EP0143727B1 - Aluminium-based alloys having a high heat stability - Google Patents

Aluminium-based alloys having a high heat stability Download PDF

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Publication number
EP0143727B1
EP0143727B1 EP84420198A EP84420198A EP0143727B1 EP 0143727 B1 EP0143727 B1 EP 0143727B1 EP 84420198 A EP84420198 A EP 84420198A EP 84420198 A EP84420198 A EP 84420198A EP 0143727 B1 EP0143727 B1 EP 0143727B1
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alloy according
solidification
alloy
weight
alloys
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EP84420198A
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German (de)
French (fr)
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EP0143727A2 (en
EP0143727A3 (en
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Salim Dermarkar
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Cegedur Societe de Transformation de lAluminium Pechiney SA
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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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/08—Amorphous alloys with aluminium as the major constituent

Definitions

  • the invention relates to Al-based alloys with high heat stability.
  • Alloys based on AI are known which exhibit good hot stability, in particular those described in French patent application FR 2 190 553 or US patent 4 347 076.
  • alloys based are described. of AI containing from 3 to 15% (by weight) of transition element belonging to the group Ti, V, Cr, Mn, Co, Ni, Fe, Zr, Nb and Mo. However, these only keep a hardness lower than 190 Vickers units, for durations of 1 week at temperatures lower than or equal to 400 ° C.
  • the invention relates to Al alloys whose heat stability is significantly higher.
  • the alloys according to the invention contain, in addition to the Al and the inevitable processing impurities, at least 5 to 20% (by weight) of Fe, and more than 0.05% Ni and 0.5% Mo.
  • the sum of the Ni + Mo contents must not exceed 8%, so as not to exceed the retention capacity of the alloying elements during rapid solidification (> 10 4 ° C / second) of the alloy.
  • the% Mo /% Ni ratio must be greater than 0.5 to obtain the desired hot stability. This stability is very much greater than that which a separate addition of Ni or Mo could confer; this point will be illustrated by examples.
  • One (or more) other refractory element (s) from the group Mn, Si, Ti, Hf, Zr, Nb, V can be added to this basic composition, for an overall content of less than 5%. weight.
  • the alloys of preferred compositions individually or in combination from 5 to 10% Fe, a ratio 0.5 ⁇ - K 2 and / or an Ni content of Mo ⁇ 1%.
  • the alloys were produced in the form of a ribbon 1 to 5 min ⁇ 20 to 40 ⁇ m, by rapid solidification on a steel casting wheel, driven at a tangential speed of 45 m / second.
  • alloys 2, 7, 8 which are outside the scope of the invention have poor heat stability, relative to the other alloys according to the invention.
  • a minimum quantity of nickel (and of Mo) is essential in order to obtain the good heat resistance properties: the preferred compositions (4, 5, 6 ) have optimal hot characteristics.
  • Table III gives the characteristics of hot resistance for longer-lasting holdings of the alloys (4 to 6) at 400 ° C.
  • alloy 4 has precipitation in semi-coherent platelets while in the alloy 8, the precipitation already consists of incoherent globules of phase type Al 9 FeNi.
  • the thermal stability of alloy 4 is associated with the slower decomposition kinetics observed on this alloy.
  • the alloys according to the invention may be used for parts of turbomachines operating at temperatures below 350 ° C for fairly long periods or operating at higher temperature for fairly short periods (missile bodies).

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Superconductors And Manufacturing Methods Therefor (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Laminated Bodies (AREA)
  • Pistons, Piston Rings, And Cylinders (AREA)

Description

L'invention concerne des alliages à base d'Al présentant une grande stabilité à chaud.The invention relates to Al-based alloys with high heat stability.

