EP2697406B1 - Aluminium-kupfer-magnesium-legierungen mit guter leistung bei hohen temperaturen - Google Patents

Aluminium-kupfer-magnesium-legierungen mit guter leistung bei hohen temperaturen Download PDF

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EP2697406B1
EP2697406B1 EP12717140.3A EP12717140A EP2697406B1 EP 2697406 B1 EP2697406 B1 EP 2697406B1 EP 12717140 A EP12717140 A EP 12717140A EP 2697406 B1 EP2697406 B1 EP 2697406B1
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wrt
alloy
product
wire
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EP2697406A1 (de
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Gaëlle POUGET
Christophe Sigli
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Constellium Issoire SAS
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Constellium Issoire SAS
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    • 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
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/057—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 aluminum-copper-magnesium alloy products, more particularly, such products, their methods of manufacture and use, intended to be implemented at high temperature.
  • Al-Cu-Mg alloys are also known.
  • the patent US 3,826,688 teaches a composition alloy (in% by weight), Cu: 2.9 - 3.7, Mg: 1.3 - 1.7 and Mn: 0.1 - 0.4.
  • the patent application EP 0 038 605 A1 teaches a composition alloy (in% by weight), Cu: 3.8 - 4.4, Mg: 1.2 - 1.8 and Mn: 0.3 - 0.9, maximum 0.12 Si, 0 , Fe, 0.25 Zn, 0.15 Ti and 0.10 Cr.
  • a first subject of the invention is a wrought product made of aluminum alloy of composition, in% by weight, Cu Corr : 2.6 - 3.7 Mg corr : 1.5 - 2.6 Mn: 0.2 - 0.5 Zr: ⁇ 0.16 Ti: 0.01 - 0.15 Cr ⁇ 0.25 If ⁇ 0.2 Fe ⁇ 0.2 other elements ⁇ 0.05 rest aluminum with Cu corr > - 0.9 ( Corr. Mg) + 4.3 and Corr Cu ⁇ - 0.9 ( Corr.
  • Yet another object of the invention is the use of a wrought product according to the invention in an application in which said product is maintained at temperatures of 100 ° C. to 200 ° C. for a significant period of at least 200 hours. hours.
  • the static mechanical characteristics in tension in other words the tensile strength R m , the conventional yield stress at 0.2% elongation R p0.2 and the elongation at break A%, are determined by a tensile test according to standard NF EN ISO 6892-1, the sampling and the direction of the test being defined by the EN 485-1 standard.
  • the hot tensile tests are carried out according to standard NF EN 10002-5. Creep tests are performed according to ASTM E139-06.
  • EN 12258 Unless otherwise specified, the definitions of EN 12258 apply.
  • the present inventors have found that, surprisingly, there is a compositional range of Al-Cu-Mg alloys containing Mn which makes it possible to obtain particularly high performance wrought products at high temperature.
  • the composition of the wrought products of the invention is defined according to the content of iron, manganese and silicon. Corrected Cu and Mg contents, called Cu Corr and Mg corr corresponding to the contents of these elements which are not trapped by intermetallic compounds containing iron, manganese or silicon, are defined. This correction is important in defining the Cu and Mg composition domain of the invention because the iron and manganese containing intermetallic compounds formed with the copper and the intermetallic compounds formed with the silicon-containing magnesium generally can not be processed. solution.
  • Cu corr and Mg corr thus correspond to the Cu and Mg contents available after solution dissolution for the formation during the recovery of the nanometric phases contributing to hardening.
  • the copper and magnesium contents thus corrected must obey the following inequalities: Cu corr > - 0 , 9 mg corr + 4 , 3 preferably Cu corr > - 0 , 9 mg corr + 4 , 5 Cu corr ⁇ - 0 , 9 mg corr + 5 , 0
  • the magnesium content is such that Mg corr is between 1.5 and 2.6% by weight and preferably between 1.6 and 2.4% by weight. In an advantageous embodiment of the invention, Mg corr is at least 1.8% by weight and preferably at least 1.9% by weight. This embodiment is particularly advantageous for products in the T6 state.
