WO1992013111A1 - Aluminium alloys, substrates coated with same and their applications - Google Patents
Aluminium alloys, substrates coated with same and their applications Download PDFInfo
- Publication number
- WO1992013111A1 WO1992013111A1 PCT/FR1992/000030 FR9200030W WO9213111A1 WO 1992013111 A1 WO1992013111 A1 WO 1992013111A1 FR 9200030 W FR9200030 W FR 9200030W WO 9213111 A1 WO9213111 A1 WO 9213111A1
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- Prior art keywords
- alloys
- thermal
- alloy
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- quasicrystalline
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- 239000000758 substrate Substances 0.000 title claims abstract description 19
- 229910000838 Al alloy Inorganic materials 0.000 title description 8
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 166
- 239000000956 alloy Substances 0.000 claims abstract description 166
- 239000000203 mixture Substances 0.000 claims abstract description 28
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 9
- 229910052751 metal Inorganic materials 0.000 claims abstract description 9
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 9
- 239000002184 metal Substances 0.000 claims abstract description 8
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 8
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 7
- 229910052742 iron Inorganic materials 0.000 claims abstract description 7
- 229910052703 rhodium Inorganic materials 0.000 claims abstract description 7
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 7
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 6
- 239000000470 constituent Substances 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910052732 germanium Inorganic materials 0.000 claims abstract description 3
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 3
- 229910052763 palladium Inorganic materials 0.000 claims abstract description 3
- 238000012545 processing Methods 0.000 claims abstract description 3
- 229910052707 ruthenium Inorganic materials 0.000 claims abstract description 3
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 3
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 claims description 39
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- 239000004411 aluminium Substances 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 57
- 238000012360 testing method Methods 0.000 description 38
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- DOIRQSBPFJWKBE-UHFFFAOYSA-N dibutyl phthalate Chemical compound CCCCOC(=O)C1=CC=CC=C1C(=O)OCCCC DOIRQSBPFJWKBE-UHFFFAOYSA-N 0.000 description 4
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- RUDFQVOCFDJEEF-UHFFFAOYSA-N yttrium(III) oxide Inorganic materials [O-2].[O-2].[O-2].[Y+3].[Y+3] RUDFQVOCFDJEEF-UHFFFAOYSA-N 0.000 description 3
- 238000007088 Archimedes method Methods 0.000 description 2
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- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 2
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- 229910018084 Al-Fe Inorganic materials 0.000 description 1
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- 229910000809 Alumel Inorganic materials 0.000 description 1
- -1 Aluminum-Manganese Chemical compound 0.000 description 1
- 229910018192 Al—Fe Inorganic materials 0.000 description 1
- 229910018461 Al—Mn Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
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- 229910002544 Fe-Cr Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
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- 241000258241 Mantis Species 0.000 description 1
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- AZDRQVAHHNSJOQ-UHFFFAOYSA-N alumane Chemical class [AlH3] AZDRQVAHHNSJOQ-UHFFFAOYSA-N 0.000 description 1
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- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
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- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
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- 230000000877 morphologic effect Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 1
- 150000002829 nitrogen Chemical class 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
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- 239000001301 oxygen Substances 0.000 description 1
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Classifications
-
- 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
-
- 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
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
Definitions
- the present invention relates to alloys, the essential constituent of which is aluminum, the substrates coated with aluminum alloys, and their applications.
- metals or metal alloys for example aluminum alloys
- cooking utensils and appliances are known, anti-friction bearings, chassis or apparatus supports, various parts obtained by molding.
- most of these metals or metal alloys have drawbacks for certain applications, linked to their insufficient hardness and resistance to wear, and to their low resistance to corrosion, in particular in an alkaline medium.
- Various attempts have been made to obtain improved aluminum alloys.
- European patent 100287 describes a family of amorphous or microcrystalline alloys having improved hardness, usable as reinforcing elements of other materials or for obtaining surface coatings improving resistance to corrosion or to wear.
- a large number of the alloys described in this patent are not stable at temperatures above 200 ° C., and during a heat treatment, in particular the treatment to which they are subjected when deposited on a substrate, they change structure: return to the microcrystalline state in the case of essentially amorphous alloys, grain magnification for essential alloys-
- 35 talline or morphological induces a change in the physical characteristics of the material which essentially affects its density. This results in the appearance of micro-cracks, hence a brittleness, which adversely affects the mechanical stability of the materials.
- Thermal stability is an essential property for an alloy to be used as a thermal barrier.
- Thermal barriers are assemblies of one or more materials intended to limit the heat transfer to or from parts and components of equipment in many domestic or industrial devices. For example there may be mentioned the use 'of thermal barriers in the heating or cooking devices, irons at the attachment of the hot part of the carcass and thermal insulation; in cars, at several points such as the turbocharger, the exhaust pipe, the insulation of the passenger compartment, etc .; in aeronautics, for example on the rear of compressors and reactors.
- Thermal barriers are sometimes used in isolation in the form of a screen, but very often they are directly associated with the heat source or with the part to be protected for reasons of mechanical strength.
- mica sheets, ceramic plates, etc. are used in household utensils, adapting them by screwing or gluing, or sheets of agglomerated glass wool supported by a metal sheet.
- a particularly advantageous method for adding a thermal barrier to a part, in particular to a metallic part consists in depositing on a substrate the material constituting the barrier in the form of a layer of thickness determined by a thermal spraying technique such as plasma spraying. for example.
- thermal barrier with other materials also deposited in layers by thermal spraying.
- these other materials can be intended to ensure the protection of the barrier vis-à-vis external aggressions such as for example mechanical shocks, a corrosive medium, etc. or can serve as a sub-layer for bonding to the substrate.
- Mention may be made of alumina which has a specific mass lower than that of zirconia, a diffusivity and a specific heat greater than that of zirconia, but whose mechanical properties are not satisfactory. Mention may also be made of stainless steels and certain refractory steels which offer thermal insulation properties, but which have a high specific mass.
- the object of the present invention is to provide a family of alloys having high hardness and thermal stability, improved ductility and resistance to corrosion.
- the present invention thus relates to a new family of alloys, the essential constituent of which is aluminum.
- the invention also relates to the metallic coatings obtained from these alloys.
- Another object of the invention consists of the substrates coated with said alloys.
- M represents one or more elements chosen from Fe, Cr, Mn, Ni, Ru, Os, Mo, V, Mg, Zn, Pd;
- N represents one or more elements chosen from W, Ti, Zr, Hf, Rh, Nb, Ta, Y, Si, Ge, rare earths; I represents the inevitable processing impurities;
- the expression "quasi-crystal-line phase” includes: 1) the phases having rotation symmetries normally incompatible with translation symmetry, that is to say symmetries of axis of rotation of order 5, 8, 10 and 12, these symmetries being revealed by the diffraction of the radiation.
- This orthorhombic phase 0 * ⁇ is said to be approximate to the decagonal phase. It is so close to it that it is not possible to distinguish its X-ray diffraction pattern from that of the decagonal phase.
- This phase is an approximate phase of the icosahedral phase.
- phase C with a cubic structure, very often observed in coexistence with the approximate phases. mantis or quasicrystalline true.
- This phase is isotype of a hexagonal phase, noted AlMn, discovered in Al-Mn alloys containing 40% by weight of Mn [MA Taylor, Intermetallic phases in the Aluminum-Manganese Binary System, Acta Metallurgica 8 (1960) 256 ].
- the cubic phase, its superstructures and the phases derived therefrom, constitute a class of approximate phases of the quasicrystalline phases of neighboring compositions.
- alloys of the present invention mention may be made of those, hereinafter designated by (II), which have the above-mentioned atomic composition (I) in which 0 ⁇ b ⁇ 5, 0 ⁇ b ' ⁇ 22 and / or 0 ⁇ c ⁇ 5, and M represents Mn + Fe + Cr or Fe + Cr.
- These alloys (II) are more particularly intended for the coating of cooking utensils.
- alloys (VII) having composition (I) and which exhibit improved ductility are those for which c> 0, preferably 0 ⁇ c ⁇ 1, and / or 7 ⁇ b 1 ⁇ 14.
- the alloys of the present invention are distinguished from the alloys of the prior art, and in particular those of EP 356 287 by their copper content which is lower, or even zero. Alloys are therefore less sensitive to corrosion in an acid medium. In addition, the low copper content is more favorable for obtaining improved ductility by adding other elements such as B or C. In the alloys of the present invention, the copper can be replaced in whole or in part by cobalt. These alloys are therefore particularly advantageous with regard to hardness, ductility and resistance to corrosion both in an alkaline medium and in an acid medium in the range of intermediate pHs (5 ⁇ pH ⁇ 7). The combination of these different properties offers the alloys of the present invention a wide range of applications.
- the alloys of the present invention can for example be used as an anti-wear or reference surface coating or for the production of metal-metal or metal-ceramic joints. They are also suitable for all uses involving food contact.
- the alloys of the invention preferably those of the group
- VII can also be used for anti-shock surfaces.
- the alloys according to the invention of groups (III) and (V) are preferably used.
- the alloys of group (III) will preferably be used, whereas those of groups (III) and (IV) are particularly suitable for surfaces resistant to corrosion.
- the alloys of groups (III), (IV) and (VII) are particularly suitable for the production of anti-cavitation or anti-erosion surfaces.
- the materials of the present invention can be used to constitute thermal protection elements of a substrate, in the form of a thermal barrier or in the form of an undercoat of attachment for thermal barriers made of conventional materials. They have good thermal insulation properties, good mechanical properties, a low specific mass, good resistance to corrosion, especially to oxidation, and great ease of use.
- the quasicrystalline alloys of the present invention are therefore suitable substitutes for the replacement of many thermal barrier materials, and in particular of zirconia, with respect to which they have advantages of low specific mass, excellent mechanical properties in this which relates to hardness, improved resistance to wear, abrasion, scratching, as well as corrosion.
- the diffusivity of the materials constituting the thermal protection elements of the present invention is reduced when the porosity of the materials increases.
- the porosity of a quasi-crystalline alloy can be increased by an appropriate heat treatment.
- the materials constituting the thermal protection elements of the present invention may contain a small proportion of heat conducting particles, for example metallic aluminum crystals.
- the thermal conduction of the material will be dominated by the conduction properties of the matrix as long as the particles do not coalesce, that is to say as long as their volume proportion remains below the percolation threshold. For approximately spherical particles with a weakly distributed radius, this threshold is around 20%.
- This condition implies that the material constituting the thermal protection element contains at least 80% by volume of quasi-crystalline phases as defined above. Preferably, therefore, materials containing at least 80% of quasi-crystalline phase are used for their application as a thermal barrier.
- the thermal protection elements can be used as thermal barriers. Such temperature conditions correspond to most domestic or automotive applications. In addition, they have a great ability to resist the stresses due to the expansion of the support and their expansion coefficient is intermediate between that of metal alloys and that of insulating oxides.
- the quasicrystalline alloys constituting the thermal barriers can contain stabilizing elements chosen from W, Zr, Ti, Rh, Nb, Hf and Ta. The content of stabilizing element is less than or equal 2% by number of atoms.
- the thermal barriers of the present invention can be multi-layer barriers having an alternation of layers of materials which are good conductors of heat and layers of materials which are poor conductors which are alloys. almost crystalline.
- Such structures constitute, for example, abradable thermal barriers.
- the thermal protection elements of the present invention can be used as a bonding undercoat for a layer serving as a thermal barrier and constituted by a material. of the prior art such as zirconia. In these temperature ranges, the materials constituting the thermal protection elements of the present invention become super ⁇ plastic. They therefore correspond well to the conditions of use required for the production of a bonding sub-layer while being capable of participating themselves in the isolation of the substrate. Thus, the thermal protection elements of the present invention can be used up to a few tens of degrees from the melting point of the material from which they are made. This limit is around 950 ° C to 1200 ° C depending on the composition.
- the alloys according to the invention can be obtained by conventional metallurgical production processes, that is to say which comprise a slow cooling phase (ie ⁇ T / t less than a few hundred degrees).
- ingots can be obtained by melting separate metallic elements or pre-alloys in a graphite crucible brazed under a protective gas blanket (argon, nitrogen), a blanket flux used in conventional metallurgy ⁇ ration, or in a crucible kept under vacuum. It is also possible to use refractory ceramic or copper crucibles cooled by high frequency current heating.
- the preparation of the powders necessary for the metallization process can be carried out for example by mechanical grinding or by ato isation of the liquid alloy in a jet of argon according to a conventional technique.
- the alloying and atomizing operations can be carried out in sequence without requiring the casting of intermediate ingots.
- the alloys thus produced can be deposited in thin form, generally up to a few tens of micrometers, but also in thick form, up to several millimeters, by any metallization technique, including those which have already been mentioned.
- the alloys of the present invention can be used in the form of a surface coating by deposition from a pre-prepared ingot, or of ingots of the separate elements, taken as targets in a sputtering reactor, or also by vapor phase deposition. produced " by vacuum melting of the solid material. Other methods, for example those which employ sintering of agglomerated powder, can also be used.
- the coatings can also be obtained by thermal spraying, for example using an oxy-gas torch, a super-sonic torch or a plasma torch The thermal spray technique is particularly interesting for the development of thermal protection elements.
- the hardness of the alloys was determined using the WOLPERT V-Testor 2 durometer under loads of 30 and 400 grams.
- An estimate of the ductility of certain alloys was obtained by measuring the length of the cracks formed from the angles of the cavity under load of 400 grams. An average value of this length, as well as the hardness, was evaluated from at least 10 different fingerprints distributed on the sample. Another estimate of the ductility is based on the amplitude of the deformation produced before rupture during a compression test applied to a cylindrical specimen of 4.8 mm in diameter and 10 mm in height machined with perfectly parallel faces perpendicular to the cylinder axis. An INSTROM brand traction / compression machine was used.
- the electrical resistivity of the samples was measured at room temperature on cylindrical specimens 20 mm long and 4.8 mm in diameter.
- the conventional method known as 4 points was used, with a constant measuring current of 10 A.
- the voltage across the internal electrodes was measured with a high precision nanovoltmeter.
- a measurement was made as a function of the temperature using a specifically adapted oven.
- the melting temperatures of some alloys were determined on heating with a speed of 5 ° C / min by Differential Thermal Analysis on a SETARAM 2000C device.
- the crystallographic structure of the alloys was defined by analysis of their X-ray diffraction diagram and their electron diffraction diagrams.
- Example 1 Development of Quasicrystalline Alloys
- a series of alloys was produced by melting pure elements in a high frequency field under an argon atmosphere in a cooled copper crucible.
- the total mass thus produced was between 50 g and 100 g of alloy.
- the melting temperature which depends on the composition of the alloy, has always been found in the temperature range between 950 and 1200 a C.
- a cylindrical test tube full of 10 mm + 0.5 mm in diameter and a few centimeters in height was formed by aspiration of the molten metal in a quartz tube. The the cooling rate of this sample was close to 250 ° C per second.
- This sample was then cut with a diamond saw to shape the metallography and hardness specimens used in the examples below. Part of the test piece was fragmented for thermal stability tests and a crushed powder fraction for X-ray diffraction analysis of each alloy. A similar assembly was used to obtain the 4.8 mm diameter cylindrical samples intended for electrical resistivity. The cooling rate of the specimen was then close to 1000 ° C per second.
- Table 1 below gives the quasicrystalline phase content of the alloys according to the invention obtained, as well as the melting temperature of some of them.
- the X-ray diffraction patterns and the electron diffraction patterns were recorded for the quasicrystalline alloys listed in Table 1. Their study made it possible to determine the crystallographic nature of the phases present. This is how, for example, alloys 2, 5, 7, 8, 9, 19, 22 mainly have the O * phase. and the alloy 1 ma mainly phase C.
- the alloy 3 mainly contains phase H.
- the alloy 6 consists essentially of phase H, as well as a small fraction of phase C.
- the other alloys contain varying proportions of phases C, 0 * ⁇ , O 3 , O4 (and H for 23).
- a bath of one hundred (100) kilograms of an alloy producing a mass fraction of more than 95% of quasicrystalline phase has been developed.
- the nominal composition of the alloy was Al 6 7Cu9 f 5Fei 2 Cr * n ( 5 in number of atoms (alloy 39).
- tion was made from industrial metallic components, namely aluminum A5, a Cu-Al-Fe alloy containing 19.5% Al by weight, 58.5% Cu by weight and 21.5 % Fe by weight.
- These elements and alloys were introduced cold into a graphite crucible brazed with alumina. Their merger was carried out under a hedging flow which was maintained until the end of the operation.
- a high frequency generator of 125 k was used.
- the specific heat of the alloy was determined in the temperature range 20-80 "C with a SETARAM scanning calorimeter.
- the thermal diffusivity of a pellet of this alloy 15 mm thick and 32 mm in diameter was deduced from the temperature / time curve measured on one face of the patch, knowing that the opposite face, previously blackened, was irradiated by a laser flash of calibrated power and shape.
- the thermal conductivity is deduced from the two previous measurements, knowing the specific gravity of the alloy which has been measured by the Archimedes method by immersion in butyl phthalate maintained at 30 "C (+ 0.1 ° C) and found equal to 4.02 g / cm 3 . Comparative Example 3
- Thermal stability The thermal stability of some alloys of the present invention has been evaluated.
- the selected alloys were subjected to maintenance at different temperatures for periods ranging from a few hours to several tens of hours.
- Fragments extracted by breaking the ingots prepared according to Example 1 were placed in quartz ampoules sealed under secondary vacuum. The volume of these fragments was of the order of 0.25 cm 3 .
- the ampoules were placed in an oven previously heated to the treatment temperature. At the end of the treatment, they were cooled under vacuum to ambient temperature by natural convection in air or at a controlled speed. The fragments were then ground for X-ray diffraction examination. Electron diffraction examinations were also carried out.
- the experimental conditions of the heat treatments are summarized in table 3 below.