On connaît des alliages à base d'AI qui présentent une bonne stabilité à chaud, en particulier ceux décrits dans la demande de brevet français FR 2 190 553 ou le brevet US 4 347 076. Dans la demande française, sont décrits des alliages à base d'AI contenant de 3 à 15% (en poids) d'élément de transition appartenant au groupe Ti, V, Cr, Mn, Co, Ni, Fe, Zr, Nb et Mo. Cependant, ceux-ci ne conservent qu'une dureté inférieure à 190 unités Vickers, pour des durées de maintien de 1 semaine à des températures inférieures ou égales à 400°C.Alloys based on AI are known which exhibit good hot stability, in particular those described in French patent application FR 2 190 553 or US patent 4 347 076. In the French application, alloys based are described. of AI containing from 3 to 15% (by weight) of transition element belonging to the group Ti, V, Cr, Mn, Co, Ni, Fe, Zr, Nb and Mo. However, these only keep a hardness lower than 190 Vickers units, for durations of 1 week at temperatures lower than or equal to 400 ° C.

Dans le brevet US 4 347 076 sont décrits des alliages à base d'Al contenant de 5 à 16% (en poids) d'éléments de transition du groupe Fe, Cr, Ni, Co, Mn, V, Ti, Zr, Mo, W et B avec Mn + V + Ti + Zr + Mo + W K 5% et B K 1 %. Ces alliages n'atteignent que des duretés inférieures à 240 unités Vickers après un traitement de 1 h 30 mn à 400°C.In US Pat. No. 4,347,076, alloys based on Al containing from 5 to 16% (by weight) of transition elements from the group Fe, Cr, Ni, Co, Mn, V, Ti, Zr, Mo are described. , W and B with Mn + V + Ti + Zr + Mo + WK 5% and BK 1%. These alloys only reach hardnesses lower than 240 Vickers units after a treatment of 1 h 30 min at 400 ° C.

L'invention concerne des alliages d'Al dont la stabilité à chaud est notablement supérieure. Les alliages selon l'invention contiennent, outre l'Al et les impuretés d'élaboration inévitables, au moins de 5 à 20% (en poids) de Fe, et plus de 0,05% Ni et 0,5% Mo.The invention relates to Al alloys whose heat stability is significantly higher. The alloys according to the invention contain, in addition to the Al and the inevitable processing impurities, at least 5 to 20% (by weight) of Fe, and more than 0.05% Ni and 0.5% Mo.

Il a été trouvé que la somme des teneurs en Ni + Mo ne doit pas excéder 8%, de manière à ne pas dépasser la capacité de rétention des éléments d'alliages lors d'une solidification rapide (> 104 °C/seconde) de l'alliage. De plus, le rapport % Mo/% Ni doit être supérieur à 0,5 pour obtenir la stabilité à chaud désirée. Cette stabilité est très largement supérieure à celle que pourrait conférer une addition séparée de Ni ou de Mo; ce point sera illustré par des exemples.It has been found that the sum of the Ni + Mo contents must not exceed 8%, so as not to exceed the retention capacity of the alloying elements during rapid solidification (> 10 4 ° C / second) of the alloy. In addition, the% Mo /% Ni ratio must be greater than 0.5 to obtain the desired hot stability. This stability is very much greater than that which a separate addition of Ni or Mo could confer; this point will be illustrated by examples.

On peut ajouter à cette composition de base un (ou plusieurs) autre(s) élément(s) réfractaire(s) du groupe Mn, Si, Ti, Hf, Zr, Nb, V, pour une teneur globale inférieure à 5% en poids.One (or more) other refractory element (s) from the group Mn, Si, Ti, Hf, Zr, Nb, V can be added to this basic composition, for an overall content of less than 5%. weight.

Les alliages de compositions préférentielles comportent individuellement ou en combinaison de 5 à Mo 10% Fe, un rapport 0,5 ≤ - K 2 et/ou une teneur Ni en Mo ≥ 1%.The alloys of preferred compositions individually or in combination from 5 to 10% Fe, a ratio 0.5 ≤ - K 2 and / or an Ni content of Mo ≥ 1%.