  • the copper content is such that Cu corr is between 2.6 and 3.7% by weight.
  • the maximum magnesium content is 2.86% by weight corresponding to a Mg content corr of 2.6% by weight, obtained for an Si content of 0.2% by weight.
  • the minimum magnesium content is 1.5% by weight, obtained for a Si content of 0% by weight.
  • the maximum copper content is 3.69% by weight, obtained for a manganese content of 0.5% by weight and corresponding to a corrected Cu corr content of 3.29% by weight.
  • an advantageous range of composition of the products according to the invention has a magnesium content of between 1.6 and 2.2% by weight and preferably between 1.8 and 2.1% by weight. and / or a copper content of between 2.8 and 3.7% by weight and preferably between 2.9 and 3.4% by weight.
  • the products according to the invention contain 0.2 to 0.5% by weight of manganese, which contributes in particular to the control of the granular structure.
  • the present inventors have found that the simultaneous addition of manganese and zirconium is advantageous for further improving the control of the granular structure.
  • the Zr content is at least 0.07% by weight and preferably at least 0.08% by weight.
  • the products according to the invention contain 0.09 to 0.15% by weight of zirconium and 0.25 to 0.45% by weight of manganese.
  • the chromium content is at most 0.25% by weight. In one embodiment of the invention, the chromium content is between 0.05 and 0.25% by weight and can contribute in particular to the control of the granular structure.
  • the presence of chromium can cause problems of recycling and sensitivity to quenching, especially for products whose thickness is at least 50 mm.
  • the chromium content is less than 0.05% by weight.
  • the titanium content is between 0.01 and 0.15% by weight.
  • the addition of titanium contributes in particular to the refining of the grains during casting. In one embodiment, it is preferred to limit the addition of titanium to a maximum value of 0.05% by weight. However, a larger ripening may be useful.
  • the titanium content is between 0.07 and 0.14% by weight.
  • the iron and silicon contents are at most 0.2% by weight each.
  • the iron and / or silicon contents are at most 0.1% by weight and preferably 0.08% by weight.
  • the equations for calculating corr Cu and Mg corr take account of variations of Fe and Si and to achieve the same value of Cu corr more copper is added when the iron content increases.
  • the content of the other elements is less than 0.05% by weight.
  • the rest is aluminum.
  • the wrought products according to the invention are typically sheets, profiles, bars or wires, but can also be screws, bolts or rivets.
  • the method of manufacturing the products according to the invention comprises the successive stages of elaboration of the alloy, casting, optionally homogenization, deformation, dissolution, tempering, optionally cold deformation and tempering.
  • a bath of liquid metal is produced so as to obtain an aluminum alloy of composition according to the invention.
  • the liquid metal bath is then typically cast in the form of a rolling plate, spinning billet, bar blank or wire.
  • the product thus cast is then homogenized so as to reach a temperature of between 450 ° C. and 520 ° C. and preferably between 500 ° C. and 510 ° C. for a period of between 5 and 60 hours.
  • the homogenization treatment can be carried out in one or more stages.
  • the product is then typically deformed by rolling, spinning and / or drawing and / or drawing and / or coining.
  • the product thus deformed is then dissolved in a heat treatment to reach a temperature of between 490 and 520 ° C and preferably between 500 and 510 ° C for 15 min to 8 h, and then quenched.
  • the quality of dissolution can be evaluated by calorimetry and / or optical microscopy.
  • the objective being that Cu and Mg are in solid solution with the exception of Cu and bound Mg in the intermetallic compounds containing manganese of iron and / or silicon.
  • the product can then optionally undergo a cold deformation.
  • an income is achieved in which the product reaches a temperature between 160 and 210 ° C and preferably between 175 and 195 ° C for 5 to 100 hours and preferably 10 to 50h.
