EP0375571A1 - Process for the preparation by spray deposits of aluminium alloys of the 7000 series, and discontinuously reinforced composite materials having these high strength, highly ductile alloys as a matrix - Google Patents

Process for the preparation by spray deposits of aluminium alloys of the 7000 series, and discontinuously reinforced composite materials having these high strength, highly ductile alloys as a matrix Download PDF

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EP0375571A1
EP0375571A1 EP89420497A EP89420497A EP0375571A1 EP 0375571 A1 EP0375571 A1 EP 0375571A1 EP 89420497 A EP89420497 A EP 89420497A EP 89420497 A EP89420497 A EP 89420497A EP 0375571 A1 EP0375571 A1 EP 0375571A1
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alloys
alloy
composition
series
spray
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EP0375571B1 (en
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Jean-François Faure
Bruno Dubost
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Pechiney Recherche GIE
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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
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • C22C1/0416—Aluminium-based alloys
    • 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
    • C22F1/053—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 zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
    • C23C4/18—After-treatment

Definitions

  • the invention relates to a process for obtaining an Al alloy of the 7000 series (Al-Zn-Mg-Cu) with high mechanical strength and good ductility by "spray-deposition" (spray deposition). More specifically, the method aims to obtain Al alloys which have in the treated state (T6) a breaking load ⁇ 800 MPa with an elongation, at least in the long direction, greater than or equal to 5%.
  • the invention also relates to obtaining composite materials with very high strength, high rigidity and good ductility having as matrix the 7000 alloys described above with a particulate reinforcement of ceramics and obtained directly by "spray-deposition".
  • spray-deposition is meant a process in which the metal is melted, atomized by a jet of gas at high pressure in the form of fine liquid droplets which are then directed and agglomerated on a substrate so as to form a massive and coherent deposit, containing low closed porosity.
  • This deposit can be in the form of billets, tubes or plates whose geometry is controlled.
  • a technique of this type is known as “Spray Deposition” by the Anglo-Saxons and is also called “OSPREY process”.
  • the volume fraction of precipitates at the base of the structural hardening of the alloy (essentially of the type ⁇ -Mg Zn2 or ⁇ ′ - (Mg, Zn, Al, Cu)) becomes insufficient and it is no longer possible to obtain the high levels of mechanical characteristics (such as breaking load ⁇ 800 MPa) which are the objective of the present invention.
  • the volume fraction of the second phase is too high and leads to a brittle material, with very low elongations at break, which prohibits its industrial use.
  • the copper and magnesium contents must be in proportions close to the stoichiometry of the hardening precipitates.
  • Mg ⁇ 2% or Cu ⁇ 0.5% the nature and the volume fraction of the precipitates formed are insufficient to achieve the targeted mechanical characteristics.
  • Mg is ⁇ 4% or Cu ⁇ 2.0%, these elements are present in excess in the alloy and weaken it considerably.
  • the preferred composition is: Zn from 8.7 to 13.7% 2.2 to 3.8% mg Cu from 0.6 to 1.6% at least one of the following 3 elements: Zr from 0.05 to 0.5% Mn from 0.05 to 0.8% Cr from 0.05 to 0.5% with Zr + Mn + Cr ⁇ 1.2% Fe up to 0.3% If up to 0.2% other (impurities) ⁇ 0.05% each ⁇ 0.15% total remains Al.
  • the content of main elements preferably obeys the following relationship, 5.5 ⁇ Mg + Cu + Zn 6 ⁇ 6.5
  • the hot transformation of the solid alloy obtained by spray-deposition generally takes place between 300 and 450 ° C, preferably by spinning, forging or rolling, in one or more successive operations; these operations may possibly be combined, for example spinning + rolling or spinning + forging / stamping.
  • the hot transformation operations can be supplemented by cold operations such as rolling, drawing, etc.
  • the solution is carried out between 440 and 520 ° C, between 2 and 8 hours depending on the size of the products; quenching is followed by tempering between 2 and 25 h between 90 and 150 ° C in one or more stages, the longest times generally being associated with the lowest temperatures (and vice-versa).
  • the product obtained by a spray-deposition process can optionally be homogenized before hot transformation between 450 and 520 ° C for 2 to 50 hours in one or more stages.
  • the invention also consists, using the alloys and the method described above, in obtaining composite materials with very high resistance (Rm ⁇ 800 MPa), high Young modulus (E ⁇ 80 GPa), with acceptable ductility by users (A ⁇ 3%), as well as good resistance to wear and friction.
  • These materials are characterized by an alloy matrix of the 7xxx series of composition indicated above and a dispersion of ceramic particles of SiC, Al2O3 or B4C type (these examples not being limiting) and are obtained directly by the spray-deposition technique.
  • the blanks are then hot-spun at 400 ° C in a press whose container has a diameter of 143 mm in the form of flats of section 50 x 22 mm, ie a spinning ratio of 14.6.
  • the flats thus obtained are then dissolved at the temperature indicated in Table 1 for 2 h, quenched in cold water and then returned for 24 h at 120 ° C.
  • the mechanical tensile characteristics in the long direction, average of 3 tests, are reported in Table 2 (Ro, 2: elastic limit at 0.2% residual deformation, Rm: breaking load; A%: elongation at break).
  • alloys No. 1 to 4 according to the invention exhibit a very high level of mechanical properties, in particular with a tensile strength of ⁇ 800 MPa and a correct level of ductility, with elongations at rupture ⁇ 5% .
  • Alloy 5 outside the analytical limits of the invention (Zn content too low) has much weaker mechanical characteristics than the alloys of the invention.
  • Alloy 6 also outside the limits of the invention due to its too high Zn content, has a very low ductility (A%) and a plastic difference (Rm- R 0.2).
  • Alloy 8 is an alloy whose composition falls within the analytical field of the alloys of the invention but which has been developed according to a powder metallurgy process described below: the alloy is melted and then atomized with nitrogen in the form powders; these are collected and sieved to 100 ⁇ m. Powders smaller than 100 ⁇ m are put in 140 mm diameter aluminum containers fitted with an orifice tube and are then degassed hot under secondary vacuum (by pumping through the tube) at a temperature of 460 ° C for 100 h. The powder containers thus degassed are sealed and then hot pressed in a blind die spinning press in a 143 mm diameter container at 450 ° C so as to reach the theoretical density of the material.
  • the billets thus obtained are then machined in order to remove the material from the container and then spun under the same conditions as the billets of the previous examples.
  • the product obtained is heat treated according to a similar procedure (see solution temperature in Table 1) and is characterized under the same conditions.
  • the results reported in Table 1 show that the product obtained has very low ductility and plastic difference despite a relatively high level of resistance.
  • An alloy of composition Al Al: 10% Zn; 3.0% Mg; 1.0% Cu; 0.1% Zr; 0.15% Cr; 0.15% Mn, rest Al was melted at 750 ° C and produced by spray-deposition in the form of 150 mm diameter billets with simultaneous coinjection of SiC particles of average size 10 ⁇ m, with a volume fraction of 15%.
  • the spray-deposit conditions were as follows: - metal flow: 5.8 kg / min. - gas flow: 15 Nm3 / min. - atomizer-deposit distance: 620 mm, kept approximately constant during the test - stainless steel collector with rotating movement - oscillation of the atomizer relative to the axis of rotation of the collector
  • the billets thus obtained are then peeled to ⁇ 140 mm, homogenized for 8 hours at 470 ° C, hot spun at 400 ° C in the form of flats with a section of 50 x 22 mm (spinning ratio 14.6).
  • the spray-deposition process according to the invention in addition to the best compromise of mechanical characteristics obtained, has the following advantages over conventional powder metallurgy: - long and costly degassing and compaction operations are avoided - the method is safer, since there is no handling of reactive powders.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Plasma & Fusion (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Coating By Spraying Or Casting (AREA)
  • Forging (AREA)
  • Conductive Materials (AREA)
  • Wrappers (AREA)
  • Laminated Bodies (AREA)

