US3303561A - Process for the preparation of an ironaluminum alloy - Google Patents

Process for the preparation of an ironaluminum alloy Download PDF

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US3303561A
US3303561A US261152A US26115263A US3303561A US 3303561 A US3303561 A US 3303561A US 261152 A US261152 A US 261152A US 26115263 A US26115263 A US 26115263A US 3303561 A US3303561 A US 3303561A
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aluminum
iron
alloy
ingot
weight
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Cabane Gerard
Mouturat Pierre
Petit Jean-Francois
Sainfort Gerard
Salesse Marc
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    • G—PHYSICS
    • G21—NUCLEAR PHYSICS; NUCLEAR ENGINEERING
    • G21C—NUCLEAR REACTORS
    • G21C3/00—Reactor fuel elements and their assemblies; Selection of substances for use as reactor fuel elements
    • G21C3/02—Fuel elements
    • G21C3/04—Constructional details
    • G21C3/06—Casings; Jackets
    • G21C3/07—Casings; Jackets characterised by their material, e.g. alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • 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
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E30/00—Energy generation of nuclear origin
    • Y02E30/30—Nuclear fission reactors
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/49—Method of mechanical manufacture
    • Y10T29/4998—Combined manufacture including applying or shaping of fluent material
    • Y10T29/49988—Metal casting
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/49—Method of mechanical manufacture
    • Y10T29/4998—Combined manufacture including applying or shaping of fluent material
    • Y10T29/49988—Metal casting
    • Y10T29/49991—Combined with rolling

Definitions

  • the present invention is directed to a process by means of which it is possible to reduce the brittleness of the alloy and to permit the production of parts carrying a proportion of aluminum which may reach approximately 40% by weight.
  • the process in accordance with the present invention is characterized by the steps of preparing a molten mixture of iron, aluminum and one or a number of components or additives which have the effect of reducing brittleness, the aluminum content :being comprised between 16% and 40%, of casting the said mixture under conditions such that internal stresses are very small, the'arrangements referred-to being so chosen as to prevent the occurrence of separations between grain boundaries, and of subsequently destroying the casting structure by a mechanical-working process of hot-state deformation.
  • the said impurities are usually introduced by the iron, since aluminum can be obtained in a high state of purity.
  • An addition of zirconium or of niobium provides appropriate and effective means of trapping the embrittling impurities such as carbon, oxygen and nitrogen.
  • the proportion of addition elements is preferably fixed as a function of the proportion of the impurities present. Accordingly, it has been possible to determine, for example, that the proportion, by Weight, of zirconium must be at least equal to approximately ten times the proportion of carbon-that is to say in an atom-for-atom ratioin order to eliminate the troublesome effects which are due to the presence of carbon, the proportion of which can generally be maintained below 0.02%.
  • the binary alloys of iron with aluminum which may comprise, if necessary, up to 1% of addition elements, containing a proportion by weight of aluminum which may vary between 18 and 31% are particularly valuable.
  • the present invention such as melting and pouring in vacuo, in an inert atmosphere or in free air under a protective fi-ux; the starting materials are preferably as pure as possible.
  • the sequence in which the two main or single constituents are introduced most effectively is that in which iron is fed in first, .followed by aluminum.
  • the particular features heretofore described have the effect of obtaining a product, as cast, which has only slight brittleness; the remainder of the treatment is carried out in such manner as to obtain good mechanical properties (breaking strength, yield strength, elongation, hardness, etc.) with suitable impact strength.
  • the remainder of the treatment according to the present invention therefore consists in a hot-state mechanical working process which produces the deformation of the as cast product.
  • the casting structure is destroyed; the temperature reached is usually within the range of 600 C. to 1,200 0., and depends on the proportion of aluminum and on the nature and proportion of the additive or additives; the said roughing-down process can be carried out either by extrusion, pressure :forging and/ or rolling; this treatment can be carried out without shocks or without excessively rapid deformations.
  • the temperature reached is usually within the range of 600 C. to 1,200 0., and depends on the proportion of aluminum and on the nature and proportion of the additive or additives; the said roughing-down process can be carried out either by extrusion, pressure :forging and/ or rolling; this treatment can be carried out without shocks or without excessively rapid deformations.
  • the roughing-down process is alone suflicient to provide directly the finished products.
  • the mechanical working process of deformation in the hot state or roughing-down process which makes it possible to destroy the casting structure, preferably compris es the steps of covering the ingot which is derived from the casting operation with a metallic jacket, of carrying out the operations of hot-state machine-work on the ingot as fitted with its jacket and of the elimination of the jacket.
  • the jacketing'or cladding process can be effected by any conventional means, but must not be conducive to subsequent weakness at any point in a zone which is subjected to high stresses during the roughing-down process.