- the alloys of the present invention are thermally stable in the sense that their structure, as it is charac ⁇ terized by the appropriate diffraction figures, does not change essentially during isothermal heat treatments at temperatures which can reach the melting temperature of the alloys. In other words, the mass fraction of quasicrystalline phase present in the raw state of production does not decrease during temperature maintenance.
- Example 5 Oxidation resistance Samples in fragments identical to those described in Example 4 were subjected to heat treatments in an oven open to air, under conditions summarized in Table 4 below.
- Example 6 Morphology and Grain Size
- the alloys of the present invention are polycrystalline materials whose morphology has been studied by optical microscopy according to a conventional metallography technique.
- the 10 mm diameter pellets produced according to the method of Example 1 were finely polished and then attacked with an appropriate metallographic reagent.
- the metallographic images were photographed with an Olympus optical microscope, working in white light.
- the grain size observed is between a few micrometers and a few tens of micrometers.
- the same characterization method was applied to the samples treated with air in the temperature range 400 "C to 500 ° C as described in Table 4 of the example above. give in.
- the Vickers hardnesses of the alloys of the present invention and of certain alloys of the prior art were measured at room temperature on fragments of alloys produced according to the method of Example 1, coated in a resin for metallographic use, then finely polished. Two loads of the microdurometer, respectively 30g and 400g, were used. The results are given in Table 5 below.
- the Vickers hardnesses observed for the alloys of the present invention are particularly high in comparison with the Vickers hardnesses under load of 400 grams recorded for the alloys of the prior art prepared as in Example 3 (sample 41 to 46).
- the ductility of alloys with high hardness is relatively low.
- the alloys of the present invention containing cobalt have a higher ductility.
- additions for example of boron or carbon.
- compositions 41 to 46 and 40 are alloys of the prior art, the others are alloys according to the invention.
- the compositions of the prior art have an electrical resistivity at room temperature which is between a few ⁇ cm and a few tens of ⁇ cm.
- alloy 42 of composition Al ⁇ sCris in number of atoms which has a resistivity of 300 ⁇ cm. This value is to be compared with the presence of a rate of quasicrystalline phase fairly close, although lower, of 30% by mass. This state is however metastable and has only been achieved thanks to the high cooling rate which characterizes the method of preparation of the present test pieces.
- the characteristic values of the electrical resistivity of the alloys of the present invention are between 300 and 600 ⁇ cm.
- Such high values mean the quasicrystalline alloys of the present invention for any application where this property must be taken advantage of, such as, for example, Joule heating, resistors with high heat dissipation, electromagnetic coupling, possibly high frequency.
- an alloy representative of the family (III) has a low temperature coefficient of electrical resistivity (1 / p dp / dT).
- the relative variation of the electrical resistivity with the temperature of a test tube of alloy 2 was measured.
- This test tube was prepared from a tape 0.1 mm thick and 1.2 mm wide. produced by quenching the liquid alloy on a copper drum, the surface of which scrolled at a speed of 12 m / s (technique, known as melt spinning).
- the ingot brought to the liquid state had been prepared according to the method of example 1.
- the test piece was heated at a constant speed of 5 ° C./minute and kept in contact with four platinum wires according to the so-called measurement method. in four points.
- the difference between potential electrodes was 20 mm and the potential measurement carried out with a precision nanovoltmeter.
- a constant current of 10 A flowed through the test tube through the other two electrodes.
- the measuring device was kept under a protective argon flow in a suitable oven. It was found that the variation in resistance is linear, which demonstrates that no transformation of the sample takes place during the measurement or during the following heating cycle, in confirmation of the great thermal stability of the alloys (example 4).
- the temperature coefficient deduced from the curve (l / ⁇ (20 ° C)) (p (T) -p (20 ° C)) / ⁇ T is -3.10 - ***. This low value distinguishes the alloy for applications where it is preferable to keep the characteristics of the material within a narrow range as a function of the temperature, such as for example heating by electromagnetic induction.
- Example 9 Corrosion resistance The dissolution of certain alloys of the present invention in different media was measured as well as that of an alloy of the prior art.
- test tube 10 mm in diameter and 3 mm thick prepared according to the procedure of Example 1, was immersed for 30 h in a corrosive solution, at different temperatures. The solution was stirred for the duration of the immersion and kept at temperature by a thermostatically controlled bath. After 30 hours, the weight loss of each test piece was determined.
- the present invention provides alloys which have excellent corrosion resistance in an acid medium (No. 2, having a Cu content greater than 5 atomic%), or in a strongly alkaline medium (No. 3 and 6, having a cobalt content greater than 5 atomic%).
- the quasicrystalline alloys of the present invention combine several properties which designate them very particularly for many applications in the form of surface coatings: high hardness, low but not negligible ductility, thermal stability, high resistance to corrosion.
- high hardness low but not negligible ductility
- thermal stability high resistance to corrosion.
- these alloys retain these properties after they have been used as a surface coating. They then have a coefficient of friction remarkably weak which enriches the range of interesting properties already mentioned.
- An ingot of two kilograms of the alloy produced according to Example 2 was reduced to powder by grinding using a mill with carbide steel concentric rollers.
- the " powder thus obtained was sieved so as to retain only the fraction of grains whose size was between 25 ⁇ m minimum and 80 ⁇ m maximum.
- a deposit of 0.5 mm thick was then produced by spraying this powder onto a mild steel plate previously sandblasted. This spraying was carried out by means of a Metco flame torch fed by a mixture dosed with 63% hydrogen and 27% oxygen.
- Example 11 Thermal diffusivity at room temperature.
- the thermal diffusivity, the specific mass d and the specific heat Cp were determined in the vicinity of room temperature for several samples prepared according to Example 1 and one sample prepared according to Example 2.
- the samples prepared according to the method of 1 ' Example 1 are pellets 10 mm in diameter and 3 mm thick.
- the sample of Example 2 is a pellet 32 mm in diameter and 15 mm thick.
- test pieces The opposite faces of each pellet have been polished mechanically under water, taking great care to guarantee their parallelism.
- the structural state of the test pieces was determined by X-ray diffraction and by electron microscopy. All selected samples contained at least 90% quasicrystalline phase volume according to the definition given above.
- the thermal diffusivity has been determined using a laboratory device combining the laser flash method with an Hg-Cd-Te semiconductor detector. The laser was used to supply pulses of power between 20 J and 30 J with a duration of 5.10 "4 s, to heat the front face of the specimen and the semiconductor thermometer was used to detect the thermal response on the opposite side of the specimen. The thermal diffusivity was deduced from the experiments according to the method described in "A. Degiovanni, High Te p. - High Pressure, 17 (1985) 683.
- the specific heat of the alloy was determined in the temperature range 20-80 ° C with a SETARAM scanning calorimeter.
- the thermal conductivity ⁇ is deduced from the two previous measurements, knowing the specific mass of the alloy which has been measured by the Archimedes method by immersion in butyl phthalate maintained at 30 ° C (+ 0.1 ° C ).
- table 9 contains, for comparison, the values relating to some materials of the prior art (samples 5 to 13), some of which are known as thermal barrier (samples 5 to 8 ).
- the thermal conductivity of the quasicrystalline alloys constituting the protective elements of the present invention is considerably lower than that of metallic materials (aluminum metal or quadratic Al 2 Cu), given by way of comparison. It is two orders of magnitude less than that of aluminum and an order of magnitude to that of stainless steel usually considered as a good thermal insulator. In addition, it is lower than that of alumina and quite comparable to that of zirconia doped with Y 2 ° 3 'considered as the archetype of thermal insulators in 1'industrie.
- the thermal diffusivity of the alloys 90, 100, 110, 120 and 130 was determined. These alloys, which form defined aluminum compounds, have compositions close to those of the quasi-crystalline alloys which can be used for the protective elements of the present invention. However, they do not have the quasi-crystalline structure defined above. In all cases, their thermal diffusivity is greater than 5.10 " 6 m 2 / s, that is to say much greater than that of the alloys selected for the present invention.
- the measurement of the thermal diffusivity was carried out according to the method of Example 11.
- Each test tube was placed under a stream of purified argon in the center of an oven heated by the Joule effect; the temperature rise rate, programmed by computer, varied linearly at the rate of 5 ° C / min.
- All the samples according to the present invention show an approximately linear increase in o. with temperature.
- the value of o; determined at 700 ° C is close to twice that measured at room temperature.
- the specific heat increases with temperature and reaches from 800 to 900 J / kgK at 700 ° C.
- the specific mass decreases on the order of 1 to 2% as indicated by thermal expansion or neutron diffraction measurements.
- Figures 1, 2 and 3 respectively represent the evolution of a as a function of the temperature for the alloys 28, 31 and 33. The measurements recorded during heating are represented by black squares, those recorded during cooling by white squares.
- the variation in the thermal expansion of the alloy 2 was measured.
- the thermal expansion curve is app 'araître that the coefficient of expansion depends very little on the tempera- ture and is 9.10 -6 / ° C, the value close to that of stainless steels.
- Example 14 The superplastic behavior of certain alloys likely to constitute the thermal protection elements of the present invention was studied. Cylindrical test pieces 4 mm in diameter and 10 mm in length, with strictly parallel faces, were produced according to the same method as those of Example 1 with alloys 34 and 35. These test pieces were subjected mechanical compression tests on an INSTROM machine. Tests were carried out up to a load of 250 MPa, at a speed of movement of the beam of 50 ⁇ m / min, the temperature being kept constant between 600 and 850 ° C. The two alloys exhibit a superplastic behavior from 600 "C.
- Example 15 The superplastic behavior of certain alloys likely to constitute the thermal protection elements of the present invention was studied. Cylindrical test pieces 4 mm in diameter and 10 mm in length, with strictly parallel faces, were produced according to the same method as those of Example 1 with alloys 34 and 35. These test pieces were subjected mechanical compression tests on an INSTROM machine. Tests were carried out up to a load of 250 MPa, at a speed of movement of the beam
- a first series of test pieces has been produced.
- the substrate was a massive copper cylinder having a diameter of 30 mm and a height of 80 mm and the coating was applied with a plasma torch according to a conventional technique.
- the C0 test tube is the uncoated copper cylinder.
- the specimen Cl was coated over its entire surface with a layer of 1 mm thick of the alloy 2 and the specimen C2 was coated with a layer of 2 mm thick of the alloy 2.
- the C5 test tube comprises a layer of alloy 2 constituting the thermal protection element of the present invention serving as a bonding layer and a layer of yttria zirconia.
- the C3 and C4 test pieces used for comparison respectively comprise a layer of yttria-containing zirconia and a layer of alumina.
- test pieces A0 to A2 Another series of test pieces was produced with, as support, a stainless steel tube having a length of 50 cm, a diameter of 40 mm, a wall thickness of 1 mm (test pieces A0 to A2).
- the support tube is coated at one of its ends over a length of 30 cm.
- the deposits were made with an oxy-gas torch. Table 10 below gives the nature and thickness of the layers for the different test pieces. The precision on the final thicknesses of the deposits was + 0.3 mm. All the test pieces were fitted with very low inertia Chromel - Alumel thermocouples.
- FIG. 4 represents a test tube of the copper cylinder 1 type comprising a coating 2 and provided with a central thermocouple 3 and a lateral thermo ⁇ couple 4, both being inserted up to half the length of the cylinder .
- FIG. 5 represents a hollow tube 5 in which a flow of hot air 6 is passed and which is provided with three thermocouples designated respectively by TI, T2 and T3, the first two being inside the tube and placed respectively at beginning of the coated area and at the end of the coated area, and the third being on the outer surface of the coating.
- test pieces C0, Cl, C2, C3, C4 and C5 were placed on their base on a refractory brick. Successive heat pulses lasting 10 s were applied to each specimen at 60 s intervals and the response of the thermocouples was recorded. These pulses were produced by the flame of a torch, placed at a constant distance from the specimen and oriented opposite the thermocouple close to the surface. The flow of combustion gases was carefully controlled and kept constant throughout the experiment. Two series of experiments were carried out: one with tests vettes initially at 20 ° C and the other with test tubes initially at 650 ° C.
- the CO to C5 test tubes make it possible to define three parameters which summarize the results of the experiment, namely the maximum temperature difference P between the two thermo ⁇ couples, ⁇ T / ⁇ t the rate of temperature rise of the lateral thermo ⁇ couple 4 during the pulse and the temperature increment ⁇ T produced in the center of the test tube (thermocouple 3). These data are shown in Table 10. It was found that the zirconia layer of the C3 specimen did not resist more than three pulses and was cracked from the first pulse. The C2 sample did not start to crack until the sixth pulse and the C1 sample withstood more than 50 pulses. These results show that the protective elements of the present invention, used as a thermal barrier, have performances at least equivalent to those of zirconia.
- Example 17 Use of the protective elements according to the invention as a thermal barrier underlay.
- the thermal protection element of the present invention constitutes an undercoat. It was found that the zirconia layer of the C3 specimen did not resist more than three heat pulses and was cracked from the first pulse.
- the surface temperature of the zirconia deposit measured by a third thermocouple placed in contact with the deposit at the end of the tests, stabilized at 1200 ° C. .
- the thermal protection elements of the present invention are therefore well suited to the production of bonding sub-layers, in particular for thermal barriers.
- EXAMPLE 18 Application of a thermal protection element of the present invention to the insulation of a reactor.
- Test specimens A0, A1 and A2 were used to assess the ability of the alloys of the invention to thermally insulate a device.
- the test pieces were each provided with 3 thermocouples TI, T2 and T3 as shown in FIG. 5.
- a current of hot air at constant flow rate was sent through the stainless steel tube constituting the substrate of each test piece.
- the inlet air temperature, measured using the TI thermocouple was 300 + 2 "C.
- the surface temperature, measured using the T3 thermocouple was recorded as a function of the time from the start of the hot air generator
- the thermocouple T2 made it possible to verify that the transient conditions for establishing the hot air flow were identical for all the measurements.
- Figures 6 and 7 show the evolution of the surface temperature of each of the test pieces A0, Al and A2 as a function of time.
- the surface temperature of the AO specimen (without coating) exceeds at equilibrium that of the A2 specimen by 3
- thermal protection elements of the present invention give interesting results with regard to thermal insulation.
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Abstract
Alloys, the essential constituent of which is aluminium, metal deposits using on said alloys, substrates coated with same and their application. The alloys of the present invention are characterized by having the following atomic composition (I): Ala?Cub?Cob'?(B, C)c?Md?Ne?If?, a + b + b' + c + d + e + f = 100 number of atoms, a 50, 0 b < 14, 0 b' 22, 0 < b + b' 30, 0 c 5, 8 d 30, 0 e 4, f 2, M being one or more elements selected from Fe, Cr, Mn, Ni, Ru, Os, Mo, V, Mg, Zn, Pd; N being one or more elements selected from W, Ti, Zr, Hf, Rh, Nb, Ta, Y, Si, Ge, the rare earths; I being the impurities inevitably formed during processing; and in that they contain at least 30 % in mass of one or more quasicrystalline phases.
Description
Alliages d'aluminium, les substrats revêtus de ces alliages et leurs applications La présente invention concerne des alliages, dont le constituant essentiel est l'aluminium, les substrats revêtus de The present invention relates to alloys, the essential constituent of which is aluminum, the substrates coated with aluminum alloys, and their applications.
' 5 ces alliages et les applications de ces alliages, par exemple * pour la constitution d'éléments de protection thermi-que.'5 these alloys and the applications of these alloys, for example * for the constitution of thermal protection elements.
Divers métaux ou alliages métalliques, par exemple les alliages d'aluminium, ont trouvé jusqu'ici de nombreuses appli¬ cations en raison de leurs propriétés intéressantes et notam- 10 ment leurs propriétés mécaniques, leur bonne conductibilité thermique, leur légèreté, leur faible coût. Ainsi, on connaît par exemple les ustensiles et appareils de cuisson, les paliers anti-friction, les châssis ou supports d'appareillage, diverses pièces obtenues par moulage. 15 Toutefois la plupart de ces métaux ou alliages métalliques présentent des inconvénients pour certaines applications, liés à leur dureté et leur résistance à l'usure insuffisantes, et à leur faible résistance à la corrosion, en particulier en milieu alcalin. 20 Différentes tentatives ont été faites pour obtenir des alliages d'aluminium améliorés. Ainsi, le brevet européen 100287 décrit une famille d'alliages amorphes ou microcristal¬ lins présentant une dureté améliorée, utilisables comme éléments de renforcement d'autres matériaux ou pour 1•obtention 25 de revêtements superficiels améliorant la résistance à la corrosion ou à l'usure. Mais un grand nombre des alliages décrits dans ce brevet ne sont pas stables à des températures supérieures à 200°C, et lors d'un traitement thermique, notam¬ ment le traitement auquel ils sont soumis lors du dépôt sur un 30 substrat, ils changent de structure : retour à l'état micro- cristallin lorsqu'il s'agit d'alliages essentiellement amorphes, grossissement des grains pour les alliages essentiel-Various metals or metal alloys, for example aluminum alloys, have hitherto found numerous applications because of their advantageous properties and in particular their mechanical properties, their good thermal conductivity, their lightness, their low cost. . Thus, for example, cooking utensils and appliances are known, anti-friction bearings, chassis or apparatus supports, various parts obtained by molding. However, most of these metals or metal alloys have drawbacks for certain applications, linked to their insufficient hardness and resistance to wear, and to their low resistance to corrosion, in particular in an alkaline medium. Various attempts have been made to obtain improved aluminum alloys. Thus, European patent 100287 describes a family of amorphous or microcrystalline alloys having improved hardness, usable as reinforcing elements of other materials or for obtaining surface coatings improving resistance to corrosion or to wear. However, a large number of the alloys described in this patent are not stable at temperatures above 200 ° C., and during a heat treatment, in particular the treatment to which they are subjected when deposited on a substrate, they change structure: return to the microcrystalline state in the case of essentially amorphous alloys, grain magnification for essential alloys-
11 lement microcristallins qui ont initialement une dimension de „ grains inférieure au micron. Ce changement de structure cris-11 microcrystalline which initially have a grain size of less than one micron. This change in structure is
35 talline ou morphologique induit un changement des caractéris¬ tiques physiques du matériau qui affecte essentiellement sa
densité. Il en résulte l'apparition de micro-fissures, d'où une fragilité, qui nuisent à la stabilité mécanique des matériaux.35 talline or morphological induces a change in the physical characteristics of the material which essentially affects its density. This results in the appearance of micro-cracks, hence a brittleness, which adversely affects the mechanical stability of the materials.