  • the income can be achieved in one or more levels.
  • the income conditions are determined so that the mechanical resistance Rp 0.2 is maximum ("peak" income).
  • a first embodiment of the method according to the invention allows the manufacture of sheets or profiles.
  • a second embodiment of the method according to the invention allows the manufacture of son or bars, such as in particular blanks for machining, blanks forging, blanks bolts, rivet threads, blanks screws and bolts, screws and rivets.
  • the first embodiment of the process according to the invention comprises the successive stages of elaboration of the alloy, cast in the form of a plate or billet, optionally homogenization, hot deformation, dissolution, tempering, optionally cold deformation and tempering. .
  • the liquid metal bath is cast in the form of a rolling plate or a spinning billet.
  • the optionally homogenized rolling plate or spinning billet is then hot deformed by rolling or spinning.
  • the hot deformation of the first embodiment is performed so as to maintain a temperature of at least 300 ° C.
  • a temperature of at least 350 ° C. and preferably at least 380 ° C. is maintained during the hot deformation.
  • no significant cold deformation is carried out, in particular by cold rolling, between the hot deformation and the dissolution. Indeed, such a cold deformation step would lead to a recrystallized structure that is undesirable in the context of the invention for wrought products in the form of sheets or profiles.
  • Significant cold deformation is typically a deformation of at least about 5%.
  • the sheet or the profile thus obtained is then put in solution by a heat treatment making it possible to reach a temperature of between 490 and 520 ° C. and preferably between 500 and 510 ° C. for 15 minutes to 8 hours, and then quenched typically with the water.
  • substantially non-recrystallized granular structure means a non-recrystallized granular structure content at mid-thickness greater than 70% and preferably greater than 85%.
  • the sheet or the profile obtained can then optionally undergo a cold deformation.
  • the cold deformation is a controlled traction with a permanent elongation of 2 to 5% to improve the mechanical strength and to obtain a T8 state after income. In the absence of cold deformation or in the presence of a low cold deformation does not improve the mechanical characteristics, after income a product is obtained in the T6 state.
  • the sheets and profiles obtained according to the first embodiment of the method of the invention have the advantage of having a high mechanical strength and good performance at high temperature.
  • the sheets and profiles according to the invention preferably have, in the longitudinal direction T8, a yield strength R p0.2 of at least 440 MPa, preferably at least 450 MPa and, preferably, at least 450 MPa. at least 455 MPa.
  • a yield strength R p0.2 of at least 470 MPa can advantageously be obtained in the longitudinal direction.
  • the reduction of the elastic limit of the sheets and profiles according to the invention in the T8 state in the longitudinal direction is advantageously less than 12%, preferably less than 10% and, preferably, less than 8%.
  • the profiles according to the invention advantageously have, in the T8 state, a yield strength measured at 150 ° C. in the longitudinal direction of at least 370 MPa and preferably at least 380 MPa.
  • the sheets or profiles made in the embodiment in which the Mg content is such that Mg corr is at least 1.8% by weight advantageously have a yield strength measured at 150 ° C. in the longitudinal direction of at least 340 MPa and a decrease in yield strength after 2000h aging at 150 ° C less than 5%.
  • the second embodiment of the method according to the invention comprises the successive stages of elaboration of the alloy, cast in the form of wire blank or bar, optionally homogenization, hot deformation and / or cold by spinning and / or stretching and / or drawing and optionally by subsequent striking of the wire or bar obtained to obtain screws, bolts or rivets, dissolution, quenching and tempering.
  • the liquid metal bath is cast as a blank of wire or bar, preferably on a casting wheel, typically with the continuous casting process known as " Properzi ".
  • the wire blank or bar may also be a spinning billet.
  • the blank wire or bar is then deformed hot and / or cold by spinning and / or drawing and / or drawing.