  • Such means can include cold hydrostatic cladding, electrolytic coating, metallizing by projection, etc.
  • One of these subsequent treatments can consist of coldstate deformation by machine-Work or so-called cold work, that is to say, which is carried out at room temperature or at a temperature between room temperature and the temperature of re-crystallization; this machinework process of deformation in the cold state or .cold work which results in strain-hardening, 'may be carried out, for example, either by rolling or drawing, and permits:
  • the mini-mum thickness which can be achieved by cold rolling is much smaller than that achieved by hot rolling alone, at least in the case of the rolling machines which are usually employed;
  • the cold working treatment is made possible by the roughing-down process which has been previously described, even when the aluminum content is higher than In this strain-hardened state and with an iron content which is higher than approximately 75%, the Fe-Al alloy is a disordered solid solution; the said alloy is therefore ferromagnetic and can be employed as a magneticmaterial, especially in the form of thin sheeting or foil.
  • the Fe-Al alloys having an iron content within the range of 75 to 84% in accordance with the present invention are therefore new magnetic materials which constitute new industrial products; the said alloys have the advantage of a density which is lower than that of other iron-base magnetic alloys and which is also lower than that of such Fe-Al magnetic alloys as have already been prepared heretofore; moreover, the oxidation resistance of the alloys in accordance with the present invention is very high, and higher than that of the Fe-Al alloys of the prior art, inasmuch as the aluminum content is higher.
  • the alloys in accordance with the present invention may, therefore, effectively replace in certain cases cobalt alloys with a view to constructing the magnets employed in nuclear reactors.
  • the said alloy For the purpose of improving the mechanical characteristics of the Fe-Al alloy, it is of advantage to subject the said alloy, either directly after the roughingdown process or after the cold working process, to a heat treatment which has the effect of modifying the distribution of impurities as well as the structure of the alloy; the said heattreatment may be of any suitable known type which is adapted to the desired modifications, while the temperature must obviously not exceed that at which the grain would grow again to a large size; this treatment may accordingly consist, for example, of an annealing process or a drawing of temper.
  • the treatment may subsequently be followed by a further mechanical treatment, either in the hot state or in the cold state or both, which is in turn followed by a heat treatment; the cycle may also be repeated a number of times.
  • the alloy is intended to be employed as a structural material in either a. medium-temperature or high-temperature reactor, it may prove desirable for the purpose of, ensuring that the mechanical behavior of the said material during operation is stabilized to the maximum extent within the shortest possible time, to carry out the said heat treatment as a preliminary step, at least at the maximum temperature which is subsequently reached in the reactor channel
  • the Fe-Al alloys in accordance with the present invention are characterized by remarkable oxidation resistance which is greater than that of stainless steel in the case of high aluminum contents (over 18%, for example), and which is essentially due to the fact that the external surface of the alloy is coated with a self-protecting film of oxide.
  • the alloys in accordance with the present invention may also be contemplated for use as structural material in nuclear reactors, especially as cladding material for fuel elements.
  • the neutron absorption of the alloy in accordance with the present invention is distinctly lower than in the case of stainless steel and the yield strength at high temperature, for example, between 450 C. and 700 C., is distinctly higher than that of stainless steel.
  • the Al-Fe alloy which may in certain cases contain beryllium or even silicon, therefore constitutes a structural material which may be employed in nuclear reactors, for example, as cladding material, especially in high-temperature reactors, and may be employed in those cases in which stainless steel or beryllium are not suitable for use, the former on account of its very high neutron-absorption capacity, the latter on account of its brittleness, of its low creep strength above 600 C., of the swelling of cans or jackets as a result of the formation of helium pockets, and finally of its unduly low corrosion resistance when hot, especially in CO at 600 C.
  • a reactor which is designed for the use of uranium oxide (natural uranium) as fuel, for the use of CO as a coolant gas at a temperature of 600 C. and a pressure of 60 kg./cm. and for the use of cylindrical fuel elements 15 'mm. in diameter, could not operv.ate with a can of stainless steel having a thickness of 0.2
  • the cross-sections 2 of the cladding tubes are as follows:
  • the percentage of aluminum contained in the alloy may be decreased while at the same time decreasing the global cross-section of the alloy; 1% by weight of beryllium is in fact equivalent from the viewpoint of neutron absorption cross-section to 2% by Weight of aluminum.
  • Another object of the present invention resides in the provision of a process for producing an iron-aluminum alloy in which thealuminum content may be increased to a range above that normally feasible heretofore, without producing a product of which the brittleness is so great as to preclude any subsequent machining operations.
