EP0391815A1 - Aluminium-based alloy with a high modulus and an increased mechanical strength and process for production - Google Patents

Aluminium-based alloy with a high modulus and an increased mechanical strength and process for production Download PDF

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EP0391815A1
EP0391815A1 EP90420166A EP90420166A EP0391815A1 EP 0391815 A1 EP0391815 A1 EP 0391815A1 EP 90420166 A EP90420166 A EP 90420166A EP 90420166 A EP90420166 A EP 90420166A EP 0391815 A1 EP0391815 A1 EP 0391815A1
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alloy
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EP0391815B1 (en
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Jean-François Faure
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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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10S428/00—Stock material or miscellaneous articles
    • Y10S428/922—Static electricity metal bleed-off metallic stock
    • Y10S428/9335—Product by special process
    • Y10S428/937—Sprayed metal
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12486—Laterally noncoextensive components [e.g., embedded, etc.]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the invention relates to alloys based on Al of the 7000 series, according to the nomenclature of Aluminum Association (AA), having a high Young modulus and high mechanical characteristics of resistance and toughness as well as their method of obtaining.
  • AA Aluminum Association
  • the most resistant Aluminum alloys of the 7000 series generally have a Young E modulus of the order of 70 GPa but not exceeding 72-73 GPa.
  • alloys based on Al containing Li Admittedly, alloys based on Al containing Li are known, the elastic modulus and mechanical characteristics of which are high. However, these pose complex production problems, given the reactivity of the Li and this therefore requires special and costly production and casting installations.
  • the alloys according to the invention can be produced using conventional installations known in the metallurgy of common Al alloys. In addition, the mechanical resistance characteristics of Al-Li are generally lower than those of 7000 alloys.
  • Alloys of type 7000 much more loaded with alloying elements and obtained by powder metallurgy have high mechanical characteristics, good resistance to corrosion under tension but a modulus less than 74 GPa.
  • the invention therefore relates to the alloys with the following weight composition (in%) Zn: 5.5 - 8.45 Mg: 2.0 - 3.5 Cu: 0.5 - 2.5 Zr: 0.1 - 0.5 Cr: 0.3 - 0.8 Mn: 0.3 - 1.1 Fe: up to 0.5 If: up to 0.5 other items each ⁇ 0.05 total ⁇ 9.15 Rest Al
  • a preferred composition is as follows: Zn: 7.0 - 8.4 Mg: 2.0 - 2.9 Cu: 0.8 - 2.0 Zr: 0.1 - 0.4 Cr: 0.3 - 0.6 Mn: 0.3 - 0.9 the rest being identical to the above compositions.
  • 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.
  • the hot transformation stage may be preceded by a homogenization treatment of the solid body, in one or more stages, between the temperatures of 450 and 520 ° C., generally between 2 and 50 hours.
  • the product thus obtained meets the characteristics referred to above. These properties are attributed to a fine dispersion of standard phases (Al, Mn, Cr) and Al3Zr - due to the combination of the composition of the alloy and to its production process; this structure makes it possible to achieve, among other things, good ductility, toughness and a high elastic limit.
  • the dissolution is generally carried out between 450 and 520 ° C and the T6 type treatment between 90 and 150 ° C, for a sufficient time to substantially obtain the hardness peak (from 2 to 25 hours).
  • the T7 treatment consists of a T6 type treatment supplemented by tempering at a higher temperature, for example between 150 and 170 ° C, for 0.5 to 20 hours.
  • the invention is also applicable to composite materials hardened by dispersed ceramic particles of the oxide, carbide, nitride, silicide, boride, etc. type introduced into the alloy according to the invention, which constitutes the matrix thereof, during operation 1 , for example by injecting the powder into the liquid stream. These particles have a size between 1 and 50 ⁇ m and represent (relative to the metal) a volume fraction of between 3 and 12%.
  • alloys 1 to 4 are in accordance with the invention, alloys 5 and 6 are outside the invention and alloy 7 is a conventional alloy (7075) from the prior art for comparison; this was poured semi-continuously and processed hot and heat treated like the other alloys; FIG. 1 represents the mechanical characteristics E and R 0.2 of the alloys tested, FIG. 2 the characteristics of toughness as a function of R 0.2 and FIG. 3 the characteristics of corrosion under tension as a function of R 0.2 .
  • the billets are homogenized for 8 hours at a temperature of 460 ° C.
  • 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 undergo a T7 type heat treatment under the following conditions: - solution for 2 hours at a temperature between 460 and 485 ° C - cold water quenching - two-bearing income: 24 hours at 120 ° C + 1 to 20 hours between 155 and 170 ° C
  • Alloys 1 to 4 are in the claimed field and have a module ⁇ 74 GPa and a long-term elastic limit ⁇ 530 MPa while having good long-term ductility ( ⁇ 8%) and long cross-beam ( ⁇ 6%), a toughness LT direction of at least 20 MPa ⁇ m and good resistance to corrosion under tension (measured according to standard ASTM G 38 73).
  • the alloy 5 is outside the invention because of its too high Cr and Mn content, and although having a high modulus and elastic limit, it is very little ductile and cannot be used for the manufacture of parts.
  • the alloy 6 is also outside the invention because of its too low Cr and Mn content, does not have the advantages of the alloys according to the invention, has a low modulus and elastic limit and therefore does not differ from the alloys classics like the 7075.
  • composition and properties of a conventional 7075 alloy conventionally cast and then transformed and heat treated according to the same range as the alloys 1 to 6 are reported for comparison.
  • the alloys according to the invention are mainly intended for the manufacture of profiles or parts of forged or stamped structures.