  • the wire blank or bar is a spinning billet, it will be hot-spun before being cold-formed by drawing and / or drawing, whereas if the wire blank or bar has been obtained by continuous casting and hot deformation at the outlet of the casting wheel, it will only be necessary to deform it cold.
  • the wire or bar obtained can be struck at this point to obtain screws, bolts or rivets.
  • the product thus obtained is then put in solution by a heat treatment making it possible to reach a temperature of between 490 and 520 ° C. and preferably between 500 and 510 ° C. for 15 minutes to 8 hours, and then typically quenched with water. .
  • essentially recrystallized structure is meant a recrystallization rate of at least 80% and preferably a fine grain structure and homogeneous size.
  • the product obtained can then optionally undergo a cold deformation.
  • certain products such as in particular bolts, screws and rivets, it is difficult to perform a cold deformation after dissolution and quenching.
  • the product is not subjected to cold deformation after dissolution and quenching, and after recovery a T6 state is obtained.
  • a particularly alloy advantageous for the T6 state has an Mg content such that Mg corr is at least equal to 1.8% by weight.
  • manufacture of products such as wire, bolt, rivet, screw, in the T8 state and having a substantially recrystallized alloy granular structure according to the invention is advantageous.
  • the products obtained according to the second embodiment of the process of the invention advantageously have in the T8 state in the longitudinal direction a yield strength R p0.2 of at least 460 MPa, preferably at least 480 MPa. and after aging at 150 ° C. for 2000 h, a decrease in the yield strength in the longitudinal direction of less than 10%, preferably less than 8%.
  • the products according to the invention are particularly useful for applications in which the products are maintained at temperatures of 100 ° C to 200 ° C, typically at about 150 ° C, for a significant period of at least 200 hours and preferably at least 2000 hours.
  • the products according to the invention are useful for fasteners intended for use in a motor typically for automobiles, such as screws or bolts or rivets.
  • the products according to the invention are also useful for the manufacture of parts of the nacelle and / or aircraft attachment masts.
  • the nacelle designates all the supports and hoods of an engine of a multi-engine aircraft:
  • the products according to the invention are also useful for the manufacture of aircraft wing leading edges.
  • the products according to the invention are also useful for the manufacture of fuselage of supersonic aircraft.
  • Alloys A-1 and C-1 have a composition according to the invention.
  • composition of the alloys is given in Table 1.
  • the plates were homogenized at a temperature of between 500 ° C. and 540 ° C., adapted according to the alloy, hot-rolled to a thickness of 15 mm, dissolved at a temperature of between 500 ° C. and 540 ° C, adapted according to the alloy, quenched with water by immersion, traced by 3 to 4% and returned to 190 ° C to reach the peak of elastic limit in tension at the T8 state.
  • the alloy plate A-1 was homogenized in two steps of 10h at 500 ° C and 20h at 509 ° C, the sheet obtained after rolling being dissolved for 2h at 507 ° C and returned for 12 hours at 190 ° C.
  • the alloy plate B-1 was homogenized in two steps of 10h at 500 ° C and 20h at 503 ° C, the sheet obtained after rolling being dissolved in 2h at 500 ° C and returned 8h at 190 ° C.
  • the alloy plate C-1 was homogenized in two steps of 10h at 500 ° C and 20h at 503 ° C, the sheet obtained after rolling being dissolved in 2h at 504 ° C and returned for 12 hours at 190 ° C.
  • the alloy plate D-1 was homogenized in two steps of 10h at 500 ° C and 20h at 536 ° C, the sheet obtained after rolling being dissolved for 2h at 535 ° C and returned 8h at 190 ° C.
  • the sheets obtained had a substantially non-recrystallized granular structure.
  • the sheets thus obtained were characterized in the longitudinal direction before and after aging at several temperatures and for several durations.