Abstract

The invention relates to a process for obtaining an Al alloy of the 7000 series (Al-Zn-Cu-Mg) of high mechanical strength and good ductility by spray deposition; the process is aimed at obtaining Al alloys having a breaking load of >/= 800 MPa and an elongation greater than or equal to 5%, or obtaining these same alloys reinforced with ceramic particles. <??>The invention accordingly consists in: 1. forming, by spray deposition, a massive alloy of the following composition by weight: Zn from 8.5 to 15%; Mg from 2.0 to 4.0%; Cu from 0.5 to 2.0%; at least one of the following 3 elements: Zr from 0.05 to 0.8%; Mn from 0.05 to 1.0%; Cr from 0.05 to 0.8%, with Zr + Mn + Cr </= 1.4%; Fe up to 0.5%; Si up to 0.5%; other elements </= 0.05% each, </= 0.15% in total; remainder Al. 2. hot transforming of the body thus obtained at between 300 and 450 DEG C and optionally in the cold and 3. treating the product thus obtained by dissolution, quenching and annealing.

Description

L'invention concerne un procédé d'obtention d'un alliage d'Al de la série 7000 (Al-Zn-Mg-Cu) à haute résistance mécanique et bonne ductilité par "pulvérisation -dépôt" (spray deposition). De façon plus précise, le procédé vise à obtenir des alliages d'Al qui possèdent à l'état traité (T6) une charge de rupture ≧ 800 MPa avec un allongement, au moins dans le sens long, supérieur ou égal à 5%.The invention relates to a process for obtaining an Al alloy of the 7000 series (Al-Zn-Mg-Cu) with high mechanical strength and good ductility by "spray-deposition" (spray deposition). More specifically, the method aims to obtain Al alloys which have in the treated state (T6) a breaking load ≧ 800 MPa with an elongation, at least in the long direction, greater than or equal to 5%.

L'invention concerne également l'obtention de matériaux composites à très haute résistance, haute rigidité et bonne ductilité ayant pour matrice les alliages 7000 décrits ci-dessus avec un renfort particulaire de cérami­ques et obtenus directement par "pulvérisation-dépôt".The invention also relates to obtaining composite materials with very high strength, high rigidity and good ductility having as matrix the 7000 alloys described above with a particulate reinforcement of ceramics and obtained directly by "spray-deposition".

De nombreux travaux ont déjà été réalisés sur les alliages de la série 7000, chargés en éléments d'alliage en vue d'obtenir de hautes résistances mécaniques associés à une bonne ductilité, soit par métallurgie classique, soit par la métallurgie des poudres.Many works have already been carried out on the alloys of the 7000 series, loaded with alloying elements with a view to obtaining high mechanical strengths associated with good ductility, either by conventional metallurgy or by powder metallurgy.

Ainsi, dans le premier cas, on connaît les brevets français FR 2517702 ou FR 2457908 dans lesquels sont présentés des alliages de la série 7000 ne dépassant pas une charge de rupture de 650-700 MPa environ, avec un allongement de l'ordre de 8-9% (dans le sens long).Thus, in the first case, we know the French patents FR 2517702 or FR 2457908 in which are presented alloys of the 7000 series not exceeding a breaking load of 650-700 MPa approximately, with an elongation of the order of 8 -9% (in the long sense).

On a aussi cherché à obtenir des alliages de la série 7000 à haute résis­tance par la métallurgie des poudres, c'est-à-dire par un procédé compor­tant la formation de particules (poudres, paillettes, ruban broyé, etc...) qui sont ensuite consolidés sous forme massive par diverses méthodes (compressions à froid, à chaud, isostatique, filage, etc...).Attempts have also been made to obtain alloys of the 7000 series with high resistance by powder metallurgy, that is to say by a process comprising the formation of particles (powders, flakes, ground ribbon, etc.) which are then consolidated in massive form by various methods (cold, hot, isostatic compressions, spinning, etc.).

Cependant, ces alliages bien qu'atteignant de hautes ou très hautes résis­tances mécaniques, possèdent des allongements très faibles, qui en interdi­sent tout emploi industriel.However, these alloys although reaching high or very high mechanical strengths, have very low elongations, which prohibit any industrial use.

