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
  • 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
• • 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
• • 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 aluminum-copper-magnesium alloy products, more particularly such products, their manufacturing processes and use, intended to be carried out at high temperature.
• Certain aluminum alloys are commonly used for applications in which they have a high working temperature, typically between 80 and 250 ° C and generally between 100 and 200 ° C, for example as a structural part or as a medium. 'Attaches near an engine in the automotive or aerospace industry or as rotors or other air suction pump parts such as vacuum pumps.
• the good mechanical performance at high temperature signifies 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 temperature of use, and of on the other hand the hot performance, that is to say that the mechanical properties measured at high temperature (static mechanical properties, creep resistance) are high.
• Patent FR 2279852 proposes an alloy with a reduced iron and nickel content of the following composition (% by weight):
• the alloy may also contain Zr, Mn, Cr, V or Mo at contents of less than 0.4%, and optionally Cd, In, Sn or Be at less than 0.2% each, Zn at less than 8% or Ag is less than 1%. With this alloy, a significant improvement is obtained in the stress concentration factor Klc representative of the resistance to crack propagation.
• the patent application EP 0756017 A1 relates to an aluminum alloy with high creep resistance of composition (% by weight): Cu: 2.0 - 3.0 Mg: 1.5 - 2.1 Mn: 0, 3 - 0.7
• Patent RU2210614C1 describes an alloy of composition (in% by weight): Cu: 3.0 - 4.2 Mg: 1.0 - 2.2 Mn: 0.1 - 0.8 Zr: 0.03 - 0, 2 Ti: 0.012 - 0.1, V: 0.001 - 0.15 at least one element among Ni: 0.001 - 0.25 and Co: 0.001 - 0.25, remainder aluminum.
• Patent application CN104164635 describes a process for improving the resistance at ambient temperature and the performance at high temperature of an Al-Cu-Mg alloy for an aluminum alloy drill rod.
• the process comprises the steps that the Al-Cu-Mg alloy is pre-stretched and deformed from 0 to 8% after the solution treatment, and then is heated at 160 ° C to 190 ° C, for four hours to 120 hours , then, the alloy is taken out of a furnace, air cooling is performed on the alloy, and the copper to magnesium content ratio 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.
• Patent application CN107354413 relates to a technique for preparing high strength heat resistant aluminum alloy material for petroleum exploration, and belongs to the technical field of heat treatment of aluminum alloy.
• the components of the alloy 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.
• RU2278179 C1 relates to aluminum-copper-magnesium alloys useful as structural materials in airspace art comprising (wt%) 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 member of the group containing silver 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.
• Patent application WO2020074818 relates to a thin sheet made of an 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.
• 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 resistance to heat and creep.
• the AA2219 alloy of 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.
• these alloys have insufficient mechanical properties for certain applications and also pose recycling problems, in particular due to the high content of iron and / or silicon and / or nickel and / or cobalt and / or vanadium.
• Al-Cu-Mg alloys are also known, which are most often in the T3 state, an economical metallurgical state which does not require any tempering heat treatment.
• US Pat. No. 3,826,688 teaches an alloy of composition (in% by weight), Cu: 2.9 - 3.7, Mg: 1.3 - 1.7 and Mn: 0.1 - 0.4.
• Patent application EP 0038605 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, at maximum 0.12 Si, 0.15 Fe, 0.25 Zn, 0.15Ti and 0.10 Cr.
• the object of the invention is the use of a wrought product in the T8 state of an aluminum alloy of composition, in% by weight,
• FIG. 1 Figure 1 shows the evolution of the tensile strength with the aging time at 150 ° C in hours.
• the static mechanical properties in traction in other words the tensile strength R m , the conventional yield strength at 0.2% elongation R p o , 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. The creep tests are carried out according to the ASTM E139-06 standard. Unless stated otherwise, the definitions of standard EN 12258 apply.
• the present inventors have observed that, surprisingly, there is a range of composition of Al-Cu-Mg alloys containing Mn which, when used in the T8 state, makes it possible to obtain wrought products which are particularly efficient at high temperature.
• 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.
• the breaking strength R m may be insufficient at ambient 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 the 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 observed that the simultaneous addition of manganese and zirconium can be advantageous in certain cases, in particular for reducing the sensitivity to aging at high temperature while achieving high mechanical properties.
• the Zr content is at most 0.15% by weight.
• the Zrest content at least equal to 0.07 in% by weight and preferably at least equal to 0.08 in% by weight.
• the products intended for the 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 the grains during casting. However, an addition greater than 0.05% by weight can result in excessive fineness of grain size which adversely affects creep resistance at elevated temperature.
• the iron and silicon contents are at most 0.20% by weight each.
• the iron content is at most 0.18% by weight and preferably 0.15% by weight.
• the silicon content is at most 0.15% by weight and preferably 0.10% by weight.
• the zinc content is at most 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 strength. However, the presence of zinc can pose recycling problems. In another embodiment, the zinc content is less than 0.20, more 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 typically unavoidable impurities.
• the rest is aluminum.