  • the results are shown in Table 2 Table 2 - Mechanical properties obtained at mid-thickness L-direction before and after aging (MPa) Aging temperature (° C) Aging time (h) A-1 C-1 B-1 D-1 R 0.2 rm R 0.2 rm R 0.2 rm R 0.2 rm R 0.2 rm No aging 456 476 468 485 470 483 385 447 150 500 450 471 471 487 451 488 379 442 150 1000 447 467 462 484 427 472 372 438 150 2000 436 467 440 473 411 463 375 450 150 5000 421 455 424 466 386 449 352 431 200 500 355 398 353 417 312 365 288 375 200 1000 340 405 332 404 295
  • the alloy billet A-2 was homogenized 24h at 508 ° C. and the bars obtained dissolved for 1 hour at 506 ° C.
  • the alloy billet C-2 was homogenized 24h at 508 ° C. and the bars obtained dissolved for 1 hour at 503 ° C. Some bars were trimmed from 3 to 4% of other bars were not pulled, all the bars finally had a peak income to get a T6 state (untracted, 20h at 190 ° C for A-2 and 16h at 190 ° C for C-2) or T8 (tractionné, 12h at 190 ° C for the two alloys).
  • the profiles obtained had a substantially non-recrystallized granular structure.
  • alloy wires 6056 in the T6 state with a diameter of 12 mm and alloy bars 2618 in the T8 state with a diameter of 40 mm were used.
  • the mechanical properties in the longitudinal direction before and after aging at 150 ° C are given in Table 4.
  • the alloy A-2 is particularly thermally stable.
  • the products according to the invention have, in particular, a breaking strength significantly higher than that of conventionally used reference products such as alloy 6056 (T6) or alloy 2618 (T8).
  • Creep tests were carried out according to the ASTM E139-06 standard for a stress of 285 MPa and at a temperature of 150 ° C. In particular, the service life, the deformation after 200h and the stationary creep rate were measured. The results are collated in Table 6.
  • a 13 mm diameter C-2 alloy cylindrical bar was obtained by hot spinning from a billet homogenized 24h at 508 ° C. The bar was then stretched cold to obtain a wire of diameter 10; 55 mm. The yarn thus obtained was dissolved for 1 hour at 503 ° C., fractionated by 3 to 4% and then returned for 12 hours at 190 ° C. to obtain a T8 state.
  • the granular structure of the yarn thus obtained was essentially recrystallized and had a fine and homogeneous grain

Claims (15)

  1. Kneterzeugnis ausgewählt aus der Gruppe bestehend aus Blechen, Profilen, Stangen/Stäben, Drähten, Schrauben, Bolzen und Nieten, erhältlich durch ein Verfahren mit den aufeinanderfolgenden Schritten: Herstellen einer Legierung, Gießen, wahlweise Homogenisieren, Umformen, Lösungsglühen, Abschrecken, wahlweise Kaltumformen und Auslagern, wobei die Legierung eine Aluminiumlegierung ist, enthaltend (in Gew.-%):
    Cucorr: 2,6 - 3,7
    Mgcorr: 1,5 - 2,6
    Mn: 0,2 - 0,5
    Zr: ≤ 0,16
    Ti: 0,01 - 0,15
    Cr ≤ 0,25
    Si ≤ 0,2
    Fe ≤ 0,2
    weitere Elemente < 0,05
    Rest Aluminium
    mit Cucorr > - 0,9 (Mgcorr) + 4,3 und CUcorr< - 0,9 (Mgcorr) + 5,0,
    wobei Cucorr= Cu - 0,74 (Mn - 0,2) - 2,28 Fe und
    Mgcorr = Mg - 1,73 (Si - 0,05) für Si ≥ 0,05 und Mgcorr = Mg für Si < 0,05, wobei Cucorr und Mgcorr Cu- und Mg-Gehalte sind, die nicht von intermetallischen Verbindungen mit Eisen, Mangan oder Silicium eingefangen sind.
