.18 by weight Mn,
    0.38 - 0.43 % by weight Ag,
    0.09 - 0.13 % by weight Zr
    max. 0.07 % by weight Ti, wherein the Ti is present as TiB2 or TiC,
    remainder Al, together with unavoidable impurities.
  3. Al-Cu-Mg-Li alloy according to claim 1 or 2, characterised in that the Mn content is between 0.10 and 0.15 % by weight.
  4. Al-Cu-Mg-Li alloy according to any one of claims 1 to 3, characterised in that the sum of the dispersion-forming elements Mn+Fe+Si < 0.3 % by weight.
  5. Al-Cu-Mg-Li alloy according to one of claims 1 to 4, characterised in that the Cu/Mg ratio is between 8.22 and 12.
  6. Al-Cu-Mg-Li alloy product with an alloy composition according to any one of claims 1 to 5, characterised in that the product has been hardened in such a way that the alloy product exhibits parallel to the fibre a 0.2% elongation limit Rp0.2 of more than 620 MPa and a tensile strength Rm of more than 630 MPa.
  7. Al-Cu-Mg-Li alloy product according to claim 6, characterised in that this exhibits parallel to the fibre an elongation after fracture A5 of at least 9% parallel to the fibre.
  8. Al-Cu-Mg-Li alloy product according to claim 6 or 7, characterised in that the composition of the alloy is selected in such a way that the product resulting from it exhibits a density of some 2.70 g/cm3.
  9. Al-Cu-Mg-Li alloy product according to any one of claims 6 to 8, characterised in that the alloy product is a structural component for an aeronautical and/or aerospace application.
EP15161219.9A 2015-03-27 2015-03-27 Al-cu-mg-li alloy and alloy product produced from same Active EP3072984B2 (en)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP15161219.9A EP3072984B2 (en) 2015-03-27 2015-03-27 Al-cu-mg-li alloy and alloy product produced from same
ES15161219T ES2642118T5 (en) 2015-03-27 2015-03-27 Al-Cu-Mg-Li alloy as well as an alloy product made from it

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP15161219.9A EP3072984B2 (en) 2015-03-27 2015-03-27 Al-cu-mg-li alloy and alloy product produced from same

Publications (3)

Publication Number Publication Date
EP3072984A1 EP3072984A1 (en) 2016-09-28
EP3072984B1 true EP3072984B1 (en) 2017-07-05
EP3072984B2 EP3072984B2 (en) 2020-05-06

Family

ID=52807628

Family Applications (1)

Application Number Title Priority Date Filing Date
EP15161219.9A Active EP3072984B2 (en) 2015-03-27 2015-03-27 Al-cu-mg-li alloy and alloy product produced from same

Country Status (2)

Country Link
EP (1) EP3072984B2 (en)
ES (1) ES2642118T5 (en)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115125422B (en) * 2022-06-09 2023-10-10 烟台南山学院 Corrosion-resistant high-strength-toughness Al-Li-Cu-Zr-Er alloy plate and preparation method thereof

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2009036953A1 (en) 2007-09-21 2009-03-26 Aleris Aluminum Koblenz Gmbh Al-cu-li alloy product suitable for aerospace application
US20090142222A1 (en) 2007-12-04 2009-06-04 Alcoa Inc. Aluminum-copper-lithium alloys
US20090180890A1 (en) 2006-04-29 2009-07-16 Oerlikon Leybold Vacuum Gmbh Rotors or stators of a turbomolecular pump
US20110030856A1 (en) 2009-06-25 2011-02-10 Alcan Rhenalu Casting process for aluminum alloys
US20110247730A1 (en) 2010-04-12 2011-10-13 Alcoa Inc. 2xxx series aluminum lithium alloys having low strength differential

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20090180890A1 (en) 2006-04-29 2009-07-16 Oerlikon Leybold Vacuum Gmbh Rotors or stators of a turbomolecular pump
WO2009036953A1 (en) 2007-09-21 2009-03-26 Aleris Aluminum Koblenz Gmbh Al-cu-li alloy product suitable for aerospace application
US20090142222A1 (en) 2007-12-04 2009-06-04 Alcoa Inc. Aluminum-copper-lithium alloys
US20110030856A1 (en) 2009-06-25 2011-02-10 Alcan Rhenalu Casting process for aluminum alloys
US20110247730A1 (en) 2010-04-12 2011-10-13 Alcoa Inc. 2xxx series aluminum lithium alloys having low strength differential

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
TEAL SHEETS: "International Alloy Designations and Chemical Composition Limits for Wrought Aluminum and Wrought Aluminum Alloys", ALUMINUM ASSOCIATION, 2015, XP055460438

Also Published As

Publication number Publication date
ES2642118T3 (en) 2017-11-15
EP3072984A1 (en) 2016-09-28
EP3072984B2 (en) 2020-05-06
ES2642118T5 (en) 2020-12-30