Une autre famille d'alliages a été décrite dans EP 356287. Ces alliages présentent des propriétés améliorées. Toutefois, leur teneur en cuivre est relativement élevée.Another family of alloys has been described in EP 356287. These alloys have improved properties. However, their copper content is relatively high.
La stabilité thermique est une propriété indispensable pour qu'un alliage puisse être utilisé comme barrière ther¬ mique.Thermal stability is an essential property for an alloy to be used as a thermal barrier.
Les barrières thermiques sont des assemblages d'un ou plusieurs matériaux destinés à limiter le transfert thermique vers ou à partir de pièces et composants d'appareillages dans de nombreux dispositifs domestiques ou industriels. On peut citer par exemple l'utilisation ' de barrières thermiques dans les dispositifs de chauffage ou de cuisson, les fers à repasser au niveau de la fixation de la partie chaude sur la carcasse et de l'isolation thermique; dans les automobiles, en plusieurs points tels que le turbocompresseur, le pot d'échappement, l'isolation de l'habitacle, etc.; dans l'aéronautique, par exemple sur la partie arrière des compresseurs et des réac- teurs.Thermal barriers are assemblies of one or more materials intended to limit the heat transfer to or from parts and components of equipment in many domestic or industrial devices. For example there may be mentioned the use 'of thermal barriers in the heating or cooking devices, irons at the attachment of the hot part of the carcass and thermal insulation; in cars, at several points such as the turbocharger, the exhaust pipe, the insulation of the passenger compartment, etc .; in aeronautics, for example on the rear of compressors and reactors.
Les barrières thermiques sont quelquefois employées isolé¬ ment sous la forme d'écran, mais très souvent elles sont direc¬ tement associées à la source de chaleur ou à la partie à protéger pour des raisons de tenue mécanique. Ainsi, on utilise des feuilles de mica, des plaques de céramique, etc... ,dans les ustensiles électroménagers, en les adaptant par vissage ou collage, ou encore des feuilles de laine de verre agglomérée supportées par une tôle métallique. Un procédé particulièrement avantageux pour adjoindre une barrière thermique à une pièce, en particulier à une pièce métallique, consiste à déposer sur un substrat le matériau constituant la barrière sous forme de couche d'épaisseur déterminée par une technique de projection thermique telle que la projection plasma par exemple.Thermal barriers are sometimes used in isolation in the form of a screen, but very often they are directly associated with the heat source or with the part to be protected for reasons of mechanical strength. Thus, mica sheets, ceramic plates, etc. are used in household utensils, adapting them by screwing or gluing, or sheets of agglomerated glass wool supported by a metal sheet. A particularly advantageous method for adding a thermal barrier to a part, in particular to a metallic part, consists in depositing on a substrate the material constituting the barrier in the form of a layer of thickness determined by a thermal spraying technique such as plasma spraying. for example.
Très souvent, il est recommandé d'associer la barrière thermique à d'autres matériaux également déposés en couche par projection thermique. Ces autres matériaux peuvent être destinés à assurer la protection de la barrière vis-à-vis
d'agressions extérieures comme par exemple des chocs méca¬ niques, un milieu corrosif, etc.. ou peuvent servir de sous- couche d'accrochage au substrat.Very often, it is recommended to combine the thermal barrier with other materials also deposited in layers by thermal spraying. These other materials can be intended to ensure the protection of the barrier vis-à-vis external aggressions such as for example mechanical shocks, a corrosive medium, etc. or can serve as a sub-layer for bonding to the substrate.
Le matériau le plus fréquemment utilisé dans l'aéronautique pour constituer des barrières thermiques est la zircone yttriée qui résiste à des températures très élevées. Le dépôt de zircone est réalisé par projection plasma selon une technique classique à partir de poudre du matériau. La zircone présente une faible diffusivité thermique (o. = 10~6 m2/s) . Toutefois, elle présente une masse spécifique d relativement élevée, ce qui constitue un inconvénient pour certaines applications ; en outre, certaines de ses propriétés mécaniques, telles que la dureté, la résistance à l'usure et à l'abrasion sont faibles. D'autres matériaux sont utilisés comme barrière thermique. On peut citer l'alumine qui présente une masse spécifique infé¬ rieure à celle de la zircone, une diffusivité et une chaleur spécifique supérieures à celles de la zircone, mais dont les propriétés mécaniques ne sont pas satisfaisantes. On peut également citer les aciers inoxydables et certains aciers réfractaires qui offrent des propriétés d'isolation thermique, mais qui présentent une masse spécifique élevée.The most frequently used material in aeronautics to form thermal barriers is yttria zirconia which withstands very high temperatures. The deposition of zirconia is carried out by plasma spraying according to a conventional technique from powder of the material. Zirconia has a low thermal diffusivity (o. = 10 ~ 6 m 2 / s). However, it has a relatively high specific mass d, which is a drawback for certain applications; in addition, some of its mechanical properties, such as hardness, resistance to wear and abrasion are low. Other materials are used as a thermal barrier. Mention may be made of alumina which has a specific mass lower than that of zirconia, a diffusivity and a specific heat greater than that of zirconia, but whose mechanical properties are not satisfactory. Mention may also be made of stainless steels and certain refractory steels which offer thermal insulation properties, but which have a high specific mass.
La présente invention a pour but de fournir une famille d'alliages ayant une dureté et une stabilité thermique élevées, une ductilité et une résistance à la corrosion améliorées. La présente invention a ainsi pour objet une nouvelle famille d'alliages dont le constituant essentiel est l'alumi¬ nium.The object of the present invention is to provide a family of alloys having high hardness and thermal stability, improved ductility and resistance to corrosion. The present invention thus relates to a new family of alloys, the essential constituent of which is aluminum.
L'invention a également pour objet les revêtements métal¬ liques obtenus à partir de ces alliages. Un autre objet de l'invention est constitué par les substrats revêtus par lesdits alliages.The invention also relates to the metallic coatings obtained from these alloys. Another object of the invention consists of the substrates coated with said alloys.
Enfin, un autre objet est constitué par les applications desdits alliages.Finally, another object is constituted by the applications of said alloys.
Les alliages de la présente invention sont caractérisés en ce que :The alloys of the present invention are characterized in that:
- qu'ils présentent la composition atomique (I) suivante :- they have the following atomic composition (I):
AlaCUbCθb'(B,C)cMdNeIf (I)
dans la-quelle : a + b + b ' + c + d + e + f = 100 en nombre d ' atomes a > 50 0 < b < 14 0 < b 1 < 22Al a CU b Cθ b ' (B, C) c M d N e I f (I) in which: a + b + b '+ c + d + e + f = 100 in number of atoms a> 50 0 <b <14 0 <b 1 <22
0 < b + b ' < 30 0 < c ≤ 5 8 ≤ d ≤ 30 0 ≤ e ≤ 4 f < 20 <b + b '<30 0 <c ≤ 5 8 ≤ d ≤ 30 0 ≤ e ≤ 4 f <2
M représente un ou plusieurs éléments choisis parmi Fe, Cr, Mn, Ni, Ru, Os, Mo, V, Mg, Zn, Pd ;M represents one or more elements chosen from Fe, Cr, Mn, Ni, Ru, Os, Mo, V, Mg, Zn, Pd;
N représente un ou plusieurs éléments choisis parmi W, Ti, Zr, Hf, Rh, Nb, Ta, Y, Si, Ge, les terres rares ; I représente les impuretés d'élaboration inévitables ;N represents one or more elements chosen from W, Ti, Zr, Hf, Rh, Nb, Ta, Y, Si, Ge, rare earths; I represents the inevitable processing impurities;
- et qu'ils contiennent au moins 30% en masse d'une ou plusieurs phases quasicristallines.- And that they contain at least 30% by mass of one or more quasicrystalline phases.
Dans le présent texte, l'expression "phase quasi-cristal¬ line" englobe : 1) les phases présentant des symétries de rotation norma¬ lement incompatibles avec la symétrie de translation, c'est-à- dire des symétries d'axe de rotation d'ordre 5, 8, 10 et 12, ces symétries étant révélées par la diffraction du rayonnement. A titre d'exemple, on peut citer la phase icosaédrique I de groupe ponctuel m3 5 (cf. D. Shechtman, I. Blech, D. Gratias, J. . Cahn, Metallic Phase w±th Long-Range Orientational Order and No Translational Symmetry, Physical Revie Letters, Vol. 53, n° 20, 1984, pages 1951-1953) et la phase décagonale D de groupe ponctuel 10/mmm (cf. L. Benders y, Quasicrystal with One Dimensional Translational Symmetry and a Tenfold Rotation .Axis, Physical Review Letters, Vol. 55, n° 14, 1985, pages 1461- 1463) . Le diagramme de diffraction des rayons X drune phase décagonale vraie a été publié dans "Diffraction approach to the structure of decagonal quasicrystals, J.M. Dubois, C. Janot, J. Pannetier, A. Pianelli, Physics Letters A 117-8 (1986) 421-
2) les phases approximantes ou composés approximants qui sont des cristaux vrais dans la mesure où leur structure cris- tallographique reste compatible avec la symétrie de transla¬ tion, mais qui présentent, dans le cliché de diffraction d'électrons, des figures de diffraction dont la symétrie est proche des axes de rotation 5, 8, 10 ou 12. Certaines d'entre ces phases approximantes avaient été identifiées dans des composés de l'art antérieur. D'autres ont été mises en évidence dans certains alliages de la présente invention. Parmi ces phases, on peut citer à titre d'exemple la phase orthorhombique 0ι, caractéristique d'un alliage de l'art anté¬ rieur ayant la composition atomique Al65Cu2oFeιoCrs, dont les paramètres de maille sont : a0d> = 2,366, b0d) = 1,267, c0<*ι> = 3,252 en nanomètres. Cette phase orthorhombique 0*ι est dite approximante de la phase décagonale. Elle en est d'ailleurs si proche qu'il n'est pas possible de distinguer son diagramme de diffraction des rayons X de celui de la phase décagonale.In the present text, the expression "quasi-crystal-line phase" includes: 1) the phases having rotation symmetries normally incompatible with translation symmetry, that is to say symmetries of axis of rotation of order 5, 8, 10 and 12, these symmetries being revealed by the diffraction of the radiation. As an example, we can cite the icosahedral phase I of point group m3 5 (cf. D. Shechtman, I. Blech, D. Gratias, J.. Cahn, Metallic Phase w ± th Long-Range Orientational Order and No Translational Symmetry, Physical Revie Letters, Vol. 53, No. 20, 1984, pages 1951-1953) and the decagonal phase D of point group 10 / mmm (cf. L. Benders y, Quasicrystal with One Dimensional Translational Symmetry and a Tenfold Rotation. Axis, Physical Review Letters, Vol. 55, n ° 14, 1985, pages 1461-1463). The diffraction pattern of X-rays d r a true decagonal phase was published in "approach to the diffraction structure of membered Quasicrystals, JM Dubois, C. Janot, J. Pannetier, A. Pianelli, Physics Letters 117-8 (1986 ) 421- 2) the approximate phases or approximate compounds which are true crystals insofar as their crystallographic structure remains compatible with the symmetry of transla¬ tion, but which present, in the electron diffraction plate, diffraction figures including the symmetry is close to the axes of rotation 5, 8, 10 or 12. Some of these approximate phases had been identified in compounds of the prior art. Others have been demonstrated in certain alloys of the present invention. Among these phases, one can cite by way of example the orthorhombic phase 0ι, characteristic of an alloy of the prior art having the atomic composition Al65Cu 2 oFeιoCrs, the mesh parameters of which are: a 0 d> = 2.366 , b 0 d) = 1.267, c 0 <* ι> = 3.252 in nanometers. This orthorhombic phase 0 * ι is said to be approximate to the decagonal phase. It is so close to it that it is not possible to distinguish its X-ray diffraction pattern from that of the decagonal phase.
On peut également citer la phase rhomboédrique de para¬ mètres aR = 3,208 nm, a = 36°, présente dans les alliages de composition voisine de Al64Cu24Fei2 en nombre d'atomes (M. Audier et P. Guyot, Microcrystalline AlFeCu Phase of Pseudo Icosahe- dral Symmetry, in Quasicrystals, eds. M.V. Jaric et S. Lundqvist, World Scientific, Singapore, 1989) .We can also cite the rhombohedral phase of parameters at R = 3.208 nm, a = 36 °, present in the alloys of composition close to Al64Cu 2 4Fei2 in number of atoms (M. Audier and P. Guyot, Microcrystalline AlFeCu Phase of Pseudo Icoshadral Symmetry, in Quasicrystals, eds. MV Jaric and S. Lundqvist, World Scientific, Singapore, 1989).
Cette phase est une phase approximante de la phase icosa- édrique.This phase is an approximate phase of the icosahedral phase.
On peut aussi citer des phases 02 et O3 orthorhombiques de paramètres respectifs ao**2-1 = 3,83 ; bo<* > = 0,41 ; c0<2> = 5,26 et ao**3-1 = 3,25 ; bot3-* = 0,41 ; Co"*3-* = 9,8 en nanomètres présentes dans un alliage de composition Al63C *,7#5Coi7f5Si2 en nombre d'atomes ou encore la phase orthorhombique O4 de paramètres a0<<*) = 1,46 ; bo'*'**.1 = 1,23 ; c0 (.->r = 1,24 en nanomètres qui se forme dans l'alliage de composition Al63CU8Fei2Cri2 en nombre d'atomes de la présente invention. Les approximants orthorhom¬ biques sont décrits par exemple dans C. Dong, J.M. Dubois, J. Materials Science, 2_6 (1991) , 1647.We can also cite orthorhombic phases 0 2 and O 3 with respective parameters a o ** 2 - 1 = 3.83; b o <*> = 0.41; c 0 <2> = 5.26 and ao ** 3 - 1 = 3.25; bot 3 - * = 0.41; Co "* 3 - * = 9.8 in nanometers present in an alloy of composition Al63C *, 7 # 5Coi7 f 5Si2 in number of atoms or also the orthorhombic phase O4 with parameters a 0 << *) = 1.46; b o '*' **. 1 = 1.23; c 0 ( .-> r = 1.24 in nanometers which is formed in the alloy of composition Al63CU8Fei2Cri 2 in number of atoms of the present invention. The approximants orthorhom¬ biques are described for example in C. Dong, JM Dubois, J. Materials Science, 2_6 (1991), 1647.
On peut encore citer une phase C, de structure cubique, très souvent observée en coexistence avec les phases approxi-
mantes ou quasicristallines vraies. Cette phase qui se forme dans certains alliages Al-Cu-Fe et Al-Cu-Fe-Cr, consiste en une surstructure, par effet d'ordre chimique des éléments d'alliage par rapport aux sites d'aluminium, d'une phase de structure type Cs-Cl et de paramètre de réseau a*ι = 0,297 n .We can also cite a phase C, with a cubic structure, very often observed in coexistence with the approximate phases. mantis or quasicrystalline true. This phase, which is formed in certain Al-Cu-Fe and Al-Cu-Fe-Cr alloys, consists of a super-structure, by chemical effect of the alloying elements compared to the aluminum sites, of a phase Cs-Cl type structure and network parameter a * ι = 0.297 n.
Un diagramme de diffraction de cette phase cubique a été publié (C. Dong, J.M. Dubois, M. de Boissieu, C. Janot ; Neutron diffraction study of the peritectic growth of the Alg5CU2oFei5 icosahedral quasicrystal; J. Phys. Condensed Matter, 2 (1990) , 6339-6360) pour un échantillon de phase cubique pure et de composition AlόsCu∑oFe-is en nombre d'atomes.A diffraction diagram of this cubic phase has been published (C. Dong, JM Dubois, M. de Boissieu, C. Janot; Neutron diffraction study of the peritectic growth of the Alg 5 CU 2 oFei 5 icosahedral quasicrystal; J. Phys. Condensed Matter, 2 (1990), 6339-6360) for a sample of pure cubic phase and of composition Al ό sCu∑oFe-is in number of atoms.
On peut aussi citer une phase H de structure hexagonale qui dérive directement de la phase C comme le démontrent les relations d'épitaxie observées par microscopie électronique entre cristaux des phases C et H et les relations simples qui relient les paramètres des réseaux cristallins, à savoir u = 3 a*-/ ? (à 4,5% près) et cH = 3 fi? ai/2 (à 2,5% près). Cette phase est isotype d'une phase hexagonale, notée AlMn, décou¬ verte dans des alliages Al-Mn contenant 40% en poids de Mn [M.A. Taylor, Intermetallic phases in the Aluminium-Manganèse Binary System, Acta Metallurgica 8 (1960) 256].One can also cite a phase H of hexagonal structure which derives directly from phase C as demonstrated by the epitaxy relations observed by electron microscopy between crystals of phases C and H and the simple relations which connect the parameters of the crystal lattices, namely u = 3 a * - /? (to within 4.5%) and c H = 3 fi? ai / 2 (to within 2.5%). This phase is isotype of a hexagonal phase, noted AlMn, discovered in Al-Mn alloys containing 40% by weight of Mn [MA Taylor, Intermetallic phases in the Aluminum-Manganese Binary System, Acta Metallurgica 8 (1960) 256 ].