C'est ainsi que HAAR rapporte dans Alcoa Report no 13-65-AP59-S- Contract no DA-360-034-ORD-3559 RD (Frankfort Arsenal), mai 1966, des charges de rupture dépassant 800 MPa mais avec des allongements de l'ordre de 1%. De même, BOWER et al- Met. Trans. Vol. 1, janvier 1970, p.191 - rapporte, sur des alliages de la même famille, élaborés par "splat cooling" (technique marteau et enclume) des charges de rupture de 800 MPa, mais avec des allon­gements de 2%.Thus HAAR Alcoa reports in Report No. 13-65-AP59-S Contract No. DA-360-034-ORD-3559 RD (Frankfort Arsenal), May 1966 breaking loads exceeding 800 MPa but with extensions of around 1%. Likewise, BOWER et al- Met. Trans. Flight. 1, January 1970, p.191 - reports, on alloys of the same family, produced by "splat cooling" (hammer and anvil technique) breaking loads of 800 MPa, but with elongations of 2%.

Les brevets US 3563814 et US 4732610 sont relatifs à des alliages de la même famille obtenus par métallurgie des poudres mais dont les caractéristi­ques mécaniques sont nettement inférieures aux objectifs visés (charge de rupture de l'ordre de 500 MPa à 600 MPa).US patents 3,563,814 and US 4,732,610 relate to alloys of the same family obtained by powder metallurgy but whose mechanical characteristics are clearly lower than the targeted objectives (breaking load of the order of 500 MPa to 600 MPa).

L'invention consiste donc :

  • 1. à former par pulvérisation-dépôt un alliage massif de composition pondé­rale suivante :
    Zn 8,5 à 15 %
    Mg 2,0 à 4,0 %
    Cu 0,5 à 2,0 %
    au moins un des 3 éléments suivants :
    Zr de 0,05 à 0,8 %
    Mn de 0,05 à 1,0 %
    Cr de 0,05 à 0,8 %
    avec Zr + Mn + Cr ≦ 1,4%
    Fe jusqu'à 0,5 %
    Si jusqu'à 0,5 %
    Autres (impuretés)
    ≦0,05 % chacune
    ≦0,15 % au total
    reste Al.
  • 2. à transformer à chaud le corps ainsi obtenu entre 300 et 450°C et éven­tuellement à froid.
  • 3. à traiter thermiquement le produit obtenu par mise en solution, trempe et revenu.
The invention therefore consists of:
  • 1. to form by spray-deposition a solid alloy of the following weight composition:
    Zn 8.5 to 15%
    Mg 2.0 to 4.0%
    Cu 0.5 to 2.0%
    at least one of the following 3 elements:
    Zr from 0.05 to 0.8%
    Mn from 0.05 to 1.0%
    Cr from 0.05 to 0.8%
    with Zr + Mn + Cr ≦ 1.4%
    Fe up to 0.5%
    If up to 0.5%
    Others (impurities)
    ≦ 0.05% each
    ≦ 0.15% in total
    remains Al.
  • 2. to transform the body thus obtained between 300 and 450 ° C hot and possibly cold.
  • 3. heat treating the product obtained by dissolving, quenching and tempering.

Par pulvérisation-dépôt, on entend un procédé dans lequel le métal est fondu, atomisé par un jet de gaz à haute pression sous forme de fines gouttelettes liquides qui sont ensuite dirigées et agglomérées sur un substrat de manière à former un dépôt massif et cohérent, contenant une faible porosité fermée. Ce dépôt peut se présenter sous la forme de billet­tes, tubes ou plaques dont la géométrie est contrôlée. Une technique de ce type est désignée sous le nom de "Spray Deposition" par les anglo-saxons et est également dénommée "procédé OSPREY".
Ce dernier procédé est principalement décrit dans les demandes de brevets (ou brevets) suivants : GB-B-1379261; GB-B-1472939; GB-B-1548616; GB-B-­1599392; GB-A-2172827; EP-A-225080; EP-A-225732; WO-A-87-03012.By spray-deposition is meant a process in which the metal is melted, atomized by a jet of gas at high pressure in the form of fine liquid droplets which are then directed and agglomerated on a substrate so as to form a massive and coherent deposit, containing low closed porosity. This deposit can be in the form of billets, tubes or plates whose geometry is controlled. A technique of this type is known as "Spray Deposition" by the Anglo-Saxons and is also called "OSPREY process".
This latter process is mainly described in the following patent applications (or patents): GB-B-1379261; GB-B-1472939; GB-B-1548616; GB-B-1599392; GB-A-2172827; EP-A-225080; EP-A-225732; WO-A-87-03012.

Les meilleures caractéristiques mécaniques (Rm ≧ 800 MPa, A ≧ 5%) sont obtenues pour la composition donnée ci-dessus.The best mechanical characteristics (Rm ≧ 800 MPa, A ≧ 5%) are obtained for the composition given above.

Si Zn ≦ 8,5% en poids, la fraction volumique de précipités à la base du durcissement structural de l'alliage (essentiellement du type η -Mg Zn₂ ou η′-(Mg,Zn,Al,Cu)) devient insuffisante et il n'est plus possible d'obtenir les niveaux de caractéristiques mécaniques élevés (tels que charge de rupture ≧ 800 MPa) qui sont l'objectif de la présente invention.If Zn ≦ 8.5% by weight, the volume fraction of precipitates at the base of the structural hardening of the alloy (essentially of the type η -Mg Zn₂ or η ′ - (Mg, Zn, Al, Cu)) becomes insufficient and it is no longer possible to obtain the high levels of mechanical characteristics (such as breaking load ≧ 800 MPa) which are the objective of the present invention.

De même, si la teneur en Zn dépasse 15% en poids, la fraction volumique de seconde phase est trop élevée et conduit à un matériau fragile, avec des allongements à rupture très faibles, ce qui interdit son emploi industriel.Similarly, if the Zn content exceeds 15% by weight, the volume fraction of the second phase is too high and leads to a brittle material, with very low elongations at break, which prohibits its industrial use.