  2. Kneterzeugnis nach Anspruch 1, bei dem Mgcorr mindestens 1,8 Gew.-% und vorzugsweise mindestens 1,9 Gew.% beträgt.
  3. Kneterzeugnis nach Anspruch 1 oder Anspruch 2, bei dem Zr mindestens 0,07 Gew.-% und vorzugsweise mindestens 0,08 Gew.% beträgt.
  4. Kneterzeugnis nach irgendeinem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass es sich um ein Blech oder Profil handelt, dessen Korngefüge im Wesentlichen nicht rekristallisiert ist.
  5. Kneterzeugnis nach Anspruch 4, welches im Zustand T8 in Längsrichtung eine Dehngrenze Rp0,2 von mindestens 440 MPa und vorzugweise mindestens 450 MPa und nach Alterung bei 150°C für eine Dauer von 2000h eine Abnahme der Dehngrenze in Längsrichtung von weniger als 12 % und vorzugsweise weniger als 10 % aufweist.
  6. Kneterzeugnis nach Anspruch 4, bei dem Mgcorr mindestens 1,8 Gew.-% beträgt und das im Zustand T6 eine in Längsrichtung gemessene 0,2 %-Dehngrenze von mindestens 340 MPa und nach 2000h Alterung bei 150°C eine Abnahme der Dehngrenze von weniger als 5 % aufweist.
  7. Kneterzeugnis nach irgendeinem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass es sich um Draht oder Stangenmaterial oder einen Bolzen oder eine Schraube oder einen Niet mit einem im Wesentlichen nicht rekristallisierten Korngefüge handelt.
  8. Kneterzeugnis nach Anspruch 7, welches im Zustand T8 in Längsrichtung eine Dehngrenze Rp0,2 von mindestens 460 MPa, vorzugsweise mindestens 480 MPa und nach Alterung bei 150°C für eine Dauer von 2000h eine Abnahme der Dehngrenze in Längsrichtung von weniger als 10 % und vorzugsweise weniger als 8 % aufweist.
  9. Verfahren zur Herstellung eines Kneterzeugnisses nach einem der Ansprüche 1 bis 8, bei dem aufeinanderfolgend
    - ein Flüssigmetallbad hergestellt wird, um eine Aluminiumlegierung mit einer Zusammensetzung nach irgendeinem der Ansprüche 1 bis 3 zu erhalten,
    - die Legierung typischerweise zu Walzbarren, Pressbarren, Vormaterial für Stangenmaterial oder Drähte vergossen wird,
    - das gegossene Erzeugnis wahlweise homogenisiert wird, um eine Temperatur zwischen 450°C und 520°C zu erreichen,
    - das erhaltene Erzeugnis vor dem Lösungsglühen umgeformt wird,
    - das umgeformte Erzeugnis durch eine Wärmebehandlung bei einer Temperatur zwischen 490 und 520°C und vorzugsweise zwischen 500 und 510°C für 15 min bis 8 h lösungsgeglüht und anschließend abgeschreckt wird,
    - das lösungsgeglühte und abgeschreckte Erzeugnis wahlweise kalt umgeformt wird,
    - das erhaltene Erzeugnis bei einer Temperatur zwischen 160 und 210°C und vorzugsweise zwischen 175 und 195°C für 5 bis 100 Stunden und vorzugsweise 10 bis 50 Stunden ausgelagert wird.
  10. Verfahren nach Anspruch 9, bei dem
    - die Legierung zu Walzbarren oder Pressbarren vergossen wird,
    - die Umformung vor dem Lösungsglühen durch Warmwalzen oder Warmpressen bei Halten einer Temperatur von mindestens 300°C erfolgt, ohne signifikante Kaltumformung.
  11. Verfahren nach Anspruch 10, bei dem die Kaltumformung des lösungsgeglühten und abgeschreckten Erzeugnisses durch kontrolliertes Ziehen mit einer bleibenden Dehnung von 2 bis 5 % erfolgt, um nach der Auslagerung einen Zustand T8 zu erhalten.