La phase cubique, ses surstructures et les phases qui en dérivent, constituent une classe de phases approximantes des phases quasicristallines de compositions voisines. Parmi les alliages de la présente invention, on peut citer ceux, désignés ci-après par (II) , qui présentent la composition atomique (I) précitée dans laquelle 0 < b < 5, 0 < b' < 22 et /ou 0 < c ≤ 5, et M représente Mn + Fe + Cr ou Fe + Cr. Ces alliages (II) sont plus particulièrement destinés aux revê- tements d'ustensiles de cuisson.The cubic phase, its superstructures and the phases derived therefrom, constitute a class of approximate phases of the quasicrystalline phases of neighboring compositions. Among the alloys of the present invention, mention may be made of those, hereinafter designated by (II), which have the above-mentioned atomic composition (I) in which 0 <b <5, 0 <b '<22 and / or 0 < c ≤ 5, and M represents Mn + Fe + Cr or Fe + Cr. These alloys (II) are more particularly intended for the coating of cooking utensils.
Une autre famille particulièrement intéressante, désignée ci-après par (III) , présente la composition atomique (I) préci¬ tée dans laquelle 15 < d < 30 et M représente au moins Fe + Cr, avec un rapport atomique Fe/Cr < 2. Ces alliages (III) présentent une résistance à l'oxydation particulièrement élevée.
En outre, parmi les alliages (III) on peut distinguer une famille d'alliages (IV) particulièrement résistant à la corro¬ sion:Another particularly interesting family, designated below by (III), presents the above atomic composition (I) in which 15 <d <30 and M represents at least Fe + Cr, with an atomic ratio Fe / Cr <2 These alloys (III) have a particularly high resistance to oxidation. In addition, among the alloys (III) one can distinguish a family of alloys (IV) particularly resistant to corrosion:
- en milieu faiblement acide (5 < pH < 7) si b > 6, b' < 7 et e > 0 avec N choisi parmi Ti, Zr, Rh et Nb en milieu fortement alcalin (jusqu'à pH = 14) si b ≤ 2, b1 > 7 et e > 0.- in weakly acidic medium (5 <pH <7) if b> 6, b '<7 and e> 0 with N chosen from Ti, Zr, Rh and Nb in strongly alkaline medium (up to pH = 14) if b ≤ 2, b 1 > 7 and e> 0.
Une autre famille d'alliages (V) intéressants par "le fait qu'ils offrent une résistance améliorée à la croissance de grain jusqu'à 700°C présente la composition des alliages (I) avec 0 < e ≤ 1, N étant choisi parmi W, Ti, Zr, Rh, Nb, Hf etAnother family of alloys (V) of interest by " the fact that they offer improved resistance to grain growth up to 700 ° C. presents the composition of the alloys (I) with 0 <e ≤ 1, N being chosen among W, Ti, Zr, Rh, Nb, Hf and
Ta.Your.
Une autre famille d'alliages (VI), ayant une dureté améliorée, présente la composition des alliages (I) , avec b < 5 et b1 > 5, de préférence b < 2 et b' > 7.Another family of alloys (VI), having improved hardness, presents the composition of the alloys (I), with b <5 and b 1 > 5, preferably b <2 and b '> 7.
Enfin, les alliages (VII) ayant la composition (I) et qui présentent une ductilité améliorée sont ceux pour lesquels c > 0, de préférence 0 < c ≤ 1, et/ou 7 ≤ b1 ≤ 14.Finally, the alloys (VII) having composition (I) and which exhibit improved ductility are those for which c> 0, preferably 0 <c ≤ 1, and / or 7 ≤ b 1 ≤ 14.
Les alliages de la présente invention se distinguent des alliages de l'art antérieur, et notamment de ceux de EP 356 287 par leur teneur en cuivre plus faible, voire nulle. Les alliages sont, de ce fait, moins sensibles à la corrosion en milieu acide. En outre, la faible teneur en cuivre est plus favorable à l'obtention d'une ductilité améliorée par addition d'autres éléments tels que B ou C. Dans les alliages de la présente invention, le cuivre peut être remplacé en tout ou partie par le cobalt. Ces alliages sont alors particulièrement intéressants en ce qui concerne la dureté, la ductilité et la résistance à la corrosion tant en milieu alcalin qu'en milieu acide dans la gamme des pH intermédiaires (5 < pH < 7) . La conjugaison de ces différentes propriétés offre aux alliages de la présente invention un large éventail d'applications.The alloys of the present invention are distinguished from the alloys of the prior art, and in particular those of EP 356 287 by their copper content which is lower, or even zero. Alloys are therefore less sensitive to corrosion in an acid medium. In addition, the low copper content is more favorable for obtaining improved ductility by adding other elements such as B or C. In the alloys of the present invention, the copper can be replaced in whole or in part by cobalt. These alloys are therefore particularly advantageous with regard to hardness, ductility and resistance to corrosion both in an alkaline medium and in an acid medium in the range of intermediate pHs (5 <pH <7). The combination of these different properties offers the alloys of the present invention a wide range of applications.
Les alliages de la présente invention peuvent par exemple être utilisés comme revêtement de surface anti-usure ou de surface de référence ou pour la réalisation de joints métal- métal ou métal-céramique. Ils conviennent également pour toutes les utilisations impliquant un contact alimentaire.
Les alliages de l'invention, de préférence ceux du groupeThe alloys of the present invention can for example be used as an anti-wear or reference surface coating or for the production of metal-metal or metal-ceramic joints. They are also suitable for all uses involving food contact. The alloys of the invention, preferably those of the group
(VII) , peuvent aussi être utilisés pour les surfaces anti-choc.(VII), can also be used for anti-shock surfaces.
Pour des applications électriques ou électrotechniques, ou pour le chauffage haute fréquence, on utilisera de préférence les alliages selon l'invention des groupes (III) et (V).For electrical or electrotechnical applications, or for high frequency heating, the alloys according to the invention of groups (III) and (V) are preferably used.
Pour réaliser des surfaces résistant à l'oxydation, on utilisera de préférence les alliages du groupe (III) , alors que ceux des groupes (III) et (IV) conviennent particulièrement bien pour les surfaces résistant à la corrosion. Les alliages des groupes (III) , (IV) et (VII) sont parti¬ culièrement adaptés à la réalisation de surfaces anti-cavita- tion ou anti-érosion.To produce surfaces resistant to oxidation, the alloys of group (III) will preferably be used, whereas those of groups (III) and (IV) are particularly suitable for surfaces resistant to corrosion. The alloys of groups (III), (IV) and (VII) are particularly suitable for the production of anti-cavitation or anti-erosion surfaces.
Les matériaux de la présente invention, et plus particuliè¬ rement ceux du groupe (V) , peuvent être utilisés pour consti- tuer des éléments de protection thermique d'un substrat, sous forme de barrière thermique ou sous forme de sous-couche d'accrochage pour des barrières thermiques constituées par des matériaux conventionnels. Ils présentent de bonnes propriétés d'isolation thermique, de bonnes propriétés mécaniques, une faible masse spécifique, une bonne résistance à la corrosion, surtout à l'oxydation, et une grande facilité de mise en oeuvre.The materials of the present invention, and more particularly those of group (V), can be used to constitute thermal protection elements of a substrate, in the form of a thermal barrier or in the form of an undercoat of attachment for thermal barriers made of conventional materials. They have good thermal insulation properties, good mechanical properties, a low specific mass, good resistance to corrosion, especially to oxidation, and great ease of use.
Les matériaux de la présente invention, utilisables pour la réalisation d'éléments de protection thermique selon la présente invention présentent des valeurs de diffusivité ther¬ mique or voisines de 10~6 m2/s qui sont très comparables à la diffusivité thermique de la zircone. Compte-tenu de la plus faible masse spécifique d de ces matériaux, la conductibilité thermique λ = αdCp au voisinage de la température ambiante ne présente pas de différence significative par rapport à celle de la zircone. Les alliages quasicristallins de la présente inven¬ tion sont donc des substituts indiqués au remplacement de nombreux matériaux de barrière thermique, et en particulier de la zircone, par rapport à laquelle ils présentent des avantages de faible masse spécifique, d'excellentes propriétés mécaniques en ce qui concerne la dureté, la résistance améliorée à l'usure, à l'abrasion, à la rayure, ainsi qu'à la corrosion.
La diffusivité des matériaux constituant les éléments de protection thermique de la présente invention est réduite lorsque la porosité des matériaux augmente. La porosité d'un alliage quasi-cristallin peut être augmentée par un traitement thermique approprié.The materials of the present invention which can be used for producing thermal protection elements according to the present invention have values of thermal diffusivity or gold close to 10 ~ 6 m 2 / s which are very comparable to the thermal diffusivity of zirconia . Given the lower specific gravity d of these materials, the thermal conductivity λ = αdCp in the vicinity of room temperature does not differ significantly from that of zirconia. The quasicrystalline alloys of the present invention are therefore suitable substitutes for the replacement of many thermal barrier materials, and in particular of zirconia, with respect to which they have advantages of low specific mass, excellent mechanical properties in this which relates to hardness, improved resistance to wear, abrasion, scratching, as well as corrosion. The diffusivity of the materials constituting the thermal protection elements of the present invention is reduced when the porosity of the materials increases. The porosity of a quasi-crystalline alloy can be increased by an appropriate heat treatment.
Les matériaux constituant les éléments de protection ther¬ mique de la présente invention peuvent contenir une faible proportion de particules conductrices de la chaleur, par exemple des cristaux d'aluminium métallique. La conduction thermique du matériau sera dominée par les propriétés de conduction de la matrice tant que les particules ne coalescent pas, c'est-à-dire tant que leur proportion volumique reste en- dessous du seuil de percolation. Pour des particules approxima¬ tivement sphériques et ayant un rayon faiblement distribué, ce seuil se situe aux environs de 20%. Cette condition implique que le matériau constituant l'élément de protection thermique contienne au moins 80% en volume de phases quasi-cristallines telles que définies ci-dessus. De préférence, on utilise donc des matériaux contenant au moins 80% de phase quasi-cristal- line, pour leur application comme barrière thermique.The materials constituting the thermal protection elements of the present invention may contain a small proportion of heat conducting particles, for example metallic aluminum crystals. The thermal conduction of the material will be dominated by the conduction properties of the matrix as long as the particles do not coalesce, that is to say as long as their volume proportion remains below the percolation threshold. For approximately spherical particles with a weakly distributed radius, this threshold is around 20%. This condition implies that the material constituting the thermal protection element contains at least 80% by volume of quasi-crystalline phases as defined above. Preferably, therefore, materials containing at least 80% of quasi-crystalline phase are used for their application as a thermal barrier.
Aux températures inférieures à environ 700°C, les éléments de protection thermique peuvent être utilisés comme barrières thermiques. De telles conditions de température correspondent à la plupart des applications domestiques ou dans le domaine de l'automobile. En outre, ils ont une grande aptitude à résister aux contraintes dues à la dilatation du support et leur coeffi¬ cient de dilatation est intermédiaire entre celui des alliages métalliques et celui des oxydes isolants. De préférence, pour les températures supérieures à environ 600"C, les alliages quasicristallins constituant les barrières thermiques peuvent contenir des éléments stabilisants choisis parmi W, Zr, Ti, Rh, Nb, Hf et Ta. La teneur en élément stabilisant est inférieure ou égale à 2% en nombre d'atomes.At temperatures below about 700 ° C, the thermal protection elements can be used as thermal barriers. Such temperature conditions correspond to most domestic or automotive applications. In addition, they have a great ability to resist the stresses due to the expansion of the support and their expansion coefficient is intermediate between that of metal alloys and that of insulating oxides. Preferably, for temperatures above about 600 "C, the quasicrystalline alloys constituting the thermal barriers can contain stabilizing elements chosen from W, Zr, Ti, Rh, Nb, Hf and Ta. The content of stabilizing element is less than or equal 2% by number of atoms.
Les barrières thermiques de la présente invention peuvent être des barrières multi-couches présentant une alternance de couches de matériaux bons conducteurs de la chaleur et de couches de matériaux mauvais conducteurs qui sont des alliages
quasi-cristallins. De telles structures constituent par exemple des barrières thermiques abradables.The thermal barriers of the present invention can be multi-layer barriers having an alternation of layers of materials which are good conductors of heat and layers of materials which are poor conductors which are alloys. almost crystalline. Such structures constitute, for example, abradable thermal barriers.
Pour les applications dans lesquelles les températures atteignent des valeurs supérieures à environ 600°C, les éléments de protection thermique de la présente invention peuvent être utilisés comme sous-couche d'accrochage pour une couche servant de barrière thermique et constituée par un maté¬ riau de l'art antérieur tel que la zircone. Dans ces domaines de température, les matériaux constituant les éléments de protection thermique de la présente invention deviennent super¬ plastiques. Ils correspondent donc bien aux conditions d'emploi requises pour la réalisation d'une sous-couche d'accrochage tout en étant capables de participer eux-mêmes à 1'isolation du substrat. Ainsi, les éléments de protection thermique de la présente invention peuvent être utilisés jusqu'à quelques dizaines de degrés du point de fusion du matériau qui les constitue. Cette limite se situe aux environs de 950°C à 1200°C selon la composition.For applications in which temperatures reach values greater than about 600 ° C., the thermal protection elements of the present invention can be used as a bonding undercoat for a layer serving as a thermal barrier and constituted by a material. of the prior art such as zirconia. In these temperature ranges, the materials constituting the thermal protection elements of the present invention become super¬ plastic. They therefore correspond well to the conditions of use required for the production of a bonding sub-layer while being capable of participating themselves in the isolation of the substrate. Thus, the thermal protection elements of the present invention can be used up to a few tens of degrees from the melting point of the material from which they are made. This limit is around 950 ° C to 1200 ° C depending on the composition.
Les alliages selon l'invention peuvent être obtenus par les procédés d'élaboration métallurgique classiques, c'est-à- dire qui comportent une phase de refroidissement lent (soit ΔT/t inférieur à quelques centaines de degrés) . Par exemple, des lingots peuvent être obtenus par fusion des éléments métal¬ liques séparés ou de préalliages dans un creuset en graphite brasqué sous une couverture de gaz protecteur (argon, azote) , de flux de couverture d'usage classique en métallurgie d'élabo¬ ration, ou dans un creuset maintenu sous vide. Il est possible aussi d'utiliser des creusets en céramique réfractaire ou en cuivre refroidi avec un chauffage par courant haute fréquence. La préparation des poudres nécessaires au procédé de métallisation peut s'effectuer par exemple par broyage méca¬ nique ou par ato isation de l'alliage liquide dans un jet d'ar¬ gon selon une technique classique. Les opérations d'élaboration de 1'alliage et d'atomisation peuvent s'effectuer en séquence sans requérir la coulée de lingots intermédiaires. Les alliages ainsi élaborés peuvent être déposés sous forme mince, générale¬ ment jusqu'à quelques dizaines de micromètres, mais également
sous forme épaisse, pouvant atteindre plusieurs millimètres, par toute technique de métallisation, dont celles qui ont déjà été citées.The alloys according to the invention can be obtained by conventional metallurgical production processes, that is to say which comprise a slow cooling phase (ie ΔT / t less than a few hundred degrees). For example, ingots can be obtained by melting separate metallic elements or pre-alloys in a graphite crucible brazed under a protective gas blanket (argon, nitrogen), a blanket flux used in conventional metallurgy ¬ ration, or in a crucible kept under vacuum. It is also possible to use refractory ceramic or copper crucibles cooled by high frequency current heating. The preparation of the powders necessary for the metallization process can be carried out for example by mechanical grinding or by ato isation of the liquid alloy in a jet of argon according to a conventional technique. The alloying and atomizing operations can be carried out in sequence without requiring the casting of intermediate ingots. The alloys thus produced can be deposited in thin form, generally up to a few tens of micrometers, but also in thick form, up to several millimeters, by any metallization technique, including those which have already been mentioned.
Les alliages de la présente invention peuvent être utilisés sous forme de revêtement superficiel par dépôt à partir d'un lingot pré-élaboré, ou de lingots des éléments séparés, pris comme cibles dans un réacteur de pulvérisation cathodique, ou encore par dépôt de phase vapeur produite" par la fusion sous vide du matériau massif. D'autres méthodes, par exemple celles qui mettent en oeuvre le frittage de poudre agglomérée, peuvent également être utilisées. Les revêtements peuvent également être obtenus par projection thermique, par exemple à l'aide d'un chalumeau oxy-gaz, d'un chalumeau super¬ sonique ou d'une torche à plasma. La technique de projection thermique est particulièrement intéressante pour l'élaboration d'éléments de protection thermique.The alloys of the present invention can be used in the form of a surface coating by deposition from a pre-prepared ingot, or of ingots of the separate elements, taken as targets in a sputtering reactor, or also by vapor phase deposition. produced " by vacuum melting of the solid material. Other methods, for example those which employ sintering of agglomerated powder, can also be used. The coatings can also be obtained by thermal spraying, for example using an oxy-gas torch, a super-sonic torch or a plasma torch The thermal spray technique is particularly interesting for the development of thermal protection elements.
La présente invention sera expliquée plus en détail par référence aux exemples non limitatifs suivants.The present invention will be explained in more detail with reference to the following nonlimiting examples.
Les alliages obtenus ont été caractérisés à l'état brut d'élaboration par leur diagramme de diffraction des rayons X avec une longueur d'onde λ = 0,17889 nm (anticathode de cobalt), complété lorsqu'il y a lieu par des diagrammes de diffraction d'électron enregistrés sur un microscope électro¬ nique Jeol 200 CX. Certains alliages ont été soumis à des maintiens en tempé¬ rature sous vide secondaire ou à l'air afin d'évaluer leur stabilité thermique et leur aptitude à résister à l'oxydation. La morphologie des phases et la taille de grain obtenues à l'état brut d'élaboration ont été analysées par micrographie optique à l'aide d'un microscope Olympus.The alloys obtained were characterized in the raw state by their X-ray diffraction diagram with a wavelength λ = 0.17889 nm (cobalt anticathode), supplemented when necessary by diagrams electron diffraction recorded on a Jeol 200 CX electron microscope. Some alloys have been subjected to temperature maintenance under secondary vacuum or in air in order to assess their thermal stability and their ability to resist oxidation. The morphology of the phases and the grain size obtained in the raw state of preparation were analyzed by optical micrography using an Olympus microscope.