A l'intérieur de l'intervalle 8 à 15% en poids de zinc, les teneurs en cuivre et magnésium doivent se situer dans des proportions proches de la stoechiométrie des précipités durcissants. En pratique, on constate que lorsque Mg < 2% ou Cu < 0,5%, la nature et la fraction volumique des précipités formés sont insuffisantes pour atteindre les caractéristiques mécaniques visées. Lorsque, au contraire, Mg est ≧ 4% ou Cu ≧ 2,0%, ces éléments sont présents en excès dans l'alliage et le fragilisent considérab­lement.
La présence de Cr, Zr, Mn, seuls ou en association, assure un durcissement supplémentaire soit par effet de fibrage en empêchant ou limitant la recris­tallisation pouvant intervenir lors du traitement thermique suivant les opérations de transformation par corroyage, soit par un mécanisme de durcis­sement par dispersion, vu que ces éléments forment en combinaison avec l'aluminium des phases dispersées fines et bien réparties (par exemple Al₃Zr, Al₆Mn, ou des phases ternaires Al₁₈Cr₂Mg₃ et (Al,Cr,Mn). Toutefois, leur teneur doit être limitée à 0,8% pour Cr et Zr et à 1,0% pour Mn et leur teneur globale (Zr+Cr+Mn) ≦ 1,4% car au-delà, les phases dispersées formées sont trop nombreuses et trop grossières et fragilisent par conséquent le matériau. De plus des teneurs en Cr,Zr et Mn supérieures aux limites indiquées ci-dessus conduisent à des températures de liquidus élevées des alliages, ce qui pose des problèmes d'élaboration liés en particulier à la sublimation du zinc ou du magnésium. Les teneurs en fer et silicium sont limitées supérieurement à 0,5%, car au-delà se forment des composés intermétalliques grossiers qui nuisent à la ductilité de l'alliage.Within the range 8 to 15% by weight of zinc, the copper and magnesium contents must be in proportions close to the stoichiometry of the hardening precipitates. In practice, it is found that when Mg <2% or Cu <0.5%, the nature and the volume fraction of the precipitates formed are insufficient to achieve the targeted mechanical characteristics. When, on the contrary, Mg is ≧ 4% or Cu ≧ 2.0%, these elements are present in excess in the alloy and weaken it considerably.
The presence of Cr, Zr, Mn, alone or in combination, provides additional hardening either by fiberizing effect by preventing or limiting the recrystallization which may occur during the heat treatment according to the transformation operations by wrought, either by a dispersion hardening mechanism, since these elements form in combination with aluminum thin and well distributed dispersed phases (for example Al₃Zr, Al₆Mn, or ternary phases Al₁₈Cr₂Mg₃ and (Al, Cr , Mn) .However, their content must be limited to 0.8% for Cr and Zr and to 1.0% for Mn and their overall content (Zr + Cr + Mn) ≦ 1.4% because beyond, the the dispersed phases formed are too numerous and too coarse and consequently embrittle the material, in addition, Cr, Zr and Mn contents greater than the limits indicated above lead to high liquidus temperatures of the alloys, which poses problems of development linked in particular to the sublimation of zinc or magnesium The iron and silicon contents are limited to more than 0.5%, because beyond that coarse intermetallic compounds are formed which harm the ductility of the alloy.

La composition préférentielle est :
Zn de 8,7 à 13,7%
Mg de 2,2 à 3,8%
Cu de 0,6 à 1,6%
au moins un des 3 éléments suivants :
Zr de 0,05 à 0,5%
Mn de 0,05 à 0,8%
Cr de 0,05 à 0,5%
avec Zr + Mn + Cr ≦ 1,2%
Fe jusqu'à 0,3%
Si jusqu'à 0,2%
autres (impuretés)
≦ 0,05% chacun
≦ 0,15% total
reste Al.The preferred composition is:
Zn from 8.7 to 13.7%
2.2 to 3.8% mg
Cu from 0.6 to 1.6%
at least one of the following 3 elements:
Zr from 0.05 to 0.5%
Mn from 0.05 to 0.8%
Cr from 0.05 to 0.5%
with Zr + Mn + Cr ≦ 1.2%
Fe up to 0.3%
If up to 0.2%
other (impurities)
≦ 0.05% each
≦ 0.15% total
remains Al.

En vue de l'obtention de meilleurs résultats, la teneur en éléments princi­paux obéit, de préférence, à la relation suivante,
5,5 ≦ Mg + Cu + Zn 6

Figure imgb0001
≦ 6,5In order to obtain better results, the content of main elements preferably obeys the following relationship,
5.5 ≦ Mg + Cu + Zn 6
Figure imgb0001
 ≦ 6.5

C'est en effet dans ce domaine de composition que la fraction volumique des phases durcissantes est maximale tout en permettant une mise en solution complète des éléments d'addition lors du traitement thermique.It is indeed in this area of composition that the volume fraction of the hardening phases is maximum while allowing complete dissolution of the addition elements during the heat treatment.

Ainsi, un très haut niveau de résistance mécanique peut être atteint tout en conservant une bonne ductilité.
En ce qui concerne l'effet des éléments formant des dispersoïdes (Zr, Cr, Mn), on s'est rendu compte qu'il était préférable de les utiliser tous les 3 en association plutôt que l'un ou l'autre séparément. En effet, pour une teneur globale en Zr + Cr + Mn donnée, on obtient une distribution de dispersoïdes plus fins et mieux répartis lorsque les 3 éléments sont présents simultanément plutôt que seulement 1 ou 2 des 3. Lorsque les 3 éléments sont associés, on a cependant intérêt à limiter leur teneur globale à 1,2%. Plus précisément, on constate que pour une teneur identique, Zr conduit à la formation de dispersoïdes (Al₃Zr) plus fins et mieux répar­tis que ceux formés à partir de Cr ou Mn; on est donc conduit, lorsque la ductilité et la ténacité de l'alliage doivent être maximisés à limiter la teneur en Mn + Cr à 0,6% maximum.Thus, a very high level of mechanical strength can be achieved while retaining good ductility.
With regard to the effect of the dispersoid forming elements (Zr, Cr, Mn), it has been realized that it was preferable to use them all 3 in combination rather than one or the other separately. Indeed, for a given overall content of Zr + Cr + Mn, we obtain a distribution of finer and better distributed dispersoids when the 3 elements are present simultaneously rather than only 1 or 2 of 3. When the 3 elements are associated, we However, it is in their interest to limit their overall content to 1.2%. More precisely, we note that for an identical content, Zr leads to the formation of dispersoids (Al₃Zr) finer and better distributed than those formed from Cr or Mn; one is therefore led, when the ductility and the toughness of the alloy must be maximized to limit the Mn + Cr content to 0.6% maximum.