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  • Organic Chemistry (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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Abstract

Al-based alloys of the 7000 series which have a high modulus (E >/= 74 GPa), a high mechanical strength (R0.2 >/= 530 MPa in the lengthwise direction), a good tenacity (KIC, lengthwise direction > 20 MPa  2ROOT m) and a good corrosion resistance under (O pressure >/= 250 MPa in the short transverse direction, lifetime >/= 30 days - ASTM Standard G 38-73). <??>The alloy according to the invention corresponds to the following weight composition: from 5.5 to 8.45% of Zr from 2 to 3.5% Mg from 0.5 to 2.5% Cu up to 0.5% Fe up to 0.5% Si other elements </= 0.05% each and up to 0.15% in all with 0.1 </= Zr </= 0.5% 0.3 </= Cr </= 0.6% 0.3 </= Mn </= 1.1% <??>It is preferably produced by the following process: a) a massive body which has the composition claimed above is formed by spray-deposition, b) this body is converted into a wrought product between 300 and 450 DEG C and then optionally when cold c) the wrought product is heat-treated by dissolving, quenching and annealing to a T6 or T7 state. <IMAGE>

Description

L'invention concerne des alliages à base d'Al de la série 7000, suivant la nomenclature d'Aluminium Association (AA), possédant un module d'Young élevé et des caractéristiques mécaniques de résistance et de ténacité élevées ainsi que leur procédé d'obtention.
Les alliages d'Aluminium de la série 7000 parmi les plus résistants possèdent généralement un module d'Young E de l'ordre de 70 GPa mais ne dépassant pas 72-73 GPa.
Cependant en vue d'alléger les structures, en particulier dans les domaines aéronautiques et spatiaux, la nécessité d'alliages légers à module d'Young plus élevé (E ≧ 74 GPa) et résistance élevée (R0,2≧ 530 MPa dans le sens long) se fait sentir, ces caractéristiques devant être atteintes sans préjudice notable sur d'autres propriétés d'emploi telles que la ténacité (KIC, sens long ≧ 20 MPa √m) ou la résistance à la corrosion sous tension (seuil de non rupture à 30 jours ≧ 250 MPa dans le sens travers court et dans le milieu d'essai considéré).The invention relates to alloys based on Al of the 7000 series, according to the nomenclature of Aluminum Association (AA), having a high Young modulus and high mechanical characteristics of resistance and toughness as well as their method of obtaining.
Among the most resistant Aluminum alloys of the 7000 series generally have a Young E modulus of the order of 70 GPa but not exceeding 72-73 GPa.
However, in order to lighten the structures, in particular in the aeronautical and space fields, the need for light alloys with higher Young's modulus (E ≧ 74 GPa) and high resistance (R 0.2 ≧ 530 MPa in the long sense) is felt, these characteristics must be achieved without significant damage to other properties of use such as toughness (KIC, long sense ≧ 20 MPa √m) or resistance to corrosion under stress (threshold of no rupture at 30 days ≧ 250 MPa in the short cross direction and in the test medium considered).

