EP4162089B1 - Utilisation de produits en alliage aluminium cuivre magnesium performants a haute temperature - Google Patents

Utilisation de produits en alliage aluminium cuivre magnesium performants a haute temperature Download PDF

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EP4162089B1
EP4162089B1 EP21734420.9A EP21734420A EP4162089B1 EP 4162089 B1 EP4162089 B1 EP 4162089B1 EP 21734420 A EP21734420 A EP 21734420A EP 4162089 B1 EP4162089 B1 EP 4162089B1
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product
use according
alloy
hours
mpa
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German (de)
English (en)
French (fr)
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EP4162089A1 (fr
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Pablo LORENZINO
Lukasz Dolega
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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
    • 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
    • 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
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F04—POSITIVE - DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS FOR LIQUIDS OR ELASTIC FLUIDS
    • F04D—NON-POSITIVE-DISPLACEMENT PUMPS
    • F04D19/00—Axial-flow pumps
    • F04D19/02—Multi-stage pumps
    • F04D19/04—Multi-stage pumps specially adapted to the production of a high vacuum, e.g. molecular pumps
    • F04D19/042—Turbomolecular vacuum pumps
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F04—POSITIVE - DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS FOR LIQUIDS OR ELASTIC FLUIDS
    • F04D—NON-POSITIVE-DISPLACEMENT PUMPS
    • F04D29/00—Details, component parts, or accessories
    • F04D29/02—Selection of particular materials
    • F04D29/023—Selection of particular materials especially adapted for elastic fluid pumps
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
    • F05D2300/00—Materials; Properties thereof
    • F05D2300/10—Metals, alloys or intermetallic compounds
    • F05D2300/17—Alloys
    • F05D2300/173—Aluminium alloys, e.g. AlCuMgPb