La transformation à chaud de l'alliage massif obtenu par pulvérisation-­dépôt a généralement lieu entre 300 et 450°C, de préférence par filage, forgeage ou laminage, en une ou plusieurs opérations successives; ces opérations peuvent éventuellement être combinées par exemple filage + laminage ou filage + forgeage/matriçage.
Les opérations de transformation à chaud peuvent être complétées par des opérations à froid telles que laminage, étirage, etc...
La mise en solution est effectuée entre 440 et 520°C, entre 2 et 8h suivant la taille des produits; la trempe est suivie d'un revenu entre 2 et 25 h entre 90 et 150°C en un ou plusieurs paliers, les temps les plus longs étant généralement associés aux températures les moins élevées (et vice-­versa).
Le produit obtenu par un procédé de pulvérisation-dépôt peut éventuellement être homogénéisé avant transformation à chaud entre 450 et 520°C pendant 2 à 50h en un ou plusieurs paliers.The hot transformation of the solid alloy obtained by spray-deposition generally takes place between 300 and 450 ° C, preferably by spinning, forging or rolling, in one or more successive operations; these operations may possibly be combined, for example spinning + rolling or spinning + forging / stamping.
The hot transformation operations can be supplemented by cold operations such as rolling, drawing, etc.
The solution is carried out between 440 and 520 ° C, between 2 and 8 hours depending on the size of the products; quenching is followed by tempering between 2 and 25 h between 90 and 150 ° C in one or more stages, the longest times generally being associated with the lowest temperatures (and vice-versa).
The product obtained by a spray-deposition process can optionally be homogenized before hot transformation between 450 and 520 ° C for 2 to 50 hours in one or more stages.

L'invention consiste également, en utilisant les alliages et la méthode décrits ci-dessus, à obtenir des matériaux composites à très haute résistan­ce (Rm ≧ 800 MPa), haut module d'Young (E ≧ 80 GPa), avec une ductilité acceptable par les utilisateurs (A ≧ 3%), ainsi qu'une bonne résistance à l'usure et au frottement. Ces matériaux se caractérisent par une matrice en alliage de la série 7xxx de composition indiquée cidessus et d'une dispersion des particules céramiques de type SiC, Al₂O₃ ou B₄C (ces exemples n'étant pas limitatifs) et sont obtenus directement par la technique de pulvérisation-dépôt.The invention also consists, using the alloys and the method described above, in obtaining composite materials with very high resistance (Rm ≧ 800 MPa), high Young modulus (E ≧ 80 GPa), with acceptable ductility by users (A ≧ 3%), as well as good resistance to wear and friction. These materials are characterized by an alloy matrix of the 7xxx series of composition indicated above and a dispersion of ceramic particles of SiC, Al₂O₃ or B₄C type (these examples not being limiting) and are obtained directly by the spray-deposition technique.

L'invention consiste donc:

  • 1/ A fondre et à pulvériser un alliage 7000 de composition décrite ci-­dessus
  • 2/ A coinjecter, dans le jet de gouttelettes métalliques atomisées des particules céramiques de type SiC, Al₂O₃, B₄C ou autres carbures, nitrures ou oxydes ou combinaison de ceux-ci, de forme sensiblement équiaxe et de taille comprise entre 1 µm et 50 µm et en fraction volumique, relative au métal, comprise entre 3 et 28%. Par taille on entend la dimension hors tout maximale de la particule.
  • 3/ A agglomérer le jet de particules métalliques et céramiques sous la forme d'un métal massif par la technique de pulvérisation-dépôt.
  • 4/ A transformer et traiter thermiquement le dépôt ainsi obtenu par une procédure analogue à celle décrite pour les alliages 7000 ci-dessus non renforcés.
The invention therefore consists of:
  • 1 / To melt and spray an alloy 7000 of the composition described above
  • 2 / To co-inject, in the jet of atomized metal droplets, ceramic particles of the SiC, Al nitrO₃, B₄C or other carbides, nitrides or oxides type or combination thereof, of substantially equiaxial shape and of size between 1 μm and 50 μm and in volume fraction, relating to the metal, between 3 and 28%. By size is meant the maximum overall dimension of the particle.
  • 3 / To agglomerate the jet of metallic and ceramic particles in the form of a solid metal by the spray-deposition technique.
  • 4 / To transform and heat treat the deposit thus obtained by a procedure similar to that described for the 7000 alloys above not reinforced.

L'invention sera mieux comprise à l'aide des exemples suivants:The invention will be better understood using the following examples:

EXEMPLE 1EXAMPLE 1

Différents alliages repérés 1 à 7 dont les compositions sont indiquées dans le tableau 1 ont été fondus et élaborés par pulvérisation-dépôt (procé­dé OSPREY) sous forme de billettes cylindriques de 150 mm de diamètre dans les conditions suivantes:
-température de coulée: 750°C
- distance atomiseur-dépôt: 600 mm, maintenue sensiblement constante pendant l'essai
-collecteur en acier inxoydable animé d'un mouvement de rotation.
-oscillation de l'atomiseur par rapport a l'axe de rotation du collecteur
Les débits gaz d'atomisation et débit métal utilisés pour chaque composition sont également indiqués au tableau 1.
Après écroûtage à 140 mm, les billettes sont homogénéisées pendant 8 h à la temperature indiquée au tableau 1.
Les ébauches sont ensuite filées à chaud à 400°C dans une presse dont le conteneur a un diamètre de 143 mm sous forme de méplats de section 50 x 22 mm, soit un rapport de filage de 14,6.
Les méplats ainsi obtenus sont ensuite mis en solution à la température indiquée dans le tableau 1 pendant 2 h, trempés à l'eau froide puis revenus pendant 24 h à 120°C.
Les caractéristiques mécaniques de traction en sens long, moyenne de 3 essais, sont reportées dans le tableau 2 (Ro,₂: limite élastique à 0,2% de déformation résiduelle, Rm: charge de rupture; A%: allongement de rupture).Different alloys marked 1 to 7, the compositions of which are given in table 1, were melted and produced by spray-deposition (OSPREY process) in the form of cylindrical billets 150 mm in diameter under the following conditions:
- casting temperature: 750 ° C
- atomizer-deposit distance: 600 mm, kept approximately constant during the test
-Stainless steel manifold animated by a rotational movement.
- oscillation of the atomizer relative to the axis of rotation of the collector
The atomization gas and metal flow rates used for each composition are also indicated in Table 1.
After peeling at 140 mm, the billets are homogenized for 8 h at the temperature indicated in Table 1.
The blanks are then hot-spun at 400 ° C in a press whose container has a diameter of 143 mm in the form of flats of section 50 x 22 mm, ie a spinning ratio of 14.6.
The flats thus obtained are then dissolved at the temperature indicated in Table 1 for 2 h, quenched in cold water and then returned for 24 h at 120 ° C.
The mechanical tensile characteristics in the long direction, average of 3 tests, are reported in Table 2 (Ro, ₂: elastic limit at 0.2% residual deformation, Rm: breaking load; A%: elongation at break).