Certes on connaît des alliages à base d'Al contenant du Li dont le module élastique et les caractéristiques mécaniques sont élevées. Cepen­dant ceux-ci posent des problèmes d'élaboration complexes, étant donné la réactivité du Li et ceci impose donc des installations d'élaboration et de coulée spéciales et coûteuses. Les alliages selon l'invention peuvent être élaborés à l'aide des installations classiques, connues dans la métallurgie des alliages d'Al courants. De plus les caractéristi­ques mécaniques de résistance des Al-Li sont généralement inférieures à celles des alliages 7000.Admittedly, alloys based on Al containing Li are known, the elastic modulus and mechanical characteristics of which are high. However, these pose complex production problems, given the reactivity of the Li and this therefore requires special and costly production and casting installations. The alloys according to the invention can be produced using conventional installations known in the metallurgy of common Al alloys. In addition, the mechanical resistance characteristics of Al-Li are generally lower than those of 7000 alloys.

Des alliages de type 7000 beaucoup plus chargés en éléments d'alliages et obtenus par métallurgie des poudres possèdent de hautes caractéristi­ques mécaniques, une bonne résistance à la corrosion sous tension mais un module inférieur à 74 GPa.Alloys of type 7000 much more loaded with alloying elements and obtained by powder metallurgy have high mechanical characteristics, good resistance to corrosion under tension but a modulus less than 74 GPa.

L'invention concerne donc les alliages de composition pondérale suivante (en %)
Zn: 5,5 - 8,45
Mg: 2,0 - 3,5
Cu: 0,5 - 2,5
Zr: 0,1 - 0,5
Cr: 0,3 - 0,8
Mn: 0,3 - 1,1
Fe: jusqu'à 0,5
Si: jusqu'à 0,5
autres éléments chacun ≦ 0,05
total ≦ 9,15
Reste AlThe invention therefore relates to the alloys with the following weight composition (in%)
Zn: 5.5 - 8.45
Mg: 2.0 - 3.5
Cu: 0.5 - 2.5
Zr: 0.1 - 0.5
Cr: 0.3 - 0.8
Mn: 0.3 - 1.1
Fe: up to 0.5
If: up to 0.5
other items each ≦ 0.05
total ≦ 9.15
Rest Al

Une composition préférentielle est la suivante:
Zn: 7,0 - 8,4
Mg: 2,0 - 2,9
Cu: 0,8 - 2,0
Zr: 0,1 - 0,4
Cr: 0,3 - 0,6
Mn: 0,3 - 0,9
le reste étant identique aux compositions ci-dessus.A preferred composition is as follows:
Zn: 7.0 - 8.4
Mg: 2.0 - 2.9
Cu: 0.8 - 2.0
Zr: 0.1 - 0.4
Cr: 0.3 - 0.6
Mn: 0.3 - 0.9
the rest being identical to the above compositions.

Un procédé d'obtention consiste :

  • 1- à former par pulvérisation-dépôt un corps massif ayant une composition rentrant dans les limites indiquées ci-dessus.
  • 2- à transformer à chaud ce corps en un produit ouvré entre 300 et 450°C, et puis éventuellement à froid.
  • 3- à le traiter thermiquement par mise en solution, trempe et revenu, en un état T6 ou, de préférence, T7 suivant la nomenclature de l'AA.
A process for obtaining it consists of:
  • 1- to form by spray-deposition a solid body having a composition falling within the limits indicated above.
  • 2- to transform this body hot into a processed product between 300 and 450 ° C, and then possibly cold.
  • 3- to heat treat it by dissolving, quenching and tempering, in a state T6 or, preferably, T7 according to the nomenclature of AA.

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.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.

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.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.

L'étape de transformation à chaud peut être précédée d'un traitement d'homogénéisation du corps massif, en un ou plusieurs paliers, compris entre les températures de 450 et 520°C, généralement comprise entre 2 et 50 heures.The hot transformation stage may be preceded by a homogenization treatment of the solid body, in one or more stages, between the temperatures of 450 and 520 ° C., generally between 2 and 50 hours.