Definitions

  • the invention relates to the use of products made of aluminum-copper-magnesium alloys, intended to be used at high temperatures.
  • Certain aluminum alloys are commonly used for applications in which they have a high operating temperature, typically between 80 and 250 °C and generally between 100 and 200 °C, for example as a structural part or means of attachment to proximity to motors in the automotive or aerospace industry or as rotors or other air suction pump parts such as vacuum pumps.
  • Good mechanical performance at high temperature means in particular, on the one hand, thermal stability, that is to say that the mechanical properties measured at room temperature are stable after long-term aging at the operating temperature, and on the other hand, on the other hand, hot performance, that is to say that the mechanical properties measured at high temperature (static mechanical properties, creep resistance) are high.
  • the AA2618 alloy which includes (% by weight): Cu:1.9-2.7 Mg:1.3-1.8 Fe:0.9-1.3, Ni:0.9-1.2 Si:0.10-0.25 Ti:0, 04-0.10 which was used for the manufacture of Concorde.
  • the patent FR 2279852 offers an alloy with a reduced iron and nickel content of the following composition (% by weight): Cu:1.8-3 Mg:1.2-2.7 Si ⁇ 0.3 Fe:0.1-0.4 Ni + Co: 0.1 - 0.4 (Ni + Co)/Fe: 0 .9 - 1.3
  • the alloy may also contain Zr, Mn, Cr, V or Mo at contents less than 0.4%, and possibly Cd, In, Sn or Be at less than 0.2% each, Zn at less than 8% or Ag has less than 1%. With this alloy we obtain a significant improvement in the stress concentration factor K1c representative of the resistance to crack propagation.
  • the alloys mentioned in this application are particularly useful for applications in which the products are maintained at temperatures of 100°C to 200°C, typically around 150°C.
  • the products mentioned in this application are useful for fastening parts intended for use in an automobile engine, such as screws or bolts or rivets or for the manufacture of nacelle parts and/or masts. aircraft hooking, the leading edges of aircraft wings and the fuselage of supersonic aircraft.
  • the patent application CN104164635 describes a method for improving the room temperature strength and high temperature performance of an Al-Cu-Mg alloy for an aluminum alloy drill pipe.
  • the process includes the steps that the Al-Cu-Mg alloy is pre-stretched and deformed by 0-8% after solution processing, and then heated to 160°C to 190°C, for four hours to 120 hours , then, the alloy is taken out of a furnace, air cooling is carried out on the alloy and the ratio of copper to magnesium content in the Al-Cu-Mg alloy is less than or equal to five, the composition of the alloy being, in % by weight, Cu: 4.0% ⁇ 4.3%, Mg: 1.5% ⁇ 1.6%, Mn: 0.4% ⁇ 0.6%, Ti: 0.1% ⁇ 0.15%, rest Al.
  • the patent application CN107354413 relates to a technique for preparing high-strength heat-resistant aluminum alloy material for oil exploration, and belongs to the technical field of heat treatment of aluminum alloy.
  • the alloy components are determined as Si ⁇ 0.35, Fe ⁇ 0.45, Cu 4.0-4.5, Mn 0.40-0.80, Mg 1.3-1.7, Zn ⁇ 0.10, Ti 0.08-0.20, Zr0.10-0.15 and other impurities 0.00-0.15.
  • the patent RU2278179 C1 relates to aluminum-copper-magnesium alloys useful as structural materials in airspace technology comprising (mass %) copper 3.8-5.5; magnesium 0.3-1.6; manganese 0.2-0.8; titanium 0.5.10 (-6) -0.07; tellurium 0.5.10 (-5) -0.01, at least one element from the silver-containing group 0.2-1.0; nickel 0.5.10 (-6) -0.05; zinc 0.5.10 (-6) -0.1; zirconium 0.05-0.3; chromium 0.05-0.3; iron 0.5.10 (-6) -0.15; silicon 0.5.10 (-6) -0.1; hydrogen 0.1.10 (-5) -2.7.10 (-5); and balance: aluminum.
  • the patent application WO2020074818 relates to a thin sheet of essentially recrystallized aluminum-based alloy with a thickness of between 0.25 and 12 mm comprising, in % by weight, Cu 3.4 - 4.0; Mg 0.5 - 0.8; Mn 0.1 - 0.7; Fe ⁇ 0.15; If ⁇ 0.15; Zr ⁇ 0.04; Ag ⁇ 0.65; Zn ⁇ 0.5; unavoidable impurities ⁇ 0.05 each and ⁇ 0.15 in total; remains aluminum.
  • the patent application US2004013529 relates to a mechanical vacuum pump comprising a rotor made of a light metal alloy obtained by powder metallurgy. Powder metallurgy increases the rotor's resistance to heat and creep.
  • AA2219 alloy with composition (in % by weight) Cu: 5.8 - 6.8 Mn: 0.20 - 0.40 Ti: 0.02 - 0.10, Zr: 0.10 - 0.25 V : 0.05 - 0.15 Mg ⁇ 0.02 is also known for high temperature applications.
  • the patent application EP 0 038 605 A1 teaches an alloy of composition (in % by weight), Cu: 3.8 - 4.4, Mg: 1.2 - 1.8 and Mn: 0.3 - 0.9, maximum 0.12 Si, 0 .15 Fe, 0.25 Zn, 0.15 Ti and 0.10 Cr.
  • FIG. 1 shows the evolution of the breaking strength with the aging time at 150 °C in hours.
  • the static mechanical characteristics in traction in other words the breaking strength R m , the conventional elastic limit 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 direction of the test being defined by standard EN 485-1. Hot tensile tests are carried out according to standard NF EN 10002-5. Creep tests are carried out according to standard ASTM E139-06. Unless otherwise stated, the definitions of EN 12258 apply.
  • the present inventors have noted that, surprisingly, there is a range of composition of Al-Cu-Mg alloys containing Mn which allows, when used in the T8 state, to obtain wrought products which are particularly efficient at high temperatures.