La dureté des alliages a été déterminée à l'aide du duro- mètre WOLPERT V-Testor 2 sous charges de 30 et 400 grammes.The hardness of the alloys was determined using the WOLPERT V-Testor 2 durometer under loads of 30 and 400 grams.
Une estimation de la ductilité de certains alliages a été obtenue en mesurant la longueur des fissures formées à partir des angles de l'empreinte sous charge de 400 grammes. Une valeur moyenne de cette longueur, ainsi que de la dureté, a été évaluée à partir d'au moins 10 empreintes différentes réparties
sur l'échantillon. Une autre estimation de la ductilité repose sur l'amplitude de la déformation réalisée avant rupture lors d'un essai de compression appliqué à une eprouvette cylindrique de 4,8 mm de diamètre et 10 mm de hauteur usinée avec des faces parfaitement parallèles perpendiculairement à l'axe du cylindre. Une machine de traction/compression de marque INSTROM a été employée.An estimate of the ductility of certain alloys was obtained by measuring the length of the cracks formed from the angles of the cavity under load of 400 grams. An average value of this length, as well as the hardness, was evaluated from at least 10 different fingerprints distributed on the sample. Another estimate of the ductility is based on the amplitude of the deformation produced before rupture during a compression test applied to a cylindrical specimen of 4.8 mm in diameter and 10 mm in height machined with perfectly parallel faces perpendicular to the cylinder axis. An INSTROM brand traction / compression machine was used.
Enfin, le coefficient de frottement d'une bille eh acier 100C6 sur un substrat revêtu d'un alliage de "la présente invention a été mesuré à l'aide d'un testeur tribologique de type pion/disque et de marque CSEM.Finally, the coefficient of friction of a 100C6 steel ball on a substrate coated with an alloy of "the present invention was measured using a tribological tester of the pion / disc type and brand CSEM.
La résistivité électrique des échantillons a été mesurée à la température ambiante sur des éprouvettes cylindriques de 20 mm de longueur et de 4,8 mm de diamètre. La méthode classique dite en 4 points a été utilisée, avec un courant de mesure constant de 10 A. La tension aux bornes des électrodes inté¬ rieures a été mesurée avec un nanovoltmètre de grande préci¬ sion. Une mesure a été effectuée en fonction de la température à l'aide d'un four spécifiquement adapté. Les températures de fusion de quelques alliages ont été déterminées au chauffage avec une vitesse de 5°C/mn par Analyse Thermique Différentielle sur un appareil SETARAM 2000C.The electrical resistivity of the samples was measured at room temperature on cylindrical specimens 20 mm long and 4.8 mm in diameter. The conventional method known as 4 points was used, with a constant measuring current of 10 A. The voltage across the internal electrodes was measured with a high precision nanovoltmeter. A measurement was made as a function of the temperature using a specifically adapted oven. The melting temperatures of some alloys were determined on heating with a speed of 5 ° C / min by Differential Thermal Analysis on a SETARAM 2000C device.
La structure cristallographique des alliages a été définie par analyse de leur diagramme de diffraction des rayons X et de leurs diagrammes de diffraction des électrons.The crystallographic structure of the alloys was defined by analysis of their X-ray diffraction diagram and their electron diffraction diagrams.
Exemple 1 Elaboration des alliages quasicristallins Une série d'alliages a été élaborée par fusion des éléments purs dans un champ haute fréquence sous atmosphère d'argon dans un creuset en cuivre refroidi. La masse totale ainsi élaborée était comprise entre 50 g et 100 g d'alliage. La température de fusion, qui dépend de la composition de l'al¬ liage, a toujours été trouvée dans l'intervalle de température situé entre 950 et 1200aC. Pendant le maintien en fusion de l'alliage, une eprouvette cylindrique pleine de 10 mm +0,5 mm de diamètre et de quelques centimètres de hauteur a été formée par aspiration du métal liquide dans un tube de quartz. La
vitesse de refroidissement de cet échantillon était voisine de 250°C par seconde. Cet échantillon a été ensuite découpé avec une scie diamantée pour façonner les éprouvettes de métallo- graphie et de dureté utilisées dans les exemples ci-après. Une partie de l'eprouvette a été fragmentée pour les essais de stabilité thermique et une fraction broyée en poudre pour l'analyse par diffraction des rayons X de chaque alliage. Un montage analogue a été utilisé pour obtenir les échantillons cylindriques de 4,8 mm de diamètre destinés à la résistivité électrique. La vitesse de refroidissement de l'eprouvette était alors proche de 1000°C par seconde.Example 1 Development of Quasicrystalline Alloys A series of alloys was produced by melting pure elements in a high frequency field under an argon atmosphere in a cooled copper crucible. The total mass thus produced was between 50 g and 100 g of alloy. The melting temperature, which depends on the composition of the alloy, has always been found in the temperature range between 950 and 1200 a C. During the maintenance of fusion of the alloy, a cylindrical test tube full of 10 mm + 0.5 mm in diameter and a few centimeters in height was formed by aspiration of the molten metal in a quartz tube. The the cooling rate of this sample was close to 250 ° C per second. This sample was then cut with a diamond saw to shape the metallography and hardness specimens used in the examples below. Part of the test piece was fragmented for thermal stability tests and a crushed powder fraction for X-ray diffraction analysis of each alloy. A similar assembly was used to obtain the 4.8 mm diameter cylindrical samples intended for electrical resistivity. The cooling rate of the specimen was then close to 1000 ° C per second.
Le tableau 1 ci-dessous donne la teneur en phase quasi- cristalline des alliages selon l'invention obtenus, ainsi que la température de fusion de certains d'entre eux. Les diagrammes de diffraction des rayons X et les diagrammes de diffraction électronique ont été enregistrés pour les alliages quasicristallins cités dans le tableau 1. Leur étude a permis de déterminer la nature cristallographique des phases présentes. C'est ainsi que, par exemple, les alliages n° 2, 5, 7, 8, 9, 19, 22 présentent majoritairement la phase O*. et l'alliage 1 ma oritairement la phase C. L'alliage 3 contient majoritairement de la phase H. L'alliage 6 est constitué essen¬ tiellement par la phase H, ainsi que d'une faible fraction de phase C. Les autres alliages contiennent des proportions variables de phases C, 0*ι, O3, O4 (et H pour 23).Table 1 below gives the quasicrystalline phase content of the alloys according to the invention obtained, as well as the melting temperature of some of them. The X-ray diffraction patterns and the electron diffraction patterns were recorded for the quasicrystalline alloys listed in Table 1. Their study made it possible to determine the crystallographic nature of the phases present. This is how, for example, alloys 2, 5, 7, 8, 9, 19, 22 mainly have the O * phase. and the alloy 1 ma mainly phase C. The alloy 3 mainly contains phase H. The alloy 6 consists essentially of phase H, as well as a small fraction of phase C. The other alloys contain varying proportions of phases C, 0 * ι, O 3 , O4 (and H for 23).
TABLEAU 1TABLE 1
TABLEAU 1 ( suite)TABLE 1 (continued)
Un bain de cent (100) kilogrammes d'un alliage produisant une fraction en masse de plus de 95% de phase quasicristalline a été élaboré. La composition nominale de l'alliage était Al67Cu9f5Fei2Cr*n(5 en nombre d'atomes (alliage 39). Cette composi-
tion a été réalisée à partir de composants métalliques indus¬ triels, à savoir de l'aluminium A5, un alliage Cu-Al-Fe conte¬ nant 19,5% Al en poids, 58,5% Cu en poids et 21,5% Fe en poids. Ces éléments et alliages ont été introduits à froid dans un creuset en graphite brasqué à l'alumine. Leur fusion a été réalisée sous un flux de couverture qui a été maintenu jusqu'à la fin de l'opération. Un générateur de courant haute fréquence de 125 k a été utilisé. Après fusion de cette charge et homo¬ généisation de sa température à 1140"C, du fer pur en barreaux de 8 mm de diamètre puis des briquettes Al-Cr contenant 74% en poids de Chrome et 14% en poids de fondant ont été ajoutés pour atteindre la composition nominale de l'alliage. Après homogé¬ néisation, il a été procédé à la coulée en lingotières de 2 kg de la totalité de la fusion. Deux prélèvements, respectivement au milieu de la coulée et à la fin ont été analysés par voie humide et ont donné deux compositions très voisines de Al66,8CU9,4Fei2,2Crιι#5 no,ι en nombre d'atomes. Le taux d'impuretés, carbone et soufre, a été trouvé inférieur à 0,1% at. L'examen par diffraction des rayons X de plusieurs prélèvements de lingots, réduits en poudre, montre des diagrammes de diffrac¬ tion correspondant à une phase O*-, approximante de la phase décagonale vraie.A bath of one hundred (100) kilograms of an alloy producing a mass fraction of more than 95% of quasicrystalline phase has been developed. The nominal composition of the alloy was Al 6 7Cu9 f 5Fei 2 Cr * n ( 5 in number of atoms (alloy 39). tion was made from industrial metallic components, namely aluminum A5, a Cu-Al-Fe alloy containing 19.5% Al by weight, 58.5% Cu by weight and 21.5 % Fe by weight. These elements and alloys were introduced cold into a graphite crucible brazed with alumina. Their merger was carried out under a hedging flow which was maintained until the end of the operation. A high frequency generator of 125 k was used. After fusion of this charge and homogenization of its temperature at 1140 "C, pure iron in bars of 8 mm in diameter then Al-Cr briquettes containing 74% by weight of Chromium and 14% by weight of flux to reach the nominal composition of the alloy. After homogenization, casting was carried out in ingot molds of 2 kg of the entire melt. Two samples, respectively in the middle of the casting and at the end, were analyzed. wet and gave two very similar compositions of Al66,8CU9,4Fei2,2Crιι # 5 no, ι in number of atoms.The rate of impurities, carbon and sulfur, was found less than 0.1% at. The X-ray diffraction examination of several ingots of samples, reduced to powder, shows diffraction diagrams corresponding to an O * - phase, approximating the true decagonal phase.
La chaleur spécifique de l'alliage a été déterminée dans la plage de températures 20-80"C avec un calorimètre à balayage SETARAM. La diffusivité thermique d'une pastille de cet alliage de 15 mm d'épaisseur et 32 mm de diamètre a été déduite de la courbe température/temps mesurée sur une face de la pastille sachant que la face opposée, préalablement noircie, a été irra¬ diée par un éclair laser de puissance et de forme calibrées. La conductivité thermique est déduite des deux précédentes mesures, connaissant la masse spécifique de l'alliage qui a été mesurée par la méthode d'Archimède par immersion dans du phta- late de butyle maintenu à 30"C (+ 0,1°C) et trouvée égale à 4,02 g/cm3.
Exemple 3 ComparatifThe specific heat of the alloy was determined in the temperature range 20-80 "C with a SETARAM scanning calorimeter. The thermal diffusivity of a pellet of this alloy 15 mm thick and 32 mm in diameter was deduced from the temperature / time curve measured on one face of the patch, knowing that the opposite face, previously blackened, was irradiated by a laser flash of calibrated power and shape. The thermal conductivity is deduced from the two previous measurements, knowing the specific gravity of the alloy which has been measured by the Archimedes method by immersion in butyl phthalate maintained at 30 "C (+ 0.1 ° C) and found equal to 4.02 g / cm 3 . Comparative Example 3
Elaboration d'alliages de l'art antérieur A titre de comparaison, une série d'alliages connus de l'art antérieur a été élaborée selon le procédé de l'exemple 1. Ces compositions sont rassemblées dans le tableau 2 ci-dessous. Les alliages contenaient au plus 30% en masse de phase quasi¬ cristalline, à l'exception de celui dont la teneur atomique en cuivre était supérieure à 18 %.Elaboration of alloys of the prior art By way of comparison, a series of alloys known from the prior art was prepared according to the method of example 1. These compositions are collated in table 2 below. The alloys contained at most 30% by mass of quasi-crystalline phase, with the exception of that whose atomic copper content was greater than 18%.
TABLEAU 2TABLE 2
Exemple 4Example 4
Stabilité thermique La stabilité thermique de quelques alliages de la présente invention a été évaluée. Les alliages sélectionnés ont été soumis à des maintiens à différentes températures pendant des durées allant de quelques heures à plusieurs dizaines d'heures. Des fragments extraits par cassure des lingots élaborés selon l'exemple 1 ont été placés dans des ampoules de quartz scellées sous vide secondaire. Le volume de ces fragments était de l'ordre de 0,25 cm3. Les ampoules ont été placées dans un four préalablement chauffé à la température du traitement. A la fin du traitement, elles ont été refroidies sous vide jusqu'à la température ambiante par convection naturelle dans l'air ou à une vitesse contrôlée. Les fragments ont ensuite été broyés pour examen par diffraction des rayons X. Des examens par diffraction des électrons ont également été effectués. Les
conditions expérimentales des traitements thermiques sont résu¬ mées dans le tableau 3 ci-dessous.Thermal stability The thermal stability of some alloys of the present invention has been evaluated. The selected alloys were subjected to maintenance at different temperatures for periods ranging from a few hours to several tens of hours. Fragments extracted by breaking the ingots prepared according to Example 1 were placed in quartz ampoules sealed under secondary vacuum. The volume of these fragments was of the order of 0.25 cm 3 . The ampoules were placed in an oven previously heated to the treatment temperature. At the end of the treatment, they were cooled under vacuum to ambient temperature by natural convection in air or at a controlled speed. The fragments were then ground for X-ray diffraction examination. Electron diffraction examinations were also carried out. The experimental conditions of the heat treatments are summarized in table 3 below.
TABLEAU 3TABLE 3
L'évolution structurale des alliages en cours de traite¬ ment isotherme du présent exemple a été appréciée par compa¬ raison avec les diagrammes de diffraction des rayons X enregis- très respectivement avant et après le traitement thermique. Il est remarquable de constater que ces diagrammes ne présentent pas de modification majeure ni dans le nombre de raies de diffraction ni dans leurs intensités relatives. On remarque toutefois un affinement des raies de diffraction qui est dû au phénomène bien connu du grossissement de grain à haute tempéra¬ ture.The structural development of the alloys during isothermal treatment of the present example was assessed by comparison with the X-ray diffraction diagrams recorded very before and after the heat treatment respectively. It is remarkable to note that these diagrams do not present any major modification neither in the number of diffraction lines nor in their relative intensities. However, there is a refinement of the diffraction lines which is due to the well-known phenomenon of grain enlargement at high temperature.
Les alliages de la présente invention sont stables thermi- quement en ce sens que leur structure, telle qu'elle est carac¬ térisée par les figures de diffraction appropriées, n'évolue pas de façon essentielle au cours de traitements thermiques isothermes à des températures pouvant atteindre la température de fusion des alliages. En d'autres termes, la fraction massique de phase quasicristalline présente à l'état brut d'élaboration ne diminue pas au cours de maintiens en tempéra- ture.The alloys of the present invention are thermally stable in the sense that their structure, as it is charac¬ terized by the appropriate diffraction figures, does not change essentially during isothermal heat treatments at temperatures which can reach the melting temperature of the alloys. In other words, the mass fraction of quasicrystalline phase present in the raw state of production does not decrease during temperature maintenance.
Exemple 5 Résistance à l'oxydation Des échantillons en fragments identiques à ceux décrits dans l'exemple 4 ont été soumis à des traitements thermiques
dans un four ouvert à l'air, dans des conditions résumées dans le tableau 4 ci-dessous.Example 5 Oxidation resistance Samples in fragments identical to those described in Example 4 were subjected to heat treatments in an oven open to air, under conditions summarized in Table 4 below.
TABLEAU 4TABLE 4
La comparaison entre les diagrammes de diffraction des échan¬ tillons avant traitement et ceux enregistrés à la fin des trai¬ tements thermiques à l'air montre que les échantillons n'ont subi aucune altération. Plus précisément, aucune trace de gros- sissement de grain n'est décelable à partir des largeurs de raies de diffraction qui sont restées identiques à celles des diagrammes caractéristiques de 1'état brut d'élaboration'.The comparison between the diffraction diagrams of the samples before treatment and those recorded at the end of the thermal air treatments shows that the samples have not undergone any alteration. Specifically, no trace of grain wholesale- quenched, is detectable from the diffraction line widths that remain identical to those of crude 1'état characteristics diagrams development.