Le produit ainsi obtenu répond aux caractéristiques visées mentionnées plus haut.
On attribue ces propriétés à une fine dispersion de phases type (Al, Mn, Cr) et Al₃Zr - due à la combinaison de la composition de l'alliage et à son procédé d'obtention; cette structure permet d'atteindre, entre autres une bonne ductilité, ténacité et une limite élastique élevée.The product thus obtained meets the characteristics referred to above.
These properties are attributed to a fine dispersion of standard phases (Al, Mn, Cr) and Al₃Zr - due to the combination of the composition of the alloy and to its production process; this structure makes it possible to achieve, among other things, good ductility, toughness and a high elastic limit.

La mise en solution est en général effectuée entre 450 et 520°C et le traitement type T6 entre 90 et 150°C, pendant une durée suffisante pour obtenir sensiblement le pic de dureté (de 2 à 25 heures).
Le traitement T7 consiste en un traitement type T6 complété par un revenu à plus haute température par exemple entre 150 et 170°C, pendant 0,5 à 20 heures.
L'invention est également applicable aux matériaux composites durcis par particules céramiques dispersées du type oxydes, carbures, nitrures, siliciures, borures, etc- introduits dans l'alliage selon l'invention, qui en constitue la matrice, lors de l'opération 1, par exemple par injection de la poudre dans le flux liquide.
Ces particules ont une taille comprise entre 1 et 50 µm et représentent (par rapport au métal) une fraction volumique comprise entre 3 et 12%.The dissolution is generally carried out between 450 and 520 ° C and the T6 type treatment between 90 and 150 ° C, for a sufficient time to substantially obtain the hardness peak (from 2 to 25 hours).
The T7 treatment consists of a T6 type treatment supplemented by tempering at a higher temperature, for example between 150 and 170 ° C, for 0.5 to 20 hours.
The invention is also applicable to composite materials hardened by dispersed ceramic particles of the oxide, carbide, nitride, silicide, boride, etc. type introduced into the alloy according to the invention, which constitutes the matrix thereof, during operation 1 , for example by injecting the powder into the liquid stream.
These particles have a size between 1 and 50 μm and represent (relative to the metal) a volume fraction of between 3 and 12%.

L'invention sera mieux comprise à l'aide des essais suivants: les allia­ges n° 1 à 4 sont conformes à l'invention, les alliages 5 et 6 sont hors l'invention et l'alliage 7 est un alliage classique (7075) de l'art antérieur pour comparaison; celui-ci a été coulé en semi-continu et transformé à chaud et traité thermiquement comme les autres alliages; la figure 1 représente les caractéristiques mécaniques E et R0,2 des alliages essayés, la figure 2 les caractéristiques de ténacité en fonc­tion de R0,2 et la figure 3 les caractéristiques de corrosion sous tension en fonction de R0,2.The invention will be better understood using the following tests: alloys 1 to 4 are in accordance with the invention, alloys 5 and 6 are outside the invention and alloy 7 is a conventional alloy (7075) from the prior art for comparison; this was poured semi-continuously and processed hot and heat treated like the other alloys; FIG. 1 represents the mechanical characteristics E and R 0.2 of the alloys tested, FIG. 2 the characteristics of toughness as a function of R 0.2 and FIG. 3 the characteristics of corrosion under tension as a function of R 0.2 .

EXEMPLEEXAMPLE

Différents alliages repérés 1 à 6 dont les compositions pondérales (en %)sont reportées au Tableau 1 ont été fondus et élaborés par pulvérisa­tion-dépôt (procédé OSPREY) sous forme de billettes
- température de coulée: 750°C
- distance atomiseur-dépôt: 600 mm, maintenue sensiblement constante pendant l'essai
- collecteur en acier inoxydable animé d'un mouvement de rotation
- oscillation de l'atomiseur par rapport à l'axe de rotation du colle­cteur
- débit gaz/débit métal de 2 à 3 m³/kg.Different alloys marked 1 to 6 whose weight compositions (in%) are given in Table 1 were melted and produced by spray-deposition (OSPREY process) in the form of billets
- casting temperature: 750 ° C
- atomizer-deposit distance: 600 mm, kept approximately constant during the test
- stainless steel collector with rotational movement
- oscillation of the atomizer relative to the axis of rotation of the collector
- gas flow / metal flow from 2 to 3 m³ / kg.