• the wrought products intended for the 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 the use according to the invention comprises the successive stages of production of the alloy, casting, optionally homogenization, hot deformation, dissolving, quenching, cold deformation and tempering.
• a liquid metal bath is produced so as to obtain an aluminum alloy of composition according to the invention.
• the liquid metal bath is then cast typically in the form of a rolling plate, spinning billet or forge 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, extruding 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 of 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 solution.
• Significant cold strain is typically a strain 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 of 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, 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 strength and to obtain, after tempering, a T8 state.
• the cold deformation can 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 realized in one or more stages.
• the tempering conditions are determined so that the mechanical strength Rpo, 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 the 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 of rectangular cross section with 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 being always the largest dimension of the elementary rectangle and B being able to be considered as the thickness of the elementary rectangle.
• the wrought products obtained according to the process of the invention have the advantage of exhibiting high mechanical strength and good performance at high temperature.
• the wrought products intended for the use according to the invention preferably exhibit in the longitudinal direction a tensile strength R m of at least 490 MPa and preferably of at least 495 MPa and having after aging at 150 ° C. for 100Oh, a tensile 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 the use according to the invention preferably have a duration necessary to reach a deformation of 0.35% during a creep test according to standard ASTM E139-06 for a stress of 250 MPa and at a temperature of 150 ° C of at least 700 hours and preferably at least 800 hours.
• the products for use according to the invention are particularly useful for applications in which the products are maintained at temperatures of 80 ° C to 250 ° C and preferably 100 ° C to 200 ° C, typically at about 150 ° C. ° C, for a significant period of at least 200 hours and preferably at least 2000 hours.
• the products intended for the use according to the invention are useful for applications of structural part or attachment means near an engine in the automotive industry or aerospace or preferably for applications of rotors or other parts in particular air suction pump impellers such as in particular vacuum pumps, such as in particular turbomolecular pumps or for applications of parts of air blowing devices such as impellers.
• Example 1 In this example 6 alloys were cast in the form of rolling plates. Alloys A and B have a composition according to the invention. Alloys C and E are taught by application 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.
• the plates were homogenized at a temperature between 490 ° C and 540 ° C, adapted according to the alloy, hot rolled to a thickness of 10 mm (alloy A) and 15 mm (alloys B to E) and 21 mm (alloy F), dissolved at a temperature between 490 ° C and 540 ° C, adapted according to the alloy, soaked in water by immersion, pulled from 2 to 4% and returned to 175 ° C or 190 ° C to reach the peak tensile yield strength in the state T8.
• the plates of alloy A and B were homogenized between 20 and 36 h at 495 ° C, the sheets obtained after rolling being placed in solution for 2 h at 498 ° C and tempering for 8 h at 190 ° C or 12 h at 175 ° C.
• the alloy C plate was homogenized in two stages of 10 h at 500 ° C then 20 h at 509 ° C, the sheet obtained after rolling being placed in solution for 2 h at 507 ° C and returning for 12 h at 190 ° C.
• the D alloy plate was homogenized in two stages of 10h at 500 ° C then 20h at
• the alloy E plate was homogenized in two stages of 10 h at 500 ° C then 20 h at 503 ° C, the sheet obtained after rolling being placed in solution for 2 h at 504 ° C and returning for 12 h at 190 ° C.
• the evolution of the breaking strength with the aging time at 150 ° C is shown in Figure 1.
• the products intended for the use according to the invention exhibit a higher breaking strength R m than that of the products of benchmark before aging and superior to most other alloys after 1000 hours at 150 ° C.
• the products intended for use according to the invention have a mechanical strength R m greater than that of the alloy F, which is an AA2618 alloy known for its properties at high temperature.
• Creep tests were carried out according to standard ASTM E139-06 for a stress of 285 MPa and at a temperature of 150 ° C (alloys C, E and F) and for a stress of 250 MPa and at a temperature of 150 ° C (alloys A, B and F) In particular, the time required to reach a deformation of 0.35% was measured. The results are collated in Table 3.
• the equivalent time t, at 150 ° C is defined by formula 1:
• T in Kelvin
• T ref is a reference temperature set at 423 K.
• t is expressed in hours.
• the aging was estimated for 233 h by linear approximation from the value of 426 MPa obtained after 100Oh.

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• Organic Chemistry (AREA)
• General Engineering & Computer Science (AREA)
• Crystallography & Structural Chemistry (AREA)
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• Powder Metallurgy (AREA)
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• Heat Treatment Of Steel (AREA)
• Structures Of Non-Positive Displacement Pumps (AREA)
• Applications Or Details Of Rotary Compressors (AREA)
• Compositions Of Macromolecular Compounds (AREA)
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• 2020
  • 2020-06-04 FR FR2005856A patent/FR3111143B1/fr active Active
• 2021
  • 2021-05-31 US US18/000,322 patent/US20230220530A1/en active Pending
  • 2021-05-31 WO PCT/FR2021/050981 patent/WO2021245345A1/fr unknown
  • 2021-05-31 KR KR1020227046352A patent/KR20230019884A/ko active Search and Examination
  • 2021-05-31 CA CA3184620A patent/CA3184620A1/fr active Pending
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