Exemple 6 Morphologie et taille de grain Les alliages de la présente invention, élaborés selon la méthode de l'exemple 1, sont des matériaux polycristallins dont la morphologie a été étudiée par microscopie optique selon une technique de métallographie classique. Pour cela, les pastilles de 10 mm de diamètre (élaborées selon la méthode de l'exemple 1) ont été finement polies puis attaquées par un réactif métal- lographique approprié. Les images métallographiques ont été photographiées avec un microscope optique Olympus, travaillant en lumière blanche. La taille de grain observée est comprise entre quelques micromètres et quelques dizaines de micromètres. La même méthode de caractérisation a été appliquée aux échantillons traités à 1'air dans le domaine de température 400"C à 500°C comme décrit dans le tableau 4 de l'exemple pré-
cèdent. Sur les images métallographiques ainsi obtenues, on a constaté que les alliages n'ont pas subi de grossissement de grain à la fin de ces traitements thermiques. Il en résulte que la morphologie polycristalline de ces matériaux, qui détermine de nombreuses propriétés thermomécaniques, notamment la dureté macroscopique (H4oo) , les coefficients de frottement, la limite élastique, la résilience, n'est pas sensible à des maintiens en température pouvant atteindre au moins 500"C pendant au moins plusieurs dizaines d'heures, y compris en présence d'air. Exemple 7Example 6 Morphology and Grain Size The alloys of the present invention, produced according to the method of Example 1, are polycrystalline materials whose morphology has been studied by optical microscopy according to a conventional metallography technique. For this, the 10 mm diameter pellets (produced according to the method of Example 1) were finely polished and then attacked with an appropriate metallographic reagent. The metallographic images were photographed with an Olympus optical microscope, working in white light. The grain size observed is between a few micrometers and a few tens of micrometers. The same characterization method was applied to the samples treated with air in the temperature range 400 "C to 500 ° C as described in Table 4 of the example above. give in. On the metallographic images thus obtained, it has been found that the alloys have not undergone grain enlargement at the end of these heat treatments. It follows that the polycrystalline morphology of these materials, which determines many thermomechanical properties, in particular the macroscopic hardness (H 4 oo), the coefficients of friction, the elastic limit, the resilience, is not sensitive to temperature maintenance can reach at least 500 "C for at least several tens of hours, including in the presence of air. Example 7
Dureté et ductilité à la température ambiante Les duretés Vickers des alliages de la présente invention et de certains alliages de l'art antérieur ont été mesurées à la température ambiante sur des fragments d'alliages élaborés selon le procédé de l'exemple 1, enrobés dans une résine pour usage métallographique, puis finement polis. Deux charges du microduromètre, respectivement de 30g et 400g, ont été employées. Les résultats sont donnés dans le tableau 5 ci- dessous. Les duretés Vickers observées pour les alliages de la présente invention sont particulièrement élevées par compa¬ raison avec les duretés Vickers sous charge de 400 grammes relevées pour les alliages de l'art antérieur élaborés comme dans l'exemple 3 (échantillon 41 à 46). La présence de cobalt dans les alliages de la présente invention accroît singulièrement les duretés observées puisque certaines valeurs dépassent HV00 = 800.Hardness and ductility at room temperature The Vickers hardnesses of the alloys of the present invention and of certain alloys of the prior art were measured at room temperature on fragments of alloys produced according to the method of Example 1, coated in a resin for metallographic use, then finely polished. Two loads of the microdurometer, respectively 30g and 400g, were used. The results are given in Table 5 below. The Vickers hardnesses observed for the alloys of the present invention are particularly high in comparison with the Vickers hardnesses under load of 400 grams recorded for the alloys of the prior art prepared as in Example 3 (sample 41 to 46). The presence of cobalt in the alloys of the present invention considerably increases the hardness observed since certain values exceed HV00 = 800.
En général, la ductilité des alliages présentant une dureté élevée est relativement faible. Toutefois, on constate de façon surprenante que les alliages de la présente invention contenant du cobalt présente une ductilité plus élevée. Pour les alliages de la présente invention ne contenant pas de cobalt, il est possible d'améliorer la ductilité grâce à des additions, par exemple de bore ou de carbone. Pour évaluer simplement l'effet de telles additions sur la ductilité de certains alliages, la longueur moyenne des fissures qui se forment à partir des angles des empreintes Vickers sous charge
2 D de 400 grammes a été mesurée. Cette longueur est d'autant plus faible que l'alliage est plus ductile. Quelques résultats sont reportés dans le tableau 5.In general, the ductility of alloys with high hardness is relatively low. However, it is surprisingly found that the alloys of the present invention containing cobalt have a higher ductility. For the alloys of the present invention not containing cobalt, it is possible to improve the ductility by means of additions, for example of boron or carbon. To simply assess the effect of such additions on the ductility of certain alloys, the average length of the cracks that form from the angles of the Vickers cavities under load 2 D of 400 grams was measured. The shorter the length, the more ductile the alloy. Some results are reported in Table 5.
TABLEAU 5TABLE 5
En outre, un essai de compression a été réalisé avec l'alliage 2 de l'exemple 1, qui ne contient pas de bore, et l'alliage 19, modifié par addition de 3,3% atomique de bore. L'essai a été conduit à la température ambiante, sous charge croissante, sur des éprouvettes cylindriques de diamètre 4,8 mm et de 10 mm de hauteur. Les faces du cylindre, sur lesquelles s'applique la charge ont été très soigneusement usinées de
sorte à être parfaitement parallèles entre elles et perpendicu¬ laires à l'axe du cylindre. D'après les courbes déformation - contrainte de compression qui ont été enregistrées en cours de déformation d'éprouvettes des alliages 2 et 19 (tels qu'éla- bores selon la méthode de l'exemple 1), on a constaté que l'addition du bore double la déformation obtenue à la rupture, qui atteint 2% environ, et la limite à la rupture, qui dépasse 1000 MPa.In addition, a compression test was carried out with alloy 2 of Example 1, which does not contain boron, and alloy 19, modified by adding 3.3 atomic% of boron. The test was carried out at ambient temperature, under increasing load, on cylindrical specimens with a diameter of 4.8 mm and 10 mm in height. The faces of the cylinder, on which the load is applied, have been very carefully machined from so as to be perfectly parallel to each other and perpendicular to the axis of the cylinder. From the deformation - compressive stress curves which were recorded during the deformation of test specimens of alloys 2 and 19 (such as elaborates according to the method of example 1), it was found that the addition boron doubles the deformation obtained at break, which reaches about 2%, and the limit at break, which exceeds 1000 MPa.
Exemple 8 Résistivité électrique à la température ambianteEXAMPLE 8 Electrical Resistivity at Room Temperature
Des mesures de résistivité ont été effectuées pour des alliages selon l'invention, et, à titre comparatif, pour des compositions de l'art antérieur. 'Dans tous les cas, des éprou¬ vettes cylindriques préparées selon le mode opératoire de l'exemple 1 ont été utilisées.Resistivity measurements were carried out for alloys according to the invention, and, for comparison, for compositions of the prior art. In all cases, cylindrical test pieces prepared according to the procedure of Example 1 were used.
Les résultats obtenus sont rassemblés dans le tableau 6 ci-dessous.The results obtained are collated in Table 6 below.
Les compositions 41 à 46 et 40 sont des alliages de l'art antérieur, les autres sont des alliages selon l'invention. Les compositions de l'art antérieur présentent une résis¬ tivité électrique à la température ambiante qui est comprise entre quelques μΩ cm et quelques dizaines de μΩ cm. On note toutefois une exception avec l'alliage 42 de composition AlβsCris en nombre d'atomes qui possède une résistivité de 300 μΩ cm. Cette valeur est à rapprocher de la présence d'un taux de phase quasicristalline assez proche, quoique inférieur, de 30% en masse. Cet état est cependant métastable et n'a été réalisé que grâce à la vitesse de refroidissement élevée qui caractérise le mode d'élaboration des présentes éprouvettes.
TABLEAU 6The compositions 41 to 46 and 40 are alloys of the prior art, the others are alloys according to the invention. The compositions of the prior art have an electrical resistivity at room temperature which is between a few μΩ cm and a few tens of μΩ cm. There is, however, an exception with the alloy 42 of composition AlβsCris in number of atoms which has a resistivity of 300 μΩ cm. This value is to be compared with the presence of a rate of quasicrystalline phase fairly close, although lower, of 30% by mass. This state is however metastable and has only been achieved thanks to the high cooling rate which characterizes the method of preparation of the present test pieces. TABLE 6
Les valeurs caractéristiques de la résistivité électrique des alliages de la présente invention sont comprises entre 300 et 600 μΩ cm. Des valeurs aussi élevées destinent les alliages quasicristallins de la présente invention à toute application où cette propriété doit être mise à profit, comme par exemple le chauffage par effet Joule, les résistances à forte dissipa- tion calorique, le couplage électromagnétique, éventuellement haute fréquence.The characteristic values of the electrical resistivity of the alloys of the present invention are between 300 and 600 μΩ cm. Such high values mean the quasicrystalline alloys of the present invention for any application where this property must be taken advantage of, such as, for example, Joule heating, resistors with high heat dissipation, electromagnetic coupling, possibly high frequency.
De plus, un alliage représentatif de la famille (III) possède un faible coefficient de température de la résistivité électrique (1/p dp/dT) . On a mesuré la variation relative de la résistivité électrique avec la température d'une eprouvette de l'alliage 2. Cette eprouvette a été préparée à partir d'un ruban de 0,1 mm d'épaisseur et de 1,2 mm de largeur élaboré par trempe de l'alliage liquide sur un tambour de cuivre dont la surface défilait à une vitesse de 12 m/s (technique, dite du melt spinning) . Le lingot porté à l'état liquide avait été élaboré selon la méthode de 1'exemple 1. L'eprouvette a été chauffée à vitesse constante de 5°C/mn et maintenue en contact avec quatre fils de platine selon la méthode de mesure dite en
quatre points. L'écart entre électrodes de potentiel était de 20 mm et la mesure de potentiel effectuée avec un nanovoltmètre de précision. Un courant constant de 10 A circulait dans 1'eprouvette au travers des deux autres électrodes. Le disposi- tif de mesure a été maintenu sous flux d'argon protecteur dans un four approprié. On a constaté que la variation de résistance est linéaire, ce qui démontre qu'aucune transformation de l'échantillon n'intervient durant la mesure ni durant le cycle de chauffage suivant, en confirmation de la grande stabilité thermique des alliages (exemple 4) . Le coefficient de tempéra¬ ture déduit de la courbe (l/ρ(20°C) ) (p(T) -p(20°C) ) / ΔT est de -3.10-***. Cette valeur faible distingue l'alliage pour les applications où il est préférable de conserver les caractéris¬ tiques du matériau à l'intérieur d'une fourchette étroite en fonction de la température, comme par exemple le chauffage par induction électromagnétique.In addition, an alloy representative of the family (III) has a low temperature coefficient of electrical resistivity (1 / p dp / dT). The relative variation of the electrical resistivity with the temperature of a test tube of alloy 2 was measured. This test tube was prepared from a tape 0.1 mm thick and 1.2 mm wide. produced by quenching the liquid alloy on a copper drum, the surface of which scrolled at a speed of 12 m / s (technique, known as melt spinning). The ingot brought to the liquid state had been prepared according to the method of example 1. The test piece was heated at a constant speed of 5 ° C./minute and kept in contact with four platinum wires according to the so-called measurement method. in four points. The difference between potential electrodes was 20 mm and the potential measurement carried out with a precision nanovoltmeter. A constant current of 10 A flowed through the test tube through the other two electrodes. The measuring device was kept under a protective argon flow in a suitable oven. It was found that the variation in resistance is linear, which demonstrates that no transformation of the sample takes place during the measurement or during the following heating cycle, in confirmation of the great thermal stability of the alloys (example 4). The temperature coefficient deduced from the curve (l / ρ (20 ° C)) (p (T) -p (20 ° C)) / ΔT is -3.10 - ***. This low value distinguishes the alloy for applications where it is preferable to keep the characteristics of the material within a narrow range as a function of the temperature, such as for example heating by electromagnetic induction.
Exemple 9 Résistance à la corrosion La dissolution de certains alliages de la présente inven- tion dans différents milieux a été mesurée ainsi que celle d'un alliage de l'art antérieur.Example 9 Corrosion resistance The dissolution of certain alloys of the present invention in different media was measured as well as that of an alloy of the prior art.
Les échantillons testés sont :The samples tested are:
- alliage n° 40 de l'art antérieur à 18,5 % de Cu- alloy No. 40 of the prior art with 18.5% Cu
- alliage n° 2 de l'invention à 9 % de Cu - alliage n° 3 de l'invention à 10 % de Co, 0 % de Cu- alloy 2 of the invention with 9% Cu - alloy 3 of the invention with 10% Co, 0% Cu
- alliage n° 6 de l'invention à 18 % de Co, 0 % de Cu.- alloy No. 6 of the invention with 18% Co, 0% Cu.
Pour mesurer le taux de dissolution, une eprouvette de 10 mm de diamètre et 3 mm d'épaisseur, élaborée selon le mode opératoire de l'exemple 1, a été immergée pendant 30 h dans une solution corrosive, à différentes températures. La solution a été agitée pendant toute la durée de 1 ' immersion et maintenue à température par un bain thermostaté. Après 30 heures, on a déterminé la perte de poids de chaque eprouvette.To measure the dissolution rate, a test tube 10 mm in diameter and 3 mm thick, prepared according to the procedure of Example 1, was immersed for 30 h in a corrosive solution, at different temperatures. The solution was stirred for the duration of the immersion and kept at temperature by a thermostatically controlled bath. After 30 hours, the weight loss of each test piece was determined.
Les résultats sont rassemblés dans le tableau 7 ci- dessous. Les grandeurs données représentent la perte de poids de l'échantillon en gm-2h"i. N.D. signifie "non détecté".
TABLEAU 7The results are collated in Table 7 below. The quantities given represent the weight loss of the sample in gm-2h "i. ND means" not detected ". TABLE 7
Il est bien connu que l'addition de cuivre diminue la résistance à la corrosion des alliages d'aluminium (chap.7 de Aluminium, Vol.I, d. K.R. Van Horn, American Society for Metals) . En milieu acide dilué, par exemple, les alliages d'aluminium présentent un taux de dissolution élevé qui diminue habituellement avec l'augmentation de la teneur en acide. A proximité de la concentration 100% d'acide, ce taux de dissolu¬ tion augmente à nouveau très fortement. A l'inverse, du côté alcalin, la tenue des alliages d'aluminium est satisfaisante jusqu'à ce que le pH s'élève au-dessus de pH=12. Le film passi- vant d'alumine qui les protège peut alors passer en solution et les alliages d'aluminium sont habituellement très peu résis¬ tants à la corrosion en milieu fortement alcalin.It is well known that the addition of copper decreases the corrosion resistance of aluminum alloys (chapter 7 of Aluminum, Vol.I, d. K.R. Van Horn, American Society for Metals). In dilute acidic medium, for example, aluminum alloys have a high dissolution rate which usually decreases with increasing acid content. Close to the 100% acid concentration, this dissolving rate again increases very sharply. Conversely, on the alkaline side, the behavior of the aluminum alloys is satisfactory until the pH rises above pH = 12. The passivating alumina film which protects them can then go into solution and the aluminum alloys are usually very little resistant to corrosion in a strongly alkaline medium.
Les essais ci-dessus montrent que la présente invention fournit des alliages qui présentent une excellente résistance à la corrosion en milieu acide (n° 2, ayant une teneur en Cu supérieure à 5% atomique) , ou en milieu fortement alcalin (n° 3 et 6, ayant une teneur en cobalt supérieure à 5% atomique).The above tests show that the present invention provides alloys which have excellent corrosion resistance in an acid medium (No. 2, having a Cu content greater than 5 atomic%), or in a strongly alkaline medium (No. 3 and 6, having a cobalt content greater than 5 atomic%).
Ainsi, les alliages quasicristallins de la présente inven¬ tion réunissent plusieurs propriétés qui les désignent tout particulièrement pour de nombreuses applications à l'état de revêtements superficiels : grande dureté, ductilité faible mais non négligeable, stabilité thermique, forte résistance à la corrosion. L'exemple suivant montrera que ces alliages conser¬ vent ces propriétés après leur mise en oeuvre comme revêtement superficiel. Ils présentent alors un coefficient de frottement
remarquablement faible qui enrichit la palette des propriétés intéressantes déjà mentionnées.Thus, the quasicrystalline alloys of the present invention combine several properties which designate them very particularly for many applications in the form of surface coatings: high hardness, low but not negligible ductility, thermal stability, high resistance to corrosion. The following example will show that these alloys retain these properties after they have been used as a surface coating. They then have a coefficient of friction remarkably weak which enriches the range of interesting properties already mentioned.
Exemple 10 Mise en oeuyre d'un alliage de la présente invention pour la réalisation d'un dépôt superficielExample 10 Use of an Alloy of the Present Invention for the Production of a Surface Deposit
Un lingot de deux kilogrammes de l'alliage élaboré selon l'exemple 2 a été réduit en poudre par broyage à l'aide d'un broyeur à galets concentriques en acier carburé. La" poudre ainsi obtenue a été tamisée de sorte à ne retenir que la frac- tion de grains dont la taille était comprise entre 25 μm au minimum et 80 μm au maximum. Un dépôt de 0,5 mm d'épaisseur a alors été réalisé par projection de cette poudre sur une plaque en acier doux préalablement sablée. Cette projection s'est effectuée par l'intermédiaire d'un chalumeau à flamme Metco alimenté par un mélange dosé à 63% d'hydrogène et 27% d'oxy¬ gène. L'opération s'est déroulée sous atmosphère protectrice d'azote hydrogéné à 30% de façon à prévenir toute oxydation de l'échantillon. Après élimination de la rugosité superficielle par polissage mécanique, un examen par diffraction des rayons X a révélé que l'alliage déposé était constitué d'au moins 95% de phase icosaédrique. L'eprouvette, constituée du substrat en acier muni de son revêtement quasicristallin, a été ensuite divisée en deux parties par tronçonnage et l'une de ces parties a été soumise à un traitement thermique à 500°C sous air comme indiqué dans l'exemple 4. Une étude du diagramme de diffrac¬ tion des rayons X effectué sur l'échantillon traité ne révèle aucune modification majeure de la structure après 28 heures de maintien et confirme la très forte stabilité thermique de l'alliage, y compris à la suite de l'opération de métallisation de surface. Le tableau 8 ci-après résume les résultats des mesures de dureté effectuées, comme dans l'exemple 7, avant et après traitement thermique. La valeur mesurée sur le lingot avant réduction en poudre est également donnée.