Après écroutage à ⌀ 140 mm, les billettes sont homogénéisées pendant 8 heures à la température de 460°C.
Les ébauches sont ensuite filées à chaud à 400°C dans une presse dont le conteneur à 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 subissent un traitement thermique de type T7 dans les conditions suivantes:
- mise en solution 2 heures à une température comprise entre 460 et 485°C
- trempe à l'eau froide
- revenu bipalier: 24 heures à 120°C + 1 à 20 heures entre 155 et 170°CAfter peeling at ⌀ 140 mm, the billets are homogenized for 8 hours at a temperature of 460 ° C.
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 undergo a T7 type heat treatment under the following conditions:
- solution for 2 hours at a temperature between 460 and 485 ° C
- cold water quenching
- two-bearing income: 24 hours at 120 ° C + 1 to 20 hours between 155 and 170 ° C

Les propriétés mécaniques obtenues sont reportées au Tableau 2.The mechanical properties obtained are reported in Table 2.

Les alliages 1 à 4 sont dans le domaine revendiqué et présentent un module ≧ 74 GPa et une limite élastique sens long ≧ 530 MPa tout en ayant une bonne ductilité sens long (≧ 8%) et travers long (≧ 6%), une ténacité sens L-T d'au moins 20 MPa √m et une bonne tenue en corr­osion sous tension (mesurée suivant norme ASTM G 38 73).Alloys 1 to 4 are in the claimed field and have a module ≧ 74 GPa and a long-term elastic limit ≧ 530 MPa while having good long-term ductility (≧ 8%) and long cross-beam (≧ 6%), a toughness LT direction of at least 20 MPa √m and good resistance to corrosion under tension (measured according to standard ASTM G 38 73).

L'alliage 5 est hors de l'invention du fait de sa teneur en Cr et Mn trop élevée, et bien qu'ayant un haut module et limite élastique, il est très peu ductile et est inutilisable pour la fabrication de pièces.The alloy 5 is outside the invention because of its too high Cr and Mn content, and although having a high modulus and elastic limit, it is very little ductile and cannot be used for the manufacture of parts.

L'alliage 6 est également hors de l'invention du fait de sa teneur en Cr et Mn trop basse,ne présente pas les avantages des alliages selon l'invention, a un faible module et limite élastique et ne se distingue donc pas des alliages classiques comme le 7075.The alloy 6 is also outside the invention because of its too low Cr and Mn content, does not have the advantages of the alloys according to the invention, has a low modulus and elastic limit and therefore does not differ from the alloys classics like the 7075.

On a reporté à titre de comparaison la composition et les propriétés d'un alliage classique 7075 coulé classiquement puis transformé et traité thermiquement suivant la même gamme que les alliages 1 à 6.The composition and properties of a conventional 7075 alloy conventionally cast and then transformed and heat treated according to the same range as the alloys 1 to 6 are reported for comparison.