  12. Verfahren nach Anspruch 9, bei dem
    - die Legierung zu Vormaterial für Drähte oder Stangenmaterial vergossen wird,
    - die Umformung vor dem Lösungsglühen durch Warm- und/oder Kaltpressen bzw. -ziehen zur Herstellung von Draht oder Stangenmaterial und wahlweise durch nachträgliches Schlagen des erhaltenen Drahtes oder Stangenmaterials erfolgt, um Schrauben, Bolzen oder Niete herzustellen,
    - keine Kaltumformung des lösungsgeglühten und abgeschreckten Erzeugnisses erfolgt,
    - der nach Auslagerung erhaltene Werkstoffendzustand ein Zustand T6 ist.
  13. Verwendung eines Kneterzeugnisses nach irgendeinem der Ansprüche 1 bis 7 in einer Anwendung, bei der das Erzeugnis auf Temperaturen von 100°C bis 200°C für eine signifikante Dauer von mindestens 200 Stunden gehalten wird.
  14. Verwendung nach Anspruch 13, wobei das Erzeugnis ein Befestigungsteil zur Verwendung in einem Motor insbesondere eines Kraftfahrzeugs, wie z. B. eine Schraube oder ein Bolzen oder ein Niet ist.
  15. Verwendung nach Anspruch 13, wobei das Erzeugnis ein Triebwerksgondel- und/oder -aufhängeteil eines Flugzeugs oder ein Flügelvorderkantenteil eines Flugzeugs oder ein Rumpfteil eines Überschallflugzeugs ist.
EP12717140.3A 2011-04-15 2012-04-06 Aluminium-kupfer-magnesium-legierungen mit guter leistung bei hohen temperaturen Active EP2697406B1 (de)

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Application Number Priority Date Filing Date Title
US201161475806P 2011-04-15 2011-04-15
FR1101187A FR2974118B1 (fr) 2011-04-15 2011-04-15 Alliages aluminium cuivre magnesium performants a haute temperature
PCT/FR2012/000134 WO2012140337A1 (fr) 2011-04-15 2012-04-06 Alliages aluminium cuivre magnesium performants a haute temperature

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EP2697406B1 true EP2697406B1 (de) 2017-09-13

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US (1) US9869008B2 (de)
EP (1) EP2697406B1 (de)
CN (1) CN103608478B (de)
BR (1) BR112013026381B1 (de)
CA (1) CA2832085C (de)
FR (1) FR2974118B1 (de)
WO (1) WO2012140337A1 (de)

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CN104164635A (zh) * 2013-05-17 2014-11-26 中国石油天然气集团公司 一种提高铝合金钻杆用Al-Cu-Mg合金室温强度和高温性能的方法
FR3040711B1 (fr) * 2015-09-03 2017-08-11 Constellium Issoire Produit extrude en alliage al-cu-mg a compromis ameliore entre resistance mecanique et tenacite
CN105112748A (zh) * 2015-09-08 2015-12-02 苏州慧驰轻合金精密成型科技有限公司 一种高强度铸造铝合金及其制备方法
CN105170765A (zh) * 2015-10-29 2015-12-23 无锡桥阳机械制造有限公司 一种镁合金加工工艺
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CN111235443A (zh) * 2020-03-30 2020-06-05 天津忠旺铝业有限公司 一种低加工变形2系铝合金板材的制备方法
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CN103608478A (zh) 2014-02-26
WO2012140337A1 (fr) 2012-10-18
FR2974118A1 (fr) 2012-10-19
EP2697406A1 (de) 2014-02-19
US9869008B2 (en) 2018-01-16
CN103608478B (zh) 2015-11-25
BR112013026381A2 (pt) 2016-12-27
CA2832085A1 (fr) 2012-10-18
CA2832085C (fr) 2019-02-26
FR2974118B1 (fr) 2013-04-26
US20120261036A1 (en) 2012-10-18
BR112013026381B1 (pt) 2019-06-25

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