TABLEAU 8An ingot of two kilograms of the alloy produced according to Example 2 was reduced to powder by grinding using a mill with carbide steel concentric rollers. The " powder thus obtained was sieved so as to retain only the fraction of grains whose size was between 25 μm minimum and 80 μm maximum. A deposit of 0.5 mm thick was then produced by spraying this powder onto a mild steel plate previously sandblasted. This spraying was carried out by means of a Metco flame torch fed by a mixture dosed with 63% hydrogen and 27% oxygen. The operation was carried out under a protective atmosphere of 30% hydrogenated nitrogen so as to prevent any oxidation of the sample After removal of the surface roughness by mechanical polishing, an examination by X-ray diffraction revealed that the alloy deposited consisted of at least 95% icosahedral phase. The specimen, consisting of the steel substrate provided with its quasicrystalline coating, was then divided into two parts by cutting and one of these parts was subjected to a heat treatment at 500 ° C. in air as indicated in example 4. A study of the X-ray diffraction diagram carried out on the treated sample does not reveal any major modification of the structure after 28 hours of maintenance and confirms the very high thermal stability of the alloy, including following the surface metallization operation. Table 8 below summarizes the results of the hardness measurements carried out, as in Example 7, before and after heat treatment. The value measured on the ingot before reduction to powder is also given. TABLE 8
En outre, le coefficient de frottement d'une bille Brinell, en acier à outils 100C6, sur le dépôt du présent exemple, a été mesuré à l'aide d'un testeur tribologique du type pion-disque de marque CSEM. Une force normale Fn — 5N a été appliquée sur le frotteur normalement au plan du dépôt. La force de résistance au déplacement du frotteur Ft (N) , mesurée (en newtons) tangentiellement au déplacement, donne le coeffi¬ cient de frottement μ = Ft (N) / Fn, sous force normale constante, qui est reporté dans le tableau 8. Il est à noter que les valeurs du tableau 8 sont comparables, voire sensible¬ ment meilleures que les valeurs retenues pour d'autres maté- riaux employés dans les applications tribologiques.In addition, the coefficient of friction of a Brinell ball, made of tool steel 100C6, on the deposit of this example, was measured using a tribological tester of the pin-disc type of CSEM brand. A normal force F n - 5N was applied to the wiper normally at the plane of the deposit. The force of resistance to displacement of the wiper F t (N), measured (in newtons) tangentially to the displacement, gives the coefficient of friction μ = F t (N) / F n , under constant normal force, which is reported in Table 8. It should be noted that the values in Table 8 are comparable, or even significantly better than the values used for other materials used in tribological applications.
Exemple 11 Diffusivité thermigue à température ambiante. La diffusivité thermique , la masse spécifique d et la chaleur spécifique Cp ont été déterminées au voisinage de la température ambiante pour plusieurs échantillons préparés selon 1'exemple 1 et un échantillon préparé selon 1 'exemple 2. Les échantillons élaborés selon la méthode de 1 'exemple 1 sont des pastilles de 10 mm de diamètre et de 3 mm d'épaisseur. L'échan¬ tillon de l'exemple 2 est une pastille de 32 mm de diamètre et de 15 mm d'épaisseur.Example 11 Thermal diffusivity at room temperature. The thermal diffusivity, the specific mass d and the specific heat Cp were determined in the vicinity of room temperature for several samples prepared according to Example 1 and one sample prepared according to Example 2. The samples prepared according to the method of 1 ' Example 1 are pellets 10 mm in diameter and 3 mm thick. The sample of Example 2 is a pellet 32 mm in diameter and 15 mm thick.
Les faces opposées de chaque pastille ont été polies méca¬ niquement sous eau en prenant un grand soin à garantir leur parallélisme. L'état structural des éprouvettes a été déterminé par diffraction des rayons X et par microscopie électronique. Tous les échantillons sélectionnés contenaient au moins 90% en
volume de phase quasicristalline selon la définition donnée ci- dessus.The opposite faces of each pellet have been polished mechanically under water, taking great care to guarantee their parallelism. The structural state of the test pieces was determined by X-ray diffraction and by electron microscopy. All selected samples contained at least 90% quasicrystalline phase volume according to the definition given above.
La conductivité thermique est donnée par le produit λ=αdCp. La diffusivité thermique a a été déterminée à l'aide d'un dispositif de laboratoire associant la méthode du flash laser à un détecteur semi-conducteur Hg-Cd-Te. Le laser a été utilisé pour fournir des impulsions de puissance entre 20 J et 30 J d'une durée de 5.10"4 s, pour chauffer la face frontale de l'eprouvette et le thermomètre semi-conducteur servait à détecter la réponse thermique sur la face opposée de l'eprou¬ vette. La diffusivité thermique a été déduite des expériences selon la méthode décrite dans "A. Degiovanni, High Te p. - High Pressure, 17 (1985) 683.The thermal conductivity is given by the product λ = αdCp. The thermal diffusivity has been determined using a laboratory device combining the laser flash method with an Hg-Cd-Te semiconductor detector. The laser was used to supply pulses of power between 20 J and 30 J with a duration of 5.10 "4 s, to heat the front face of the specimen and the semiconductor thermometer was used to detect the thermal response on the opposite side of the specimen. The thermal diffusivity was deduced from the experiments according to the method described in "A. Degiovanni, High Te p. - High Pressure, 17 (1985) 683.
La chaleur spécifique de l'alliage a été déterminée dans la plage de températures 20-80°C avec un calorimètre à balayage SETARAM.The specific heat of the alloy was determined in the temperature range 20-80 ° C with a SETARAM scanning calorimeter.
La conductivité thermique λ est déduite des deux précé¬ dentes mesures, connaissant la masse spécifique de l'alliage qui a été mesurée par la méthode d'Archimède par immersion dans du phtalate de butyle maintenu à 30°C (+ 0,1°C).The thermal conductivity λ is deduced from the two previous measurements, knowing the specific mass of the alloy which has been measured by the Archimedes method by immersion in butyl phthalate maintained at 30 ° C (+ 0.1 ° C ).
Les valeurs obtenues sont reportées dans le tableau 9. Ce tableau contient, à titre de comparaison, les valeurs concer¬ nant quelques matériaux de l'art antérieur (échantillons 5 à 13), dont certains sont connus comme barrière thermique (échantillons 5 à 8) .The values obtained are given in table 9. This table contains, for comparison, the values relating to some materials of the prior art (samples 5 to 13), some of which are known as thermal barrier (samples 5 to 8 ).
Dans le tableau 9, les sigles de la dernière colonne ont la signification donnée précédemment.
In Table 9, the acronyms in the last column have the meanings given above.
Ces résultats font apparaître que, à température ambiante, la conductivité thermique des alliages quasicristallins consti¬ tuant les éléments de protection de la présente invention est considérablement inférieure à celle des matériaux métalliques (aluminium métal ou Al2Cu quadratique) , donnés à titre de comparaison. Elle est inférieure de deux ordres de grandeur à
celle de l'aluminium et d'un ordre de grandeur à celle de l'acier inoxydable considéré habituellement comme un bon isolant thermique. En outre, elle est inférieure à celle de l'alumine et tout-à-fait comparable à celle de la zircone dopée par Y2°3' considéré comme l'archétype des isolants thermiques dans 1'industrie.These results show that, at room temperature, the thermal conductivity of the quasicrystalline alloys constituting the protective elements of the present invention is considerably lower than that of metallic materials (aluminum metal or quadratic Al 2 Cu), given by way of comparison. It is two orders of magnitude less than that of aluminum and an order of magnitude to that of stainless steel usually considered as a good thermal insulator. In addition, it is lower than that of alumina and quite comparable to that of zirconia doped with Y 2 ° 3 'considered as the archetype of thermal insulators in 1'industrie.
A titre de comparaison, la diffusivité thermique des alliages 90, 100, 110, 120 et 130 a été déterminée. Ces alliages, qui forment des composés définis de l'aluminium, présentent des compositions voisines de celles des alliages quasi-cristallins utilisables pour les éléments de protection de la présente invention. Toutefois, ils ne présentent pas la structure quasi-cristalline définie ci-dessus. Dans tous les cas, leur diffusivité thermique est supérieure à 5.10"6 m2/s, c'est-à-dire bien supérieure à celle des alliages retenus pour la présente invention.By way of comparison, the thermal diffusivity of the alloys 90, 100, 110, 120 and 130 was determined. These alloys, which form defined aluminum compounds, have compositions close to those of the quasi-crystalline alloys which can be used for the protective elements of the present invention. However, they do not have the quasi-crystalline structure defined above. In all cases, their thermal diffusivity is greater than 5.10 " 6 m 2 / s, that is to say much greater than that of the alloys selected for the present invention.
Exemple 12Example 12
Diffusivité thermigue en fonction de la températureThermal diffusivity as a function of temperature
Les valeurs de a ont été relevées en fonction de la tempé- rature jusqu'à 900°C.The values of a were recorded as a function of the temperature up to 900 ° C.
La mesure de la diffusivité thermique a été effectuée selon la méthode de l'exemple 11. Chaque eprouvette a été placée sous flux d'argon purifié au centre d'un four chauffé par effet Joule ; la vitesse de montée en température, programmée par ordinateur, variait linéairement à raison de 5°C/mn. Tous les échantillons conformes à la présente invention présentent une augmentation approximativement linéaire de o. avec la tempéra¬ ture. La valeur de o; déterminée à 700°C est proche du double de celle qui est mesurée à la température ambiante. De même, la chaleur spécifique augmente avec la température et atteint de 800 à 900 J/kgK à 700°C. La masse spécifique diminue de l'ordre de 1 à 2% comme l'indiquent des mesures de dilatation thermique ou de diffraction des neutrons. Par conséquent, la conductivité thermique reste inférieure à 12 W/mK, c'est-à-dire à la conduc- tivité thermique des aciers inoxydables qui sont utilisés pour certaines applications d'isolation thermique.
Les figures 1, 2 et 3 représentent respectivement l'évolu¬ tion de a en fonction de la température pour les alliages 28, 31 et 33. Les mesures enregistrées lors du chauffage sont représentées par des carrés noirs, celles enregistrées lors du refroidissement par des carrés blancs.The measurement of the thermal diffusivity was carried out according to the method of Example 11. Each test tube was placed under a stream of purified argon in the center of an oven heated by the Joule effect; the temperature rise rate, programmed by computer, varied linearly at the rate of 5 ° C / min. All the samples according to the present invention show an approximately linear increase in o. with temperature. The value of o; determined at 700 ° C is close to twice that measured at room temperature. Likewise, the specific heat increases with temperature and reaches from 800 to 900 J / kgK at 700 ° C. The specific mass decreases on the order of 1 to 2% as indicated by thermal expansion or neutron diffraction measurements. Consequently, the thermal conductivity remains below 12 W / mK, that is to say the thermal conductivity of stainless steels which are used for certain thermal insulation applications. Figures 1, 2 and 3 respectively represent the evolution of a as a function of the temperature for the alloys 28, 31 and 33. The measurements recorded during heating are represented by black squares, those recorded during cooling by white squares.
Exemple 13Example 13
La variation de la dilatation thermique de 1 'alliage 2 a été mesurée. La courbe de dilatation thermique fait app'araître que le coefficient de dilatation dépend très peu de la tempéra- ture et vaut 9.10~6/°C, valeur proche de celles des aciers inoxydables.The variation in the thermal expansion of the alloy 2 was measured. The thermal expansion curve is app 'araître that the coefficient of expansion depends very little on the tempera- ture and is 9.10 -6 / ° C, the value close to that of stainless steels.
Exemple 14 Le comportement superplastiquè de certains alliages suscep¬ tibles de constituer les éléments de protection thermique de la présente invention a été étudié. Des éprouvettes cylindriques de 4 mm de diamètre et de 10 mm de longueur, à faces rigoureu¬ sement parallèles, ont été réalisés selon la même méthode que celles de l'exemple 1 avec les alliages 34 et 35. Ces éprou¬ vettes ont été soumises à des essais mécaniques en compression sur une machine INSTROM. Des essais ont été effectués jusqu'à une charge de 250 MPa, à une vitesse de déplacement de la poutre de 50 μm/min, la température étant maintenue constante entre 600 et 850°C. Les deux alliages manifestent un comporte¬ ment superplastique dès 600"C. Exemple 15Example 14 The superplastic behavior of certain alloys likely to constitute the thermal protection elements of the present invention was studied. Cylindrical test pieces 4 mm in diameter and 10 mm in length, with strictly parallel faces, were produced according to the same method as those of Example 1 with alloys 34 and 35. These test pieces were subjected mechanical compression tests on an INSTROM machine. Tests were carried out up to a load of 250 MPa, at a speed of movement of the beam of 50 μm / min, the temperature being kept constant between 600 and 850 ° C. The two alloys exhibit a superplastic behavior from 600 "C. Example 15
Elaboration d'éléments de protection thermique selon l'invention et selon l'art antérieur.Development of thermal protection elements according to the invention and according to the prior art.
Une première série d'éprouvettes a été réalisée. Le substrat était un cylindre massif de cuivre ayant un diamètre de 30 mm et une hauteur de 80 mm et le revêtement a été appliqué à la torche à plasma selon une technique classique. L'eprouvette C0 est le cylindre de cuivre non revêtu. L'eprou¬ vette Cl a été revêtue sur toute sa surface d'une couche de 1 mm d'épaisseur de l'alliage 2 et l'eprouvette C2 a été revêtue d'une couche de 2 mm d'épaisseur de l'alliage 2. L'eprouvette C5 comporte une couche de l'alliage 2 constituant 1 'élément de protection thermique de la présente invention
servant de couche d'accrochage et une couche de zircone yttriée. Les éprouvettes C3 et C4 servant de comparaison comportent respectivement une couche de zircone yttriée et une couche d'alumine. Une autre série d' éprouvettes a été réalisée avec, comme support, un tube d'acier inoxydable ayant une longueur de 50 cm, un diamètre de 40 mm, une épaisseur de paroi de 1 mm (éprouvettes A0 à A2) . Dans chaque cas, le tube support est revêtu à l'une de ses extrémités sur une longueur dé 30 cm. Dans ce dernier cas, les dépôts ont été effectués au chalumeau oxy-gaz. Le tableau 10 ci-dessous donne la nature et l'épais¬ seur des couches pour les différentes éprouvettes. La précision sur les épaisseurs finales des dépôts était de + 0,3 mm. Toutes les éprouvettes ont été munies de thermocouples Chromel - Alumel à très faible inertie. La figure 4 représente une eprouvette du type cylindre de cuivre 1 comportant un revête¬ ment 2 et munie d'un thermocouple central 3 et d'un thermo¬ couple latéral 4, les deux étant insérés jusqu'à la moitié de la longueur du cylindre. La figure 5 représente un tube creux 5 dans lequel on fait passer un flux d'air chaud 6 et qui est muni de trois thermocouples désignés respectivement par TI, T2 et T3 , les deux premiers étant à 1 ' intérieur du tube et placés respectivement au début de la zone revêtue et à la fin de la zone revêtue, et le troisième étant sur la surface externe du revêtement. Exemple 16A first series of test pieces has been produced. The substrate was a massive copper cylinder having a diameter of 30 mm and a height of 80 mm and the coating was applied with a plasma torch according to a conventional technique. The C0 test tube is the uncoated copper cylinder. The specimen Cl was coated over its entire surface with a layer of 1 mm thick of the alloy 2 and the specimen C2 was coated with a layer of 2 mm thick of the alloy 2. The C5 test tube comprises a layer of alloy 2 constituting the thermal protection element of the present invention serving as a bonding layer and a layer of yttria zirconia. The C3 and C4 test pieces used for comparison respectively comprise a layer of yttria-containing zirconia and a layer of alumina. Another series of test pieces was produced with, as support, a stainless steel tube having a length of 50 cm, a diameter of 40 mm, a wall thickness of 1 mm (test pieces A0 to A2). In each case, the support tube is coated at one of its ends over a length of 30 cm. In the latter case, the deposits were made with an oxy-gas torch. Table 10 below gives the nature and thickness of the layers for the different test pieces. The precision on the final thicknesses of the deposits was + 0.3 mm. All the test pieces were fitted with very low inertia Chromel - Alumel thermocouples. FIG. 4 represents a test tube of the copper cylinder 1 type comprising a coating 2 and provided with a central thermocouple 3 and a lateral thermo¬ couple 4, both being inserted up to half the length of the cylinder . FIG. 5 represents a hollow tube 5 in which a flow of hot air 6 is passed and which is provided with three thermocouples designated respectively by TI, T2 and T3, the first two being inside the tube and placed respectively at beginning of the coated area and at the end of the coated area, and the third being on the outer surface of the coating. Example 16
Utilisation des éléments de protection comme protection par rapport à une flamme. Les éprouvettes C0, Cl, C2 , C3 , C4 et C5 ont été placées sur leur base sur une brique réfractaire. Des impulsions de chaleur successives d'une durée de 10 s ont été appliquées à chaque eprouvette à intervalle de 60 s et la réponse des ther¬ mocouples a été enregistrée. Ces impulsions ont été produites par la flamme d'un chalumeau, placé à distance constante de 1'eprouvette et orientée face au thermocouple proche de la surface. Le débit des gaz de combustion a été soigneusement contrôlé et maintenu constant durant toute l'expérience. Deux séries d'expériences ont été menées : l'une avec des éprou-
vettes initialement à 20°C et l'autre avec des éprouvettes initialement à 650°C.Use of protective elements as protection against a flame. The test pieces C0, Cl, C2, C3, C4 and C5 were placed on their base on a refractory brick. Successive heat pulses lasting 10 s were applied to each specimen at 60 s intervals and the response of the thermocouples was recorded. These pulses were produced by the flame of a torch, placed at a constant distance from the specimen and oriented opposite the thermocouple close to the surface. The flow of combustion gases was carefully controlled and kept constant throughout the experiment. Two series of experiments were carried out: one with tests vettes initially at 20 ° C and the other with test tubes initially at 650 ° C.
Les éprouvettes CO à C5 permettent de définir trois para¬ mètres qui résument les résultats de l'expérience, à savoir la différence maximale P de température entre les deux thermo¬ couples, ΔT/Δt la vitesse de montée en température du thermo¬ couple latéral 4 durant 1' impulsion et 1' incrément de tempéra¬ ture ΔT réalisé au centre de l'eprouvette (thermocouple 3). Ces données figurent dans le tableau 10. On a constaté que la couche de zircone de l'eprouvette C3 ne résistait pas à plus de trois impulsions et était fissurée dès la première impulsion. L'échantillon C2 n'a commencé à se fissurer qu'à la sixième impulsion et l'échantillon Cl a résisté à plus de 50 impul¬ sions. Ces résultats font apparaître que les éléments de protection de la présente invention, utilisés comme barrière thermique, présentent des performances au moins équivalentes à celles de la zircone.The CO to C5 test tubes make it possible to define three parameters which summarize the results of the experiment, namely the maximum temperature difference P between the two thermo¬ couples, ΔT / Δt the rate of temperature rise of the lateral thermo¬ couple 4 during the pulse and the temperature increment ΔT produced in the center of the test tube (thermocouple 3). These data are shown in Table 10. It was found that the zirconia layer of the C3 specimen did not resist more than three pulses and was cracked from the first pulse. The C2 sample did not start to crack until the sixth pulse and the C1 sample withstood more than 50 pulses. These results show that the protective elements of the present invention, used as a thermal barrier, have performances at least equivalent to those of zirconia.