On constate que le module et la limite élastique de cet alliage sont nettement plus faibles que pour les alliages de l'invention. TABLEAU 1 COMPOSITION DES ALLIAGES TESTES Alliage Zn Mg Cu Cr Mn Zr Fe Si Reste 1 7,8 2,3 1,4 0,35 0,85 0,16 <0,1 <0,1 Al 2 8,0 2,4 1,35 0,45 0,50 0,17 <0,1 <0,1 Al 3 6,5 2,2 1,5 0,50 0,60 0,20 <0,1 <0,1 Al 4 7,0 2,3 1,4 0,35 0,40 0,18 <0,1 <0,1 Al 5 7,5 2,2 1,35 0,9 1,2 0,25 <0,1 <0,1 Al 6 6,0 2,2 1,5 0,15 0,18 0,12 <0,1 <0,1 Al 7075 classique 5,5 2,3 1,6 0,23 - - <0,05 <0,04 Al TABLEAU 2 PROPRIETES DES ALLIAGES TESTES (état T7) Alliage Traction sens long Traction sens travers long Module (GPa) Ténacité* sens L-T (MPa √m) Corrosion** sous tension (non rupture à 30 j) (MPa) R0,2 (MPa) Rm (MPa) A% R0,2 (MPa) Rm (MPa) A% 1 580 620 9,0 550 590 7,0 76 22,5 310 2 590 630 8,5 560 595 6,5 75,5 21,8 310 3 535 600 12,0 520 570 9,2 76,4 30,8 310 4 575 610 10,0 550 580 8,5 74,5 35,2 280 5 582 612 3,0 540 555 1,5 78,2 12,0 240 6 520 550 13,1 500 525 8,2 72,5 35,9 310 7075 classique 470 536 14,5 428 501 14,2 72,0 45,0 310 *Effort dans le sens long, propagation de la fissure dans le sens travers **Essais dans le sens travers court selon ASTM G38 73. It is noted that the modulus and the elastic limit of this alloy are significantly lower than for the alloys of the invention. TABLE 1 COMPOSITION OF TESTED ALLOYS Alloy Zn Mg Cu Cr Mn Zr Fe Yes Rest 1 7.8 2.3 1.4 0.35 0.85 0.16 <0.1 <0.1 Al 2 8.0 2.4 1.35 0.45 0.50 0.17 <0.1 <0.1 Al 3 6.5 2.2 1.5 0.50 0.60 0.20 <0.1 <0.1 Al 4 7.0 2.3 1.4 0.35 0.40 0.18 <0.1 <0.1 Al 5 7.5 2.2 1.35 0.9 1.2 0.25 <0.1 <0.1 Al 6 6.0 2.2 1.5 0.15 0.18 0.12 <0.1 <0.1 Al 7075 classic 5.5 2.3 1.6 0.23 - - <0.05 <0.04 Al PROPERTIES OF TESTED ALLOYS (state T7) Alloy Long-distance traction Long cross direction Module (GPa) Tenacity * direction LT (MPa √m) Corrosion ** under tension (non break at 30 d) (MPa) R0.2 (MPa) Rm (MPa) AT% R0.2 (MPa) Rm (MPa) AT% 1 580 620 9.0 550 590 7.0 76 22.5 310 2 590 630 8.5 560 595 6.5 75.5 21.8 310 3 535 600 12.0 520 570 9.2 76.4 30.8 310 4 575 610 10.0 550 580 8.5 74.5 35.2 280 5 582 612 3.0 540 555 1.5 78.2 12.0 240 6 520 550 13.1 500 525 8.2 72.5 35.9 310 7075 classic 470 536 14.5 428 501 14.2 72.0 45.0 310 * Effort in the long direction, propagation of the crack in the cross direction ** Tests in the short cross direction according to ASTM G38 73.

Les alliages selon l'invention sont principalement destinés à la fabrica­tion de profilés ou de pièces de structures forgées ou matricées.The alloys according to the invention are mainly intended for the manufacture of profiles or parts of forged or stamped structures.

Claims (9)