On constate que les alliages no 1 à 4 suivant l'invention présentent un très haut niveau de caractéristiques mécaniques, avec en particulier une charge de rupture ≧ 800 MPa ainsi qu'un niveau correct de ductilité, avec des allongements à rupture ≧ 5%.It is noted that the alloys No. 1 to 4 according to the invention exhibit a very high level of mechanical properties, in particular with a tensile strength of ≧ 800 MPa and a correct level of ductility, with elongations at rupture ≧ 5% .

L'alliage 5, hors des limites analytiques de l'invention (teneur en Zn trop faible) présente des caractéristiques mécaniques nettement plus faibles que les alliages de l'invention.Alloy 5, outside the analytical limits of the invention (Zn content too low) has much weaker mechanical characteristics than the alloys of the invention.

L'alliage 6, également hors des limites de l'invention du fait de sa trop forte teneur en Zn présente une ductilité (A%) et un écart plastique (Rm- R 0,2) très faibles.Alloy 6, also outside the limits of the invention due to its too high Zn content, has a very low ductility (A%) and a plastic difference (Rm- R 0.2).

L'alliage 7 se situe également hors du cadre de l'invention du fait de la teneur globale en Zr + Cr + Mn trop élevée. Ceci se traduit, malgré le bon niveau de caractéristiques mécaniques par une ductilité très faible (allongement à rupture = 2%).
Il est donc clair qu'un ensemble de propriétés nettement supérieur est obtenu dans le cadre analytique de l'invention pour des alliages élaborés par la technique de pulvérisation-dépôt.The alloy 7 is also outside the scope of the invention because of the overall Zr + Cr + Mn content which is too high. This is reflected, despite the good level of mechanical characteristics, by a very low ductility (elongation at break = 2%).
It is therefore clear that a clearly superior set of properties is obtained in the analytical framework of the invention for alloys produced by the spray-deposition technique.

L'alliage 8 est un alliage dont la composition entre dans le domaine analy­tique des alliages de l'invention mais qui a été élaboré suivant une voie Métallurgie des Poudres décrite ci-après: l'alliage est fondu puis atomisé à l'azote sous forme de poudres; celles-ci sont récupérées et tamisées à 100 µm. Les poudres de taille inférieure à 100 µm sont mises dans des conteneurs en aluminium de diamètre 140 mm munies d'un tube orifice puis sont dégazées à chaud sous vide secondaire (par pompage à travers le tube) à la température de 460°C pendant 100 h. Les conteneurs de poudre ainsi dégazés sont soudés de manière étanche puis comprimés à chaud dans une presse à filer à matrice borgne dans un conteneur de diamètre 143 mm à 450°C de manière à atteindre la densité théorique du matériau. Les billettes ainsi obtenues sont alors usinées afin d'éliminer le matériau du conteneur puis filées dans les mêmes conditions que les billettes des exemples précé­dents. Le produit obtenu est traité thermiquement suivant une procédure analogue (voir température de mise en solution dans le tableau 1) et est caractérisé dans les mêmes conditions.
Les résultats reportés tableau 1 montrent que le produit obtenu a une ductilité et un écart plastique très faibles malgré un niveau de résistance relativement élevé.Alloy 8 is an alloy whose composition falls within the analytical field of the alloys of the invention but which has been developed according to a powder metallurgy process described below: the alloy is melted and then atomized with nitrogen in the form powders; these are collected and sieved to 100 µm. Powders smaller than 100 µm are put in 140 mm diameter aluminum containers fitted with an orifice tube and are then degassed hot under secondary vacuum (by pumping through the tube) at a temperature of 460 ° C for 100 h. The powder containers thus degassed are sealed and then hot pressed in a blind die spinning press in a 143 mm diameter container at 450 ° C so as to reach the theoretical density of the material. The billets thus obtained are then machined in order to remove the material from the container and then spun under the same conditions as the billets of the previous examples. The product obtained is heat treated according to a similar procedure (see solution temperature in Table 1) and is characterized under the same conditions.
The results reported in Table 1 show that the product obtained has very low ductility and plastic difference despite a relatively high level of resistance.

Le cas du dernier alliage illustre bien la supériorité de la méthode de l'invention pour obtenir des alliages ayant à la fois de très hautes résis­tances et une bonne ductilité.The case of the last alloy illustrates well the superiority of the method of the invention for obtaining alloys having both very high strengths and good ductility.

EXEMPLE 2EXAMPLE 2

Un alliage d'Al de composition:
Al: 10%Zn; 3,0%Mg; 1,0%Cu; 0,1%Zr; 0,15%Cr; 0,15%Mn, reste Al
a été fondu à 750°C et élaboré par pulvérisation-dépôt sous la forme de billettes de 150 mm de diamètre avec une coinjection simultanée de particu­les de SiC de taille moyenne 10 µm, avec une fraction volumique de 15%.An alloy of composition Al:
Al: 10% Zn; 3.0% Mg; 1.0% Cu; 0.1% Zr; 0.15% Cr; 0.15% Mn, rest Al
was melted at 750 ° C and produced by spray-deposition in the form of 150 mm diameter billets with simultaneous coinjection of SiC particles of average size 10 μm, with a volume fraction of 15%.