Ces alliages obtenus par solidification rapide (> 104 °C/seconde), par tout moyen connu, présentent à l'état brut de solidification soit une structure monophasée (solution solide sursaturée à base d'AI) soit une structure particulière constituée de cette solution solide à base d'Al et d'une fine précipitation de type eutectoïde, d'une phase (que nous appele- rons µ) d'aspect filiforme dont la largeur, sur coupe micrographique, est de l'ordre de 5 à 50 nm. Cette phase µ, contient au moins 1 % en poids de Ni et 1 % de Mo. Cette phase µ, microcristalline possède les distances interréticulaires suivantes:

  • 0,38 - 0,203 à 0,211 - 0,147 - 0,125 - 0,107 nm

sa structure étant probablement cubique complexe. La taille des cristallites de cette phase µ, est de l'ordre de 1 nm ce qui se traduit par l'existence de plusieurs anneaux larges et diffus sur les clichés de diffraction électronique. Les distances interréticulaires sont les distances de divers plans d'atomes du réseau cristallin, déterminées par radiocristallographie.These alloys obtained by rapid solidification (> 10 4 ° C / second), by any known means, present in the solid state of solidification either a single-phase structure (supersaturated solid solution based on AI) or a particular structure made up of this solid solution based on Al and of a fine precipitation of eutectoid type, of a phase (which we will call µ) of filiform appearance whose width, on micrographic section, is of the order of 5 to 50 nm. This µ phase contains at least 1% by weight of Ni and 1% of Mo. This µ microcrystalline phase has the following interreticular distances:
  • 0.38 - 0.203 to 0.211 - 0.147 - 0.125 - 0.107 nm

its structure is probably complex cubic. The size of the crystallites of this phase µ, is of the order of 1 nm, which results in the existence of several large and diffuse rings on the electron diffraction radiographs. Inter-reticular distances are the distances from various planes of atoms in the crystal lattice, determined by X-ray crystallography.

Cette précipitation est particulièrement stable lors des maintiens à chaud, ce qui explique les propriétés ainsi obtenues. Lors de ces maintiens, la phase µ, se décompose progressivement en plaquettes semico- hérentes (phase µ') puis en globules incohérents ayant la structure du composé AlgFeNi.This precipitation is particularly stable during heat maintenance, which explains the properties thus obtained. During these maintenance operations, the µ phase progressively breaks down into semicoherent platelets (µ µ phase) and then into incoherent globules having the structure of the AlgFeNi compound.

L'invention sera mieux comprise à l'aide des exemples suivants et figures suivantes:

  • La figure 1 représente l'évolution de la dureté des alliages après maintien de 10 mn à diverses températures.
  • La figure 2 représente, au grossissement 31000, la microstructure de l'alliage 8 après maintien de 10 mn à 400°C.
  • La figure 3 représente, au grossissement 31000, la microstructure de l'alliage 4 après maintien de 10 mn à 400°C.
The invention will be better understood using the following examples and the following figures:
  • FIG. 1 represents the evolution of the hardness of the alloys after maintaining 10 minutes at various temperatures.
  • FIG. 2 represents, at 31000 magnification, the microstructure of the alloy 8 after holding for 10 min at 400 ° C.
  • FIG. 3 represents, at 31000 magnification, the microstructure of alloy 4 after holding for 10 min at 400 ° C.

ExemplesExamples

Les alliages dont les compositions pondérales sont reportées au tableau 1, ont été élaborés sous forme de ruban 1 à 5 mn x 20 à 40 µm, par solidification rapide sur une roue de coulée en acier, animée d'une vitesse tangentielle de 45 m/seconde.The alloys, the weight compositions of which are given in Table 1, were produced in the form of a ribbon 1 to 5 min × 20 to 40 μm, by rapid solidification on a steel casting wheel, driven at a tangential speed of 45 m / second.