1. Alliage à base d'Aluminium, contenant de 5,5 à 8,45% (en poids) de Zn, de 2 à 3,5% de Mg, de 0,5 à 2,5% Cu, jusqu'à 0,5% Fe, jusqu'à 0,5% Si, autres éléments: < 0,05% chacun et jusqu'à 0,15% au total, caractérisé en ce qu'il contient aussi
de 0,1 à 0,5% de Zr,
de 0,3 à 0,6% de Cr,
et de 0,3 à 1,1% Mn.1. Aluminum-based alloy containing 5.5 to 8.45% (by weight) of Zn, 2 to 3.5% of Mg, 0.5 to 2.5% Cu, up to 0.5% Fe, up to 0.5% Si, other elements: <0.05% each and up to 0.15% in total, characterized in that it also contains
from 0.1 to 0.5% of Zr,
from 0.3 to 0.6% of Cr,
and from 0.3 to 1.1% Mn. 2. Alliage à base d'Aluminium contenant de 7,0 à 8,4% (en poids) de Zn, de 2 à 2,9% de Mg, de 0,8 à 2,0% de Cu, jusqu'à 0,5% Fe, jusqu'à 0,5% Si, autres éléments: ≦ 0,05% chacun et jusqu'à 0,15% au total caractérisé en ce qu'il contient, aussi
de 0,1 à 0,4% Zr
de 0,3 à 0,6% Cr
et de 0,3 à 0,9% Mn2. Aluminum alloy containing from 7.0 to 8.4% (by weight) of Zn, from 2 to 2.9% of Mg, from 0.8 to 2.0% of Cu, up to 0.5% Fe, up to 0.5% Si, other elements: ≦ 0.05% each and up to 0.15% in total, characterized in that it also contains
0.1 to 0.4% Zr
from 0.3 to 0.6% Cr
and from 0.3 to 0.9% Mn 3. Alliage selon l'une des revendications 1 ou 2 caractérisé en ce qu'il contient une dispersion homogène de particules céramiques dont la taille est comprise entre 1 et 50µm et de fraction volumique (relative au métal) comprise entre 3 et 12%.3. Alloy according to one of claims 1 or 2 characterized in that it contains a homogeneous dispersion of ceramic particles whose size is between 1 and 50 µm and volume fraction (relative to the metal) between 3 and 12%. 4. Procédé d'obtention d'un alliage selon l'une des revendications 1 à 3 caractérisé en ce qu' a) on forme par pulvérisation-dépôt un corps massif ayant la composi­tion revendiqué ci-dessus, b) on transforme ce corps en un produit ouvré, entre 300 et 450°C et puis éventuellement à froid c) on traite thermiquement le produit ouvré par une mise en solution, trempe et revenu en un état T6 ou T7. 4. Method for obtaining an alloy according to one of claims 1 to 3 characterized in that a) a massive body having the composition claimed above is formed by spray-deposition, b) this body is transformed into a worked product, between 300 and 450 ° C and then possibly cold c) the processed product is heat treated by dissolving, quenching and returning to a T6 or T7 state. 5. Procédé selon la revendication 4 caractérisé en ce que, entre les étapes a et b, le corps est homogénéisé entre 450 et 520°C pendant une durée comprise entre 2 et 50 heures.5. Method according to claim 4 characterized in that, between steps a and b, the body is homogenized between 450 and 520 ° C for a period between 2 and 50 hours. 6. Procédé selon l'une des revendications 4 à 5 caractérisé en ce que la mise en solution a lieu entre 440 et 520°C.6. Method according to one of claims 4 to 5 characterized in that the dissolution takes place between 440 and 520 ° C. 7. Procédé selon l'une des revendications 4 à 6 caractérisé en ce que le revenu est effectué entre 90 et 150°C pendant 2 à 25 heures.7. Method according to one of claims 4 to 6 characterized in that the tempering is carried out between 90 and 150 ° C for 2 to 25 hours. 8. Procédé selon la revendication 7 caractérisé en ce que ce revenu est complété par un 2ème revenu à plus haute température entre 150 et 170°C pendant une durée comprise entre 0,5 et 20 heures.8. Method according to claim 7 characterized in that this income is supplemented by a second income at higher temperature between 150 and 170 ° C for a period between 0.5 and 20 hours. 9. Produit corroyé de composition conforme à l'une des revendications 1 à 3 caractérisé en ce qu'il possède les propriétés mécaniques suivantes:
E (module d'Young) ≧ 74 GPa
R0,2 (limite élastique, sens long) ≧ 530 MPa
KIC (sens long ≧ 20 MPa√m
Résistance à la corrosion sous tension (30 jours) dans le sens sens travers court σ≧ 250 MPa9. Wrought product of composition in accordance with one of claims 1 to 3 characterized in that it has the following mechanical properties:
E (Young's modulus) ≧ 74 GPa
R 0.2 (elastic limit, long sense) ≧ 530 MPa
KIC (long sense ≧ 20 MPa√m
Corrosion resistance under tension (30 days) in the short cross direction σ ≧ 250 MPa
EP90420166A 1989-04-05 1990-04-03 Aluminium-based alloy with a high modulus and an increased mechanical strength and process for production Expired - Lifetime EP0391815B1 (en)

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CN103255327A (en) * 2013-04-27 2013-08-21 北京工业大学 Al-Zn-Mg-Cu-Mn-Zr-Er alloy and preparation technology
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RU2676817C2 (en) * 2014-11-11 2019-01-11 Новелис Инк. Multipurpose heat-treated aluminum alloys and related processes and applications

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DE69016241D1 (en) 1995-03-09
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JPH032345A (en) 1991-01-08
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US5047092A (en) 1991-09-10

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