  • the magnesium content is such that Mg is between 1.2 and 1.4% by weight and preferably between 1.25 and 1.35% by weight.
  • Mg content is not in the range according to the invention, the mechanical properties are not satisfactory.
  • the breaking strength R m may be insufficient at room temperature and/or after aging at 150°C.
  • the copper content is such that Cu is between 3.6 and 4.4% by weight.
  • Advantageously Cu is at least 3.9% by weight and preferably at least 4.0% by weight.
  • Advantageously Cu is at most 4.3% by weight and preferably at most 4.25% by weight.
  • the products intended for use according to the invention contain 0.5 to 0.8% by weight of manganese which contributes in particular to the control of the granular structure.
  • the Mn content is between 0.51 and 0.65% by weight.
  • the present inventors have found that the simultaneous addition of manganese and zirconium can be advantageous in certain cases, in particular to reduce the sensitivity to aging at high temperatures while achieving high mechanical properties.
  • the Zr content is a maximum of 0.15% by weight.
  • the Zr content is at least equal to 0.07% by weight and preferably at least equal to 0.08% by weight.
  • the products intended for use according to the invention contain 0.09 to 0.15% by weight of zirconium and 0.50 to 0.60% by weight of manganese.
  • the titanium content is between 0.01 and 0.05% by weight.
  • the addition of titanium contributes in particular to the refining of grains during casting. However, an addition greater than 0.05% by weight can result in excessively fine grain size which impairs creep resistance at elevated temperatures.
  • the iron and silicon contents are a maximum of 0.20% by weight each.
  • the iron content is a maximum of 0.18% by weight and preferably 0.15% by weight.
  • the silicon content is a maximum of 0.15% by weight and preferably 0.10% by weight.
  • the zinc content is a maximum of 0.25% by weight. In one embodiment of the invention, the zinc content is between 0.05 and 0.25% by weight and can contribute in particular to the mechanical resistance. However, the presence of zinc can pose recycling problems. In another embodiment, the zinc content is less than 0.20, preferably less than 0.15% by weight.
  • the content of the other elements is less than 0.05% by weight and preferably less than 0.04% by weight. Preferably, the total of the other elements is less than 0.15% by weight.
  • the other elements are unavoidable impurities.
  • the rest is aluminum.
  • the wrought products intended for use according to the invention are preferably sheets, profiles or forged products.
  • the profiles are typically obtained by spinning.
  • Forged products can be obtained by forging cast blocks or extruded products or rolled products.
  • the process for manufacturing the products intended for use according to the invention comprises the successive stages of preparing the alloy, casting, optionally homogenization, hot deformation, solution, quenching, 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 or forging blank.
  • the product thus cast is then homogenized so as to reach a temperature of between 450°C and 520°C and preferably between 495°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 hot deformed typically by rolling, spinning and/or forging.
  • the hot deformation is carried out so as to preferably maintain a temperature of at least 300°C.
  • a temperature of at least 350°C and preferably at least 380°C is maintained during hot deformation.
  • No significant cold deformation is carried out, in particular by cold rolling, between hot deformation and solution application.
  • Significant cold deformation is typically a deformation of at least about 5%.
  • the product thus deformed is then put into solution by a heat treatment making it possible to reach a temperature between 485 and 520 ° C and preferably between 495 and 510 ° C for 15 min to 8 h, then quenched.
  • the quality of the solution can be evaluated by calorimetry and/or optical microscopy.
  • the wrought product obtained typically a sheet metal, a profile or a forged product, then undergoes cold deformation.
  • the cold deformation is a deformation of 2 to 5% making it possible to improve the mechanical resistance and to obtain a T8 state after tempering.
  • the cold deformation may in particular be a controlled tensile deformation leading to a T851 state or a compression deformation leading to a T852 state.
  • tempering is carried out 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 50 hours. In an advantageous embodiment, tempering is carried out in which the product reaches a temperature of between 170 and 180°C for 10 to 15 hours.
  • the income can be made in one or more stages.
  • the tempering conditions are determined so that the mechanical resistance Rp 0.2 is maximum (“peak” tempering). Tempering under the conditions according to the invention makes it possible in particular to improve the mechanical properties and their stability during aging at 150°C.
  • the thickness of the products intended for use according to the invention is advantageously between 6 mm and 300 mm, preferably between 10 and 200 mm.
  • a sheet is a rolled product with a rectangular cross section and a uniform thickness.
  • the thickness of the profiles is defined according to standard EN 2066:2001: the cross section is divided into elementary rectangles of dimensions A and B; A always being the largest dimension of the elementary rectangle and B can be considered as the thickness of the elementary rectangle.