Les conditions de pulvérisation-dépôt étaient les suivantes:
- débit métal : 5,8 kg/min.
- débit gaz : 15 Nm3/min.
- distance atomiseur-dépôt: 620 mm, maintenue sensiblement constante pendant l'essai
- collecteur en acier inox animé d'un mouvement de rotation
- oscillation de l'atomiseur par rapport à l'axe de rotation du collecteurThe spray-deposit conditions were as follows:
- metal flow: 5.8 kg / min.
- gas flow: 15 Nm3 / min.
- atomizer-deposit distance: 620 mm, kept approximately constant during the test
- stainless steel collector with rotating movement
- oscillation of the atomizer relative to the axis of rotation of the collector

Les billettes ainsi obtenues sont ensuite écroûtées à Ø 140 mm, homogénéi­sées 8 h à 470°C, filées à chaud à 400°C sous forme de méplats de section 50 x 22 mm (rapport de filage 14,6).The billets thus obtained are then peeled to Ø 140 mm, homogenized for 8 hours at 470 ° C, hot spun at 400 ° C in the form of flats with a section of 50 x 22 mm (spinning ratio 14.6).

Ces méplats sont traités thermiquement dans les conditions suivantes:
- mise en solution 2 h à 470°C
- trempe à l'eau froide
- revenu 24 h à 120°CThese flats are heat treated under the following conditions:
- solution solution 2 h at 470 ° C
- cold water quenching
- 24 hour heat recovery at 120 ° C

Les caractéristiques de traction ainsi que le module d'Young (E) ont été mesurées sens long. Les résultats obtenus, moyenne de 3 essais, sont donnés ci-dessous:
Ro,₂ = 798 MPa, Rm = 820 MPa, A = 4%, E = 95 GPaThe tensile characteristics as well as the Young's modulus (E) were measured long-term. The results obtained, average of 3 tests, are given below:
Ro, ₂ = 798 MPa, Rm = 820 MPa, A = 4%, E = 95 GPa

Le procédé de pulvérisation-dépôt selon l'invention, outre le meilleur compromis de caractéristiques mécaniques obtenues, possède sur la métallur­gie des poudres classique les avantages suivants :
- on évite les opérations longues et coûteuses de dégazage et de compactage
- la méthode est plus sûre, car il n'y a pas de manipulation de poudres réactives. TABLEAU 1 ALLIAGE No COMPOSITION (% PONDERAUX) PROCEDE D'ELABORATION DEBIT GAZ (m3/min) DEBIT METAL (kg/min) TEMPERATURE HOMOGENEISATION (°C) TEMPERATURE DE MISE EN SOLUTION Zn Mg Cu Mn Cr Zr Al 1 12,0 3,0 1,0 0,25 0,20 0,20 rest Pulvérisation dépôt 15 6,0 470 470 2 13,0 2,5 1,4 0,20 0,15 0,20 " " 14 5,8 465 465 3 14,5 2,2 1,1 0,15 0,10 0,30 " " 16 6,1 460 460 4 9,0 3,5 1,2 0,25 0,15 0,25 " " 12 5,6 470 470 5 8,0 2,5 1,6 0,25 0,20 0,20 " " 12 6,0 470 470 6 16,0 3,2 1,0 0,20 0,15 0,22 " " 16 5,8 460 460 7 12,2 2,9 1,1 0,7 0,5 0,6 " " 14,8 6,1 470 470 8 12,1 2,9 1,0 0,20 0,20 0,15 " Métallurgie des Poudres - - - 470 TABLEAU 2 ALLIAGE Ro,2 (MPa) Rm (PMa) A (%) 1 790 810 8,0 2 792 812 7,0 3 795 809 6,0 4 785 805 9,0 5 710 755 9,0 6 765 768 1,2 7 795 802 2,0 8 791 793 0,5 The spray-deposition process according to the invention, in addition to the best compromise of mechanical characteristics obtained, has the following advantages over conventional powder metallurgy:
- long and costly degassing and compaction operations are avoided
- the method is safer, since there is no handling of reactive powders. TABLE 1 ALLOY # COMPOSITION (% PONDERAUX) ELABORATION PROCESS GAS FLOW (m3 / min) METAL FLOW (kg / min) HOMOGENEIZATION TEMPERATURE (° C) SOLUTION TEMPERATURE Zn Mg Cu Mn Cr Zr Al 1 12.0 3.0 1.0 0.25 0.20 0.20 rest Spray depot 15 6.0 470 470 2 13.0 2.5 1.4 0.20 0.15 0.20 " " 14 5.8 465 465 3 14.5 2.2 1.1 0.15 0.10 0.30 " " 16 6.1 460 460 4 9.0 3.5 1.2 0.25 0.15 0.25 " " 12 5.6 470 470 5 8.0 2.5 1.6 0.25 0.20 0.20 " " 12 6.0 470 470 6 16.0 3.2 1.0 0.20 0.15 0.22 " " 16 5.8 460 460 7 12.2 2.9 1.1 0.7 0.5 0.6 " " 14.8 6.1 470 470 8 12.1 2.9 1.0 0.20 0.20 0.15 " Powder metallurgy - - - 470 ALLOY Ro, 2 (MPa) Rm (PMa) AT (%) 1 790 810 8.0 2 792 812 7.0 3 795 809 6.0 4 785 805 9.0 5 710 755 9.0 6 765 768 1.2 7 795 802 2.0 8 791 793 0.5

Claims (11)