Exemple 17 Utilisation des éléments de protection selon 1 'invention comme sous-couche de barrière thermique.Example 17 Use of the protective elements according to the invention as a thermal barrier underlay.
Dans 1'eprouvette C5, 1 'élément de protection thermique de la présente invention constitue une sous-couche. On a constaté que la couche de zircone de l'eprouvette C3 ne résistait pas à plus de trois impulsions de chaleur et était fissurée dès la première impulsion. Pour l'eprouvette C5, soumise également à une série d'impulsions thermiques, la température de surface du dépôt de zircone, mesurée par un troisième thermocouple placé en contact avec le dépôt à la fin des essais, s'est stabilisée à 1200 ° C . L'expérience a porté sur 50 impulsions et l'éprou- vette C5 a résisté sans dommage apparent, bien que le coeffi¬ cient de dilatation du cuivre soit proche du double de celui de l'alliage quasi-cristallin, ce qui impliquerait d'importantes contraintes de cisaillement à l'interface substrat/dépôt, si le matériau de sous-couche ne devenait pas plastique. Les éléments de protection thermique de la présente invention sont donc bien adaptés à la réalisation de sous-couches d'accrochage, en particulier pour des barrières thermiques.
TABLEAU 10In the C5 specimen, the thermal protection element of the present invention constitutes an undercoat. It was found that the zirconia layer of the C3 specimen did not resist more than three heat pulses and was cracked from the first pulse. For the C5 test tube, also subjected to a series of thermal pulses, the surface temperature of the zirconia deposit, measured by a third thermocouple placed in contact with the deposit at the end of the tests, stabilized at 1200 ° C. . The experiment focused on 50 pulses and the C5 test-tube resisted without apparent damage, although the coeffi¬ cient of copper expansion is close to twice that of the quasi-crystalline alloy, which would imply significant shear stresses at the substrate / deposition interface, if the underlay material does not become plastic. The thermal protection elements of the present invention are therefore well suited to the production of bonding sub-layers, in particular for thermal barriers. TABLE 10
EXEMPLE 18 Application d'un élément de protection thermique de la présente invention à l'isolation d'un réacteur. Les éprouvettes A0, Al et A2 ont été utilisées pour évaluer l'aptitude des alliages de l'invention à isoler thermiquement un dispositif. Les éprouvettes étaient munies chacune de 3 thermocouples TI, T2 et T3 tels que représentés sur la figure 5. Un courant d'air chaud à débit constant a été envoyé à travers le tube en acier inoxydable constituant le substrat de chaque eprouvette. La température de l'air à l'entrée, mesurée à l'aide du thermocouple TI, était de 300+2"C. La température de surface, mesurée à l'aide du thermocouple T3, a été enregis¬ trée en fonction du temps à partir de la mise en route du géné- rateur d'air chaud. Le thermocouple T2 a permis de vérifier que les conditions transitoires d'établissement du flux d'air chaud étaient identiques pour toutes les mesures.EXAMPLE 18 Application of a thermal protection element of the present invention to the insulation of a reactor. Test specimens A0, A1 and A2 were used to assess the ability of the alloys of the invention to thermally insulate a device. The test pieces were each provided with 3 thermocouples TI, T2 and T3 as shown in FIG. 5. A current of hot air at constant flow rate was sent through the stainless steel tube constituting the substrate of each test piece. The inlet air temperature, measured using the TI thermocouple, was 300 + 2 "C. The surface temperature, measured using the T3 thermocouple, was recorded as a function of the time from the start of the hot air generator The thermocouple T2 made it possible to verify that the transient conditions for establishing the hot air flow were identical for all the measurements.
Les figures 6 et 7 représentent 1'évolution de la température du surface de chacun des éprouvettes A0, Al et A2 en fonction du temps. La température de surface de l'eprouvette AO (sans revêtement) dépasse à l'équilibre celle de 1 'eprouvette A2 de
3Figures 6 and 7 show the evolution of the surface temperature of each of the test pieces A0, Al and A2 as a function of time. The surface temperature of the AO specimen (without coating) exceeds at equilibrium that of the A2 specimen by 3
35°C environ et celle de 1*eprouvette Al de 27°C. Les éléments de protection thermique de la présente invention donnent des résultats intéressants en ce qui concerne 1' isolation thermiqu .
35 ° C approximately and that of the A1 specimen 27 ° C. The thermal protection elements of the present invention give interesting results with regard to thermal insulation.
Claims
1. Alliages dont le constituant essentiel est l'aluminium caractérisés en ce que :1. Alloys, the essential constituent of which is aluminum, characterized in that:
- ils présentent la composition atomique suivante : AlaCUbCθb«(B,C)cMdNeIf (I) a + b + b' + c + d + e + f = 100 en nombre d'atomes a > 50 0 < b < 14 0 ≤ b' ≤ 22 0 < b + b' < 30- they have the following atomic composition: Al a CUbCθb “(B, C) cMdN e If (I) a + b + b '+ c + d + e + f = 100 in number of atoms a> 50 0 <b <14 0 ≤ b '≤ 22 0 <b + b'<30
0 ≤ c ≤ 5 8 ≤ d < 300 ≤ c ≤ 5 8 ≤ d <30
0 ≤ e < 4 f < 2 M représente un ou plusieurs éléments choisis parmi Fe, Cr, Mn, Ni, Ru, Os, Mo, V, Mg, Zn, Pd ;0 ≤ e <4 f <2 M represents one or more elements chosen from Fe, Cr, Mn, Ni, Ru, Os, Mo, V, Mg, Zn, Pd;
N représente un ou plusieurs éléments choisis parmi W, Ti, Zr, Hf, Rh, Nb, Ta, Y, Si, Ge, les terres rares ;N represents one or more elements chosen from W, Ti, Zr, Hf, Rh, Nb, Ta, Y, Si, Ge, rare earths;
1 représente les impuretés d'élaboration inévitables ; - et ils contiennent au moins 30% en masse d'une ou plusieurs phases quasicristallines.1 represents the inevitable processing impurities; - And they contain at least 30% by mass of one or more quasicrystalline phases.
2. Alliages selon la revendication 1, caractérisés en ce qu'ils présentent la composition atomique (I) avec 0 < b < 5, 0 < b' < 22 et/ou 0 < c < 5, M représentant Mn + Fe + Cr ou Fe + Cr.2. Alloys according to claim 1, characterized in that they have the atomic composition (I) with 0 <b <5, 0 <b '<22 and / or 0 <c <5, M representing Mn + Fe + Cr or Fe + Cr.
3. Alliages selon la revendication 1, caractérisés en ce qu'ils présentent la composition atomique (I) avec 15 < d ≤ 30, M représentant au moins Fe + Cr, avec un rapport atomique Fe/Cr < 2. 3. Alloys according to claim 1, characterized in that they have the atomic composition (I) with 15 <d ≤ 30, M representing at least Fe + Cr, with an atomic ratio Fe / Cr <2.
4. Alliages selon la revendication 3, caractérisés en ce que b > 6, b' < 7 et e > 0 et N est choisi parmi Ti, Zr, Rh et4. Alloys according to claim 3, characterized in that b> 6, b '<7 and e> 0 and N is chosen from Ti, Zr, Rh and
Nb.Nb.
5. Alliages selon la revendication 3, caractérisés en ce que b < 2, b' > 7 et e >. 0. 5. Alloys according to claim 3, characterized in that b <2, b '> 7 and e> . 0.
6. Alliages selon la revendication 1, caractérisés en ce que 0 < e ≤ 1, N étant choisi parmi W, Ti, Zr, Rh, Nb, Hf et6. Alloys according to claim 1, characterized in that 0 <e ≤ 1, N being chosen from W, Ti, Zr, Rh, Nb, Hf and
Ta. Your.
7. Alliages selon la revendication 1, caractérisés en ce que b < 5 et b' 5.7. Alloys according to claim 1, characterized in that b <5 and b '5.
8. Alliages selon la revendication 7, caractérisés en ce que b < 2 et b1 > 7. 8. Alloys according to claim 7, characterized in that b <2 and b 1 > 7.
9. Alliages selon la revendication 1, caractérisés en ce que 0 < c < 1 et/ou 7 < b' < 14.9. Alloys according to claim 1, characterized in that 0 <c <1 and / or 7 <b '<14.
10. Alliages selon l'une quelconque des revendications 1 à 9, caractérisés en ce qu'ils sont obtenus sous forme de pièce massive. 10. Alloys according to any one of claims 1 to 9, characterized in that they are obtained in the form of a solid part.
11. Alliages selon l'une quelconque des revendications 1 à 9, caractérisés en ce qu'ils sont obtenus sous forme de dépôt sur un substrat.11. Alloys according to any one of claims 1 to 9, characterized in that they are obtained in the form of a deposit on a substrate.
12. Substrats revêtus par un alliage selon l'une quel¬ conque des revendications 1 à 9. 12. Substrates coated with an alloy according to one of the claims 1 to 9.
13. Application d'un alliage selon l'une quelconque des revendications 1 à 9, à 1'élaboration de surfaces anti-usure et/ou anti-frottement, de surfaces anti-choc, de surfaces de référence, de surfaces anti-cavitation ou anti-érosion, de surface résistant à l'oxydation ou à la corrosion. 13. Application of an alloy according to any one of claims 1 to 9, to the development of anti-wear and / or anti-friction surfaces, anti-shock surfaces, reference surfaces, anti-cavitation surfaces or anti-erosion, surface resistant to oxidation or corrosion.
14. Application d'un alliage selon l'une quelconque des revendications 1 à 9, à l'élaboration de joints métal-métal ou de joints métal-céramique.14. Application of an alloy according to any one of claims 1 to 9, in the preparation of metal-metal joints or metal-ceramic joints.
15. Application d'un alliage selon l'une quelconque des revendications 1 à 9, au revêtement d'ustensiles pour contact alimentaire.15. Application of an alloy according to any one of claims 1 to 9, to the coating of utensils for food contact.
16. Applications électrotechniques des alliages selon l'une quelconque des revendications 1 à 9.16. Electrotechnical applications of the alloys according to any one of claims 1 to 9.
17. Application selon la revendication 16 à la réalisation d'éléments de chauffage par induction électromagnétique. 17. Application according to claim 16 for the production of heating elements by electromagnetic induction.
18. Application d'un alliage selon l'une quelconque des revendications 1 à 9, à la réalisation d'éléments de protection thermique d'un substrat.18. Application of an alloy according to any one of claims 1 to 9, to the production of thermal protection elements of a substrate.
19. Application selon la revendication 18, caractérisée en ce que 1'élément de protection thermique est constitué par un matériau quasicristallin constitué essentiellement par ledit alliage, déposé sur le substrat. 19. Application according to claim 18, characterized in that the thermal protection element consists of a quasicrystalline material consisting essentially of said alloy, deposited on the substrate.
20. Application selon la revendication 19, caractérisée en ce que ledit matériau quasicristallin est déposé sur le substrat par projection thermique.20. Application according to claim 19, characterized in that said quasicrystalline material is deposited on the substrate by thermal spraying.
21. Application selon la revendication 18, caractérisée en ce que ledit matériau quasicristallin comporte au moins 80% en volume d'au moins une phase quasi-cristalline.21. Application according to claim 18, characterized in that said quasicrystalline material comprises at least 80% by volume of at least one quasi-crystalline phase.
22. Application selon la revendication 18, caractérisée en ce que ledit matériau quasicristallin présente une porosité supérieure à 10%. 22. Application according to claim 18, characterized in that said quasicrystalline material has a porosity greater than 10%.
23. Application selon la revendication 18, caractérisée en ce que l'élément de protection thermique constitue une barrière thermique à des températures inférieures à 800"C.23. Application according to claim 18, characterized in that the thermal protection element constitutes a thermal barrier at temperatures below 800 "C.
24. Application selon la revendication 23, caractérisée en ce que ledit matériau quasicristallin contient en outre des éléments stabilisants à une teneur inférieure à 2 % en nombre d'atomes, choisis parmi W, Zr, Ti, Rh, Nb, Hf et Ta.24. Application according to claim 23, characterized in that said quasicrystalline material also contains stabilizing elements at a content of less than 2% by number of atoms, chosen from W, Zr, Ti, Rh, Nb, Hf and Ta.
25. Application selon la revendication 18, caractérisée en ce que l'élément de protection thermique est utilisé sous forme d'une couche intermédiaire d'accrochage entre un support et une barrière thermique, la température de surface de ladite barrière pouvant éventuellement dépasser 800°C.25. Application according to claim 18, characterized in that the thermal protection element is used in the form of an intermediate bonding layer between a support and a thermal barrier, the surface temperature of said barrier possibly being able to exceed 800 °. vs.
26. Application selon la revendication 25, caractérisée en ce que 1'élément de protection thermique est constitué par une alternance de couches de matériau quasi-cristallin et de couches de matériaux bons conducteurs de la chaleur. 26. Application according to claim 25, characterized in that the thermal protection element is constituted by an alternation of layers of quasi-crystalline material and layers of materials which are good conductors of heat.
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
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EP92904842A EP0521138B1 (en) | 1991-01-18 | 1992-01-15 | Aluminium alloys, substrates coated with same and their applications |
DE69223180T DE69223180T2 (en) | 1991-01-18 | 1992-01-15 | ALUMINUM ALLOYS AND SUBSTRATES COATED WITH THESE ALLOYS AND THEIR USE |
AU12717/92A AU648876B2 (en) | 1991-01-18 | 1992-01-15 | Aluminium based, copper-cobalt alloy |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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FR9100549A FR2671808B1 (en) | 1991-01-18 | 1991-01-18 | ALUMINUM ALLOYS WITH SPECIFIC PROPERTIES. |
FR91/00549 | 1991-01-18 |
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WO1992013111A1 true WO1992013111A1 (en) | 1992-08-06 |
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PCT/FR1992/000030 WO1992013111A1 (en) | 1991-01-18 | 1992-01-15 | Aluminium alloys, substrates coated with same and their applications |
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EP (1) | EP0521138B1 (en) |
JP (1) | JP3244178B2 (en) |
AU (1) | AU648876B2 (en) |
DE (1) | DE69223180T2 (en) |
ES (1) | ES2110492T3 (en) |
FR (1) | FR2671808B1 (en) |
WO (1) | WO1992013111A1 (en) |
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FR2699554A1 (en) * | 1992-12-23 | 1994-06-24 | Metallisation Ind Ste Nle | Thermal barriers, material and process for their preparation. |
WO1996002798A1 (en) * | 1994-07-15 | 1996-02-01 | Thomas Eisenhammer | Radiation converter for converting electromagnetic radiation into heat and vice versa |
EP0757114A1 (en) * | 1995-07-31 | 1997-02-05 | Gaz De France | Quasicrystallic coating and process for coating |
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FR2745304A1 (en) * | 1996-02-23 | 1997-08-29 | Centre Nat Rech Scient | Multi-phase aluminium alloy for use in vehicle and aircraft engine parts |
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ES2131451A1 (en) * | 1996-10-04 | 1999-07-16 | Inst Nacional De Tecnica Aeroe | Quasicrystalline coatings of the thermal barrier type for the protection of components in the hot zones of turbines |
WO2000037713A1 (en) * | 1998-12-22 | 2000-06-29 | MTU MOTOREN- UND TURBINEN-UNION MüNCHEN GMBH | Antiabrasion coating |
CN106498247A (en) * | 2016-12-05 | 2017-03-15 | 郑州丽福爱生物技术有限公司 | Wear-resisting composite alloy material of a kind of impact resistance and preparation method thereof |
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FR2833020B1 (en) * | 2001-11-30 | 2004-10-22 | Inst Francais Du Petrole | USE OF QUASI-CRYSTALLINE ALUMINUM ALLOYS IN REFINING AND PETROCHEMICAL APPLICATIONS |
US20040022662A1 (en) * | 2002-07-31 | 2004-02-05 | General Electric Company | Method for protecting articles, and related compositions |
DE10332420A1 (en) | 2003-07-16 | 2005-02-10 | Alstom Technology Ltd | Aluminum-based multinary alloys and their use as heat and corrosion protective coatings |
DE10358813A1 (en) * | 2003-12-16 | 2005-07-21 | Alstom Technology Ltd | Quasi-crystalline alloy used in the production of a component of a gas turbine or compressor comprises a composition containing aluminum, nickel, ruthenium and transition metal |
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WO2010063930A1 (en) | 2008-12-01 | 2010-06-10 | Saint-Gobain Coating Solution | Coating for a device for shaping glass material |
JP2016156055A (en) * | 2015-02-24 | 2016-09-01 | トヨタ自動車株式会社 | Insulation material |
CN105821261B (en) * | 2016-05-30 | 2017-10-27 | 广州晶品智能压塑科技股份有限公司 | A kind of lid maker mold materials of highly corrosion resistant |
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Also Published As
Publication number | Publication date |
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ES2110492T3 (en) | 1998-02-16 |
EP0521138A1 (en) | 1993-01-07 |
JP3244178B2 (en) | 2002-01-07 |
AU1271792A (en) | 1992-08-27 |
DE69223180T2 (en) | 1998-04-23 |
EP0521138B1 (en) | 1997-11-19 |
AU648876B2 (en) | 1994-05-05 |
JPH05505649A (en) | 1993-08-19 |
FR2671808B1 (en) | 1994-06-17 |
DE69223180D1 (en) | 1998-01-02 |
FR2671808A1 (en) | 1992-07-24 |
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