  • the wrought products obtained according to the process have the advantage of having high mechanical strength and good performance at high temperatures.
  • the wrought products intended for use according to the invention preferably have in the longitudinal direction a breaking strength R m of at least 490 MPa and preferably at least 495 MPa and having after aging at 150°C for 1000 hours, a breaking strength R m of at least 475 MPa and preferably at least 480 MPa.
  • the wrought products intended for use according to the invention are resistant to creep.
  • the wrought products intended for use according to the invention preferably have a duration necessary to reach a deformation of 0.35% during a creep test according to the ASTM E139-06 standard for a stress of 250 MPa and at a temperature of 150°C for at least 700 hours and preferably at least 800 hours.
  • the products intended for use according to the invention are particularly useful for applications in which the products are maintained at temperatures of 100°C to 250°C and preferably of 100°C to 200°C, typically at about 150°C. °C, for a significant duration of at least 200 hours and preferably at least 2000 hours.
  • the products intended for use according to the invention are useful for applications of structural parts or means of attachment near the engine in the automobile industry or aerospace or preferably for applications of rotors or other parts in particular impellers of air suction pumps such as in particular vacuum pumps, such as in particular turbomolecular pumps or for applications of parts of air blowing devices such as impellers.
  • Alloy B has a composition according to the invention. Alloys C and E are taught by demand WO2012/140337 for their performance in high temperature uses. Alloy F is an AA2618 alloy, known for its performance in high temperature applications.
  • composition of the alloys in % by weight is given in Table 1. ⁇ b>[Table 1] ⁇ /b> Alloy If Fe Cu Mn Mg Neither Zn Ti Zr HAS 0.08 0.14 4.2 0.51 1.35 - 0.20 0.02 0.02 B (Invention) 0.04 0.07 4.0 0.58 1.40 - 0.12 0.02 0.10 C (Reference) 0.04 0.05 3.3 0.34 1.9 - - 0.02 0.11 D (Reference) 0.04 0.05 4.2 0.34 1.3 - - 0.02 0.11 E (Reference) 0.04 0.05 3.7 0.34 1.6 - - 0.02 0.11 F (Reference) 0.22 1.10 2.6 0.05 1.60 1.10 0.08 0.01 0.00
  • the plates were homogenized at a temperature between 490°C and 540°C, adapted depending on the alloy, hot rolled to a thickness of 10 mm (alloy A) and 15 mm (alloys B to E) and 21 mm (alloy F), put in solution at a temperature between 490 °C and 540 °C, adapted depending on the alloy, quenched in water by immersion, tensile from 2 to 4% and returned to 175 °C or 190 °C to reach the peak tensile yield strength in the state T8.
  • the alloy plates A and B were homogenized between 20 and 36 hours at 495°C, the sheets obtained after rolling being put in solution for 2 hours at 498°C and returned for 8 hours at 190°C or 12 hours at 175°C.
  • the alloy C plate was homogenized in two stages of 10 hours at 500 °C then 20 hours at 509 °C, the sheet obtained after rolling being put in solution for 2 hours at 507 °C and returned for 12 hours at 190 °C.
  • the alloy D plate was homogenized in two stages of 10 hours at 500 °C then 20 hours at 503 °C, the sheet obtained after rolling being put in solution for 2 hours at 500 °C and returned for 8 hours at 190 °C.
  • the alloy E plate was homogenized in two stages of 10 hours at 500 °C then 20 hours at 503 °C, the sheet obtained after rolling being put in solution for 2 hours at 504 °C and returned for 12 hours at 190 °C.
  • the evolution of the breaking strength with the aging time at 150 °C is represented on the Figure 1 .
  • the products intended for use according to the invention have a breaking strength R m greater than that of the reference products before aging and greater than most other alloys after 1000 hours at 150°C. After 3000 hours of aging, the products intended for use according to the invention have a mechanical resistance R m greater than that of alloy F, which is an AA2618 alloy known for its high temperature properties.
  • T (in Kelvin) is the instantaneous metal treatment temperature, which changes with time t (in hours)
  • T ref is a reference temperature fixed at 423 K.
  • t i is expressed in hours.
  • aging was estimated for 233 h by linear approximation from the value of 426 MPa obtained after 1000 h.
  • thermal stability of the product in the T851 state is much greater than the thermal stability in the T351 state.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • General Engineering & Computer Science (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Powder Metallurgy (AREA)
  • Applications Or Details Of Rotary Compressors (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Heat Treatment Of Steel (AREA)
  • Forging (AREA)
  • Compositions Of Macromolecular Compounds (AREA)
  • Structures Of Non-Positive Displacement Pumps (AREA)
EP21734420.9A 2020-06-04 2021-05-31 Utilisation de produits en alliage aluminium cuivre magnesium performants a haute temperature Active EP4162089B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR2005856A FR3111143B1 (fr) 2020-06-04 2020-06-04 Produits en alliage aluminium cuivre magnésium performants à haute température
PCT/FR2021/050981 WO2021245345A1 (fr) 2020-06-04 2021-05-31 Utilisation de produits en alliage aluminium cuivre magnesium performants a haute temperature