Ces alliages ont été portés 10 mn à différentes températures, entre 300 et 500°C et les mesures de microdureté Vickers sous 10 g ont été effectuées. Les résultats (moyenne de 6 essais) en sont reportés au tableau Il et représentés graphiquement sur la figure 1.These alloys were brought 10 minutes to different temperatures, between 300 and 500 ° C. and the Vickers microhardness measurements under 10 g were carried out. The results (average of 6 tests) are reported in Table II and shown graphically in Figure 1.

On peut constater que les alliages 2, 7, 8 qui sont hors du domaine de l'invention présentent une stabilité à chaud médiocre, relativement aux autres alliages conformes à l'invention. De plus, comme le montrent les essais effectués sur l'alliage 7 (et 8), une quantité minimale de nickel (et de Mo) est indispensable pour obtenir les bonnes propriétés de résistance à chaud: les compositions préférentielles (4, 5, 6) présentent les caractéristiques à chaud optimales.It can be seen that the alloys 2, 7, 8 which are outside the scope of the invention have poor heat stability, relative to the other alloys according to the invention. In addition, as shown by the tests carried out on alloy 7 (and 8), a minimum quantity of nickel (and of Mo) is essential in order to obtain the good heat resistance properties: the preferred compositions (4, 5, 6 ) have optimal hot characteristics.

Le tableau III donne les caractéristiques de résistance à chaud pour des maintiens de plus longue durée des alliages (4 à 6) à 400°C.Table III gives the characteristics of hot resistance for longer-lasting holdings of the alloys (4 to 6) at 400 ° C.

On remarque que sur les figures 2 et 3, pour une même température de maintien, l'alliage 4 présente une précipitation en plaquettes semi-cohérentes alors que dans l'alliage 8, la précipitation est déjà constituée de globules incohérents de phase type Al9FeNi. La stabilité thermique de l'alliage 4 est associée à la cinétique de décomposition plus lente observée sur cet alliage.Note that in Figures 2 and 3, for the same holding temperature, the alloy 4 has precipitation in semi-coherent platelets while in the alloy 8, the precipitation already consists of incoherent globules of phase type Al 9 FeNi. The thermal stability of alloy 4 is associated with the slower decomposition kinetics observed on this alloy.

Les alliages selon l'invention pourront être utilisés pour des parties de turbomachines fonctionnant à des températures inférieures à 350°C pendant d'assez longues durées ou fonctionnant à température plus élevée pendant des durées assez courtes (corps de missiles).The alloys according to the invention may be used for parts of turbomachines operating at temperatures below 350 ° C for fairly long periods or operating at higher temperature for fairly short periods (missile bodies).

Ils peuvent également être utilisés sous forme de revêtement sur des substrats de nature différente, et, éventuellement durcis par traitement laser ou bombardement électronique.

Figure imgb0001
Figure imgb0002
Figure imgb0003
 They can also be used as a coating on substrates of different nature, and, optionally hardened by laser treatment or electronic bombardment.
Figure imgb0001
Figure imgb0002
Figure imgb0003

Claims (10)

1. An Al-based alloy characterised in that it contains (in percent by weight):
Figure imgb0006
and optionally up to 5% in total of one (or more) element(s) from the group Si, Mn, Ti, Hf, Zr, V and Nb, the remainder being Al and inevitable impurities.
2. An alloy according to claim 1, characterised in that
5 ≤ Fe ≤ 10.
3. An alloy according to one of claims 1 and 2, characterised in that
Mo/Ni ≤ 2.
4. An alloy according to one of claims 1 to 3, charactersied in that
Mo ≥ 1.
5. An alloy according to one of claims 1 to 4, characterised in that in the crude state of solidification, the structure is a supersaturated solid Al-based solution.
6. An alloy according to one of claims 1 to 4, characterised in that in the crude state of solidification, besides the solid solution, it also includes a crystalline phase in which the interreticular distances as determined from diffraction plates are:
0.38-0.203 to 0.211 -0.147-0.125-0.107 nm.
7. An alloy according to claim 6, characterised in that the crystalline phase contains at least 1 % by weight of Ni and 1 % by weight of Mo.
8. An alloy according to one of claims 6 and 7, characterised in that in the crude state of solidification, the size of the grains of the crystalline phase is of the order of 1 nm.
9. An alloy according to claim 8, characterised in that the micro-crystalline phase forms a filiform system whose width, in a micrographic section, is between 5 and 50 nm.
10. A process for producing an alloy according to one of claims 1 to 9, characterised in that the rate of solidification is higher than 104 °C/second.
EP84420198A 1983-11-29 1984-11-27 Aluminium-based alloys having a high heat stability Expired EP0143727B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR8319434 1983-11-29
FR8319434A FR2555610B1 (en) 1983-11-29 1983-11-29 ALUMINUM ALLOYS HAVING HIGH HOT STABILITY