Similar Documents

Publication Publication Date Title
EP2954081B1 (en) Aluminium casting alloy
EP1683882B1 (en) Aluminium alloy with low quench sensitivity and process for the manufacture of a semi-finished product of this alloy
DE69912850T2 (en) METHOD OF PRODUCING AN ALUMINUM-MAGNESIUM-LITHIUM ALLOY PRODUCT
AT502310B1 (en) AN AL-ZN-MG-CU ALLOY
DE69125436T2 (en) Aluminum alloy sheet with good resistance to damage for aircraft sheet
EP1888798B1 (en) Aluminium plain bearing alloy
DE69325804T2 (en) HIGH-STRENGTH AL-LI ALLOY WITH LOW DENSITY AND HIGH TENSITY AT HIGH TEMPERATURES
DE102016219711B4 (en) Aluminum alloy for die casting and process for its heat treatment
DE69823387T2 (en) ALUMINUM ALLOY WITH HIGH TENSILE FOR USE IN AVIATION
EP3024958B1 (en) High temperature strength aluminium casting alloy and casting for combustion engines cast from said alloy
EP3775309B1 (en) Aluminum die casting alloy
WO2004003244A1 (en) Al/cu/mg/ag alloy with si, semi-finished product made from such an alloy and method for production of such a semi-finished product
EP3072985B1 (en) Ag-free al-cu-mg-li alloy
WO2007025528A2 (en) Aluminium casting alloy
EP2455505A1 (en) Cylinder head for combustion engines made of an aluminium alloy
EP1747298A1 (en) Titanium/aluminium alloy
DE69717858T2 (en) ALUMINUM ALLOY PRODUCT
DE3486352T2 (en) Aluminum-lithium alloy.
EP3072984B1 (en) Al-cu-mg-li alloy and alloy product produced from same
DE202017100517U1 (en) Al-Cu-Li-Mg-Mn-Zn wrought alloy product
EP3818187B1 (en) Aluminum alloy and overaged aluminum alloy product made of such an alloy
EP3252179A1 (en) Copper alloy comprising aluminium and nickel and its use
DE102017103148A1 (en) Al-cast alloy
EP3763845B1 (en) Magnesium alloy and its process of manufacture
DE102004030021B4 (en) Rolled product

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): 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

17P Request for examination filed

Effective date: 20161011

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20170308

RBV Designated contracting states (corrected)

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

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): 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: AT

Ref legal event code: REF

Ref document number: 906661

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170715

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: DE

Ref legal event code: R096

Ref document number: 502015001365

Country of ref document: DE

REG Reference to a national code

Ref country code: CH

Ref legal event code: NV

Representative=s name: ALDO ROEMPLER PATENTANWALT, CH

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20170705

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2642118

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20171115

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

REG Reference to a national code

Ref country code: NO

Ref legal event code: T2

Effective date: 20170705

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: 20170705

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: 20170705

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: 20170705

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: 20170705

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: 20170705

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: 20171006

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: 20170705

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: 20171105

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: 20170705

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: 20171005

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: 20170705

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 4

REG Reference to a national code

Ref country code: DE

Ref legal event code: R026

Ref document number: 502015001365

Country of ref document: DE

PLBI Opposition filed

Free format text: ORIGINAL CODE: 0009260

PLAX Notice of opposition and request to file observation + time limit sent

Free format text: ORIGINAL CODE: EPIDOSNOBS2

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: 20170705

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: 20170705

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: 20170705

26 Opposition filed

Opponent name: ARCONIC INC.

Effective date: 20180403

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

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: 20170705

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: 20170705

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: 20170705

PLBB Reply of patent proprietor to notice(s) of opposition received

Free format text: ORIGINAL CODE: EPIDOSNOBS3

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: 20170705

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: 20170705

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

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: 20170705

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20180331

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: LU

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

Effective date: 20180327

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: 20180327

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: 20180331

APBM Appeal reference recorded

Free format text: ORIGINAL CODE: EPIDOSNREFNO

APBP Date of receipt of notice of appeal recorded

Free format text: ORIGINAL CODE: EPIDOSNNOA2O

APAH Appeal reference modified

Free format text: ORIGINAL CODE: EPIDOSCREFNO

APBU Appeal procedure closed

Free format text: ORIGINAL CODE: EPIDOSNNOA9O

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: 20170705

PUAH Patent maintained in amended form

Free format text: ORIGINAL CODE: 0009272

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

Free format text: STATUS: PATENT MAINTAINED AS AMENDED

REG Reference to a national code

Ref country code: CH

Ref legal event code: AELC

27A Patent maintained in amended form

Effective date: 20200506

AK Designated contracting states

Kind code of ref document: B2

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: DE

Ref legal event code: R102

Ref document number: 502015001365

Country of ref document: DE

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: 20170705

REG Reference to a national code

Ref country code: NO

Ref legal event code: TB2

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: 20150327

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: 20170705

Ref country code: MK

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

Effective date: 20170705

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

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: 20170705

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 502015001365

Country of ref document: DE

Representative=s name: HAVERKAMP PATENTANWAELTE PARTG MBB, DE

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

Ref country code: GB

Payment date: 20220324

Year of fee payment: 8

Ref country code: CH

Payment date: 20220324

Year of fee payment: 8

Ref country code: AT

Payment date: 20220214

Year of fee payment: 8

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

Ref country code: NO

Payment date: 20220322

Year of fee payment: 8

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

Ref country code: IT

Payment date: 20220331

Year of fee payment: 8

Ref country code: ES

Payment date: 20220420

Year of fee payment: 8

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

Ref country code: FR

Payment date: 20230320

Year of fee payment: 9

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

Ref country code: DE

Payment date: 20230310

Year of fee payment: 9

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

Effective date: 20230529

REG Reference to a national code

Ref country code: NO

Ref legal event code: MMEP

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 906661

Country of ref document: AT

Kind code of ref document: T

Effective date: 20230327

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

Effective date: 20230327

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: 20230327

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

Ref country code: NO

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

Effective date: 20230331

Ref country code: LI

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

Effective date: 20230331

Ref country code: GB

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

Effective date: 20230327

Ref country code: CH

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

Effective date: 20230331

Ref country code: AT

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

Effective date: 20230327

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: 20230327

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20240528

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

Ref country code: ES

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

Effective date: 20230328

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

Ref country code: ES

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

Effective date: 20230328