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EP4162089A1 EP4162089A1 (fr) 2023-04-12
EP4162089B1 true EP4162089B1 (fr) 2024-03-20

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US (1) US20230220530A1 (ja)
EP (1) EP4162089B1 (ja)
JP (1) JP2023533152A (ja)
KR (1) KR20230019884A (ja)
CN (1) CN115698356A (ja)
BR (1) BR112022023160A2 (ja)
CA (1) CA3184620A1 (ja)
FR (1) FR3111143B1 (ja)
WO (1) WO2021245345A1 (ja)

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Publication number Priority date Publication date Assignee Title
CN115323294B (zh) * 2022-06-30 2023-07-14 广西科技大学 一种Al-Cu-Mg合金的强塑性变形方法
CN115466889B (zh) * 2022-09-02 2023-05-23 中国航发北京航空材料研究院 一种高强韧、高抗疲劳铝合金及其制备方法
EP4151860A3 (de) * 2022-12-22 2023-04-05 Pfeiffer Vacuum Technology AG Vakuumpumpe

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FR2279852B1 (fr) 1974-07-23 1977-01-07 Cegedur Transf Aumin Pechiney Alliage d'aluminium de bonne tenue au fluage et de resistance a la propagation des criques amelioree
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FR2974118B1 (fr) 2011-04-15 2013-04-26 Alcan Rhenalu Alliages aluminium cuivre magnesium performants a haute temperature
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FR3087206B1 (fr) * 2018-10-10 2022-02-11 Constellium Issoire Tôle en alliage 2XXX à haute performance pour fuselage d’avion

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US20230220530A1 (en) 2023-07-13
CN115698356A (zh) 2023-02-03
EP4162089A1 (fr) 2023-04-12
KR20230019884A (ko) 2023-02-09
FR3111143A1 (fr) 2021-12-10
JP2023533152A (ja) 2023-08-02
FR3111143B1 (fr) 2022-11-18
CA3184620A1 (fr) 2021-12-09
BR112022023160A2 (pt) 2022-12-20
WO2021245345A1 (fr) 2021-12-09

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