Publications (3)

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EP0143727A2 EP0143727A2 (en) 1985-06-05
EP0143727A3 EP0143727A3 (en) 1985-07-10
EP0143727B1 true EP0143727B1 (en) 1987-06-24

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EP (1) EP0143727B1 (en)
JP (1) JPS60215730A (en)
KR (1) KR850004122A (en)
DE (1) DE3464387D1 (en)
ES (1) ES8602149A1 (en)
FR (1) FR2555610B1 (en)
IL (1) IL73645A (en)
NO (1) NO162426C (en)

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2146352B (en) * 1982-09-03 1986-09-03 Alcan Int Ltd Aluminium alloys
JPS60234936A (en) * 1984-05-09 1985-11-21 Sumitomo Light Metal Ind Ltd Formed material with superior strength at high temperature made of material of aluminum alloy solidified by rapid
JPS6148551A (en) * 1984-08-13 1986-03-10 Sumitomo Light Metal Ind Ltd Formed material having superior strength at high temperature made of aluminium alloy material solidified by rapid cooling
FR2584095A1 (en) * 1985-06-28 1987-01-02 Cegedur AL ALLOYS WITH HIGH LI AND SI CONTENT AND METHOD OF MANUFACTURE
EP0218035A1 (en) * 1985-10-02 1987-04-15 Allied Corporation Rapidly solidified aluminum based, silicon containing, alloys for elevated temperature applications
US4878967A (en) * 1985-10-02 1989-11-07 Allied-Signal Inc. Rapidly solidified aluminum based, silicon containing alloys for elevated temperature applications
US4729790A (en) * 1987-03-30 1988-03-08 Allied Corporation Rapidly solidified aluminum based alloys containing silicon for elevated temperature applications
JPH01149936A (en) * 1987-12-04 1989-06-13 Honda Motor Co Ltd Heat-resistant al alloy for powder metallurgy

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR1195247A (en) * 1956-12-14 1959-11-16 Kaiser Aluminium Chem Corp Aluminum alloys
GB1192030A (en) * 1967-12-30 1970-05-13 Ti Group Services Ltd Aluminium Alloys
US4347076A (en) * 1980-10-03 1982-08-31 Marko Materials, Inc. Aluminum-transition metal alloys made using rapidly solidified powers and method
FR2529909B1 (en) * 1982-07-06 1986-12-12 Centre Nat Rech Scient AMORPHOUS OR MICROCRYSTALLINE ALLOYS BASED ON ALUMINUM

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KR850004122A (en) 1985-07-01
JPS60215730A (en) 1985-10-29
FR2555610A1 (en) 1985-05-31
EP0143727A2 (en) 1985-06-05
NO162426C (en) 1989-12-27
EP0143727A3 (en) 1985-07-10
FR2555610B1 (en) 1987-10-16
NO162426B (en) 1989-09-18
IL73645A0 (en) 1985-02-28
IL73645A (en) 1987-10-30
DE3464387D1 (en) 1987-07-30
NO844743L (en) 1985-05-30
ES538034A0 (en) 1985-11-01
ES8602149A1 (en) 1985-11-01

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