1. Méthode d'obtention d'alliages d'Al de la série 7000, à haute résistance et bonne ductilité caractérisée en ce que : a) on forme par pulvérisation-dépôt un alliage massif de composition pondé­rale suivante :
Zn de 8,5 à 15,0%
Mg de 2,0 à 4,0%
Cu de 0,5 à 2,0%
au moins un des 3 éléments suivants :
Zr de 0,05 à 0,8%
Mn de 0,05 à 1,0% Cr de 0,05 à 0,8%
avec Zr + Mn + Cr ≦ 1,4%
Fe jusqu'à 0,5%
Si jusqu'à 0,5%
autres (impuretés)
≦ 0,05% chacun
≦ 0,15% total
reste Al. b) on transforme à chaud le corps ainsi obtenu entre 300 et 450°C, puis éventuellement à froid. c) on traite thermiquement le produit obtenu par mise en solution, trempe et revenu. 1. Method for obtaining Al alloys of the 7000 series, with high resistance and good ductility, characterized in that: a) a massive alloy of the following weight composition is formed by spray-deposition:
Zn from 8.5 to 15.0%
Mg from 2.0 to 4.0%
Cu from 0.5 to 2.0%
at least one of the following 3 elements:
Zr from 0.05 to 0.8%
Mn from 0.05 to 1.0% Cr from 0.05 to 0.8%
with Zr + Mn + Cr ≦ 1.4%
Fe up to 0.5%
If up to 0.5%
other (impurities)
≦ 0.05% each
≦ 0.15% total
remains Al. b) the body thus obtained is transformed hot between 300 and 450 ° C., then optionally cold. c) the product obtained is heat treated by dissolving, quenching and tempering. 2. Méthode selon la revendication 1 caractérisée en ce que la composition chimique est la suivante :
Zn de 8,7 à 13,7%
Mg de 2,2 à 3,8%
Cu de 0,6 à 1,6%
au moins un des 3 éléments suivants :
Zr de 0,05 à 0,5%
Mn de 0,05 à 0,8%
Cr de 0,05 à 0,5%
avec Zr + Mn + Cr ≦ 1,2%
Fe jusqu'à 0,3%
Si jusqu'à 0,2%
autres (impuretés)
≦ 0,05% chacun
≦ 0,15% total
reste Al2. Method according to claim 1 characterized in that the chemical composition is as follows:
Zn from 8.7 to 13.7%
2.2 to 3.8% mg
Cu from 0.6 to 1.6%
at least one of the following 3 elements:
Zr from 0.05 to 0.5%
Mn from 0.05 to 0.8%
Cr from 0.05 to 0.5%
with Zr + Mn + Cr ≦ 1.2%
Fe up to 0.3%
If up to 0.2%
other (impurities)
≦ 0.05% each
≦ 0.15% total
stay Al 3. Méthode selon les revendications 1 et 2 caractérisée en ce que les teneurs en Mg, Cu et Zn exprimées en pourcentages pondéraux obéissent à la relation:
5,5 ≦ Mg + Cu + Zn 6
Figure imgb0002
≦6,53. Method according to claims 1 and 2 characterized in that the contents of Mg, Cu and Zn expressed in weight percentages obey the relationship:
5.5 ≦ Mg + Cu + Zn 6
Figure imgb0002
 ≦ 6.5 4. Méthode selon les revendications 1, 2 ou 3 caractérisée en ce que Cr, Zr et Mn sont présentés simultanément dans la composition de l'alliage, avec:
Cr ≧ 0,05%, Mn ≧ 0,05%, Zr ≧ 0,05%
et Mn + Cr + Zr ≦ 1,2%.4. Method according to claims 1, 2 or 3 characterized in that Cr, Zr and Mn are presented simultaneously in the composition of the alloy, with:
Cr ≧ 0.05%, Mn ≧ 0.05%, Zr ≧ 0.05%
and Mn + Cr + Zr ≦ 1.2%. 5. Méthode selon la revendication 4 caractérisée en ce que la composition de l'alliage est telle que:
Mn + Cr ≦ 0,6%.5. Method according to claim 4 characterized in that the composition of the alloy is such that:
Mn + Cr ≦ 0.6%. 6. Méthode selon l'une des revendications 1 à 5 caractérisée en ce qu'une homogénéisation entre 450 et 520°C pendant 2 à 50 h est effectuée entre les étapes a) et b).6. Method according to one of claims 1 to 5 characterized in that a homogenization between 450 and 520 ° C for 2 to 50 h is carried out between steps a) and b). 7. Méthode selon l'une des revendications 1 à 6 caractérisée en ce que la transformation à chaud est effectuée par filage, laminage ou forgeage ou une combinaison de ces opérations.7. Method according to one of claims 1 to 6 characterized in that the hot transformation is carried out by spinning, rolling or forging or a combination of these operations. 8. Méthode selon la revendication 7, caractérisée en ce que la transforma­tion à chaud est complétée par une transformation à froid.8. Method according to claim 7, characterized in that the hot transformation is supplemented by a cold transformation. 9.Méthode selon l'une des revendications 1 à 8 caractérisée en ce que la mise en solution est effectuée entre 440 et 520°C pendant 2 à 8h.9. Method according to one of claims 1 to 8 characterized in that the dissolution is carried out between 440 and 520 ° C for 2 to 8 hours. 10.Méthode selon l'une des revendications 1 à 9 caractérisée en ce que le revenu est effectué entre 90 et 150°C pendant 2 à 25 h.10. Method according to one of claims 1 to 9 characterized in that the tempering is carried out between 90 and 150 ° C for 2 to 25 h. 11.Méthode d'obtention de matériaux composites à matrice métallique dans laquelle on obtient un alliage massif selon l'une des revendications 1 à 10 caractérisée en ce que l'on coinjecte pendant l'opération de pulvérisation-dépôt des particules céramiques de forme sensiblement équiaxe, de taille comprise entre 1 et 50 µm, et de fraction volumique (relative au métal) comprise entre 3 et 28%.11. Method for obtaining composite materials with a metal matrix in which a solid alloy is obtained according to one of the claims 1 to 10 characterized in that, during the spraying-deposition operation, ceramic particles of substantially equiaxial shape, of size between 1 and 50 μm, and of volume fraction (relative to the metal) of between 3 and 28 are co-injected %.
EP89420497A 1988-12-19 1989-12-18 Process for the preparation by spray deposits of aluminium alloys of the 7000 series, and discontinuously reinforced composite materials having these high strength, highly ductile alloys as a matrix Expired - Lifetime EP0375571B1 (en)

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AU4681689A (en) 1990-06-21
BR8906543A (en) 1990-09-04
CA2005747C (en) 1996-04-09
TR24392A (en) 1991-09-01
DE68907331T2 (en) 1993-10-21
IL92727A0 (en) 1990-09-17
HUT53681A (en) 1990-11-28
FR2640644B1 (en) 1991-02-01
DE68907331D1 (en) 1993-07-29
FR2640644A1 (en) 1990-06-22
HU896605D0 (en) 1990-02-28
AU615366B2 (en) 1991-09-26
NO895100L (en) 1990-06-20
NO895100D0 (en) 1989-12-18

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