  • Another object of the present invention resides in the provision of a novel iron-aluminum alloy containing, by weight, approximately 16 to 40% of aluminum of which the brittleness is relatively low and which permits of subsequent hot or cold working operations.
  • a further object of the present invention resides in the provision of Fe-Al alloys in which the brittleness is controlled to a degree not realizable heretofore.
  • a further object of the present invention resides in the provision of a process for the manufacture of iron-aluminum alloys in which the thermal stresses are reduced and incipient boundary separations are controlled to fall within acceptable values.
  • a still further object of the present invention resides in a novel alloy principally containing iron and aluminum and having a relatively high proportion of aluminum which has magnetic properties and may be produced in the form of thin sheeting or foil.
  • Another object of the present invention resides in the provision of a process for the manufacture of an ironaluminum alloy which permits of obtaining very small thicknesses, accurate dimensions, and cold working treatments as well as subsequent heat treatments.
  • a further object of the present invention resides in the provision of a process for producing a low density iron-base magnetic alloy and in the resulting product which not only exhibits such low density properties, but also an oxidation resistance that is considerably higher than that of other iron-aluminum alloys as well as stainless steel.
  • Still another object of the present invention resides in the provision of a process for producing an ironaluminum alloy having neutron absorption properties that are distinctly lower than those of stainless steel and having a yield strength that is considerably higher than that of stainless steel.
  • Still a further object of the present invention resides in the provision of a process for producing an ironaluminum alloy and the alloy resulting from such process which may be used in nuclear reactors and has such properties and characteristics as to obviate the need for enriched fuels.
  • the alloy to be produced has the following composition:
  • the cooling rate is limited to approximately 50 C. per hour. It should be noted in passing that preheating is of course necessary in this example only on account of the fact that the casting mass employed in this example is small.
  • step (b) Roughing-down.
  • the ingot which is obtained from step (a) above after cooling is fitted with a metallic jacket, for example, of ordinary steel (XC 12 or XC 35 in particular).
  • the covering of the ingot may be carried into effect by means of any one of the methods of conventional cladding, for example, by welding a sheet which has previously been wrapped around the ingot, by cold-state hydrostatic cladding, etc.
  • the thickness of the jacket is obviously designed so that the subsequent mechanical treatments permit a thickness to remain which is such that there is no danger of tearing. This thickness was of the order of 2 mm. in the example described.
  • the composite work-piece formedby the ingot which is covered with its jacket is subjected to a series of rolling passes at 1050 C., each pass necessarily resulting in a reduction in thickness which is sufficient to work-harden the metal right through.
  • the presence of the jacket makes it possible to facilitate the surface flow of the alloy and permits of deformations which the ingot would not withstand if it were treated in the uncovered state.
  • each pass resulted in a reduction in thickness of 2 mm.
  • a reheating for a period of two minutes, thereby bringing the temperature back to 1050 C.
  • the thickness of the composite workpiece can thus be reduced without difficulty to approximately 2 mm. It is apparent that the reheating treatment is only necessary on account of the fact that the temperature of the work-piece falls substantially as a result of the small dimensions of the latter.
  • the composite work-piece can then be freed of its steel jacket (the thickness of which has obviously been substantially reduced to the same extent as those of the workpiece) by dilferent methods.
  • the jacket which in the example described only remains in the form of a film of the order of a few tenths of a millimeter, can be, for example:
  • Cold working-The alloy which is thus obtained may be subjected to subsequent mechanical operations which result in limited deformations, for example, deformation by rolling at room temperature with annealing treatments between successive rolling passes.
  • EXAMPLE II (a) Melting and casting.A cast is prepared under conditions which are similar to those of Example I starting with 2.9 kilograms of electrolytic iron, 1.1 kilograms of aluminum and 4 grams of zirconium. The temperature is then raised to a few tens of degrees above the solidification temperature (or liquidus temperature) of the alloy and the latter is poured off in vacuo into a preheated ingot-mold. The cooling process is then carried out as in Example I.
  • the alloy which is thus cast has the following composition by weight:
  • the said machining operation may not be necessary in the case of certain surface conditions and when the roughing-down operation consists in a rolling process which can be performed after cladding according to a procedure which is similar to that described in the previous example. However, such a machining operation is necessary for the purpose of shaping the ingot when the treatment involves extrusion of the jacketed ingot.
  • the lathe turning operation is performed with a view to obtaining a cylinder having a rounded front end.
  • the work-piece which is thus machined is covered by means of any conventional process with a steel jacket having a shape which is adapted to that of the said work-piece and a thickness of a few millimeters. It may be useful to replace mild steel by other metals or alloys such as iron-aluminum alloys containing a low percentage of aluminum, which have the advantage of better oxidation resistance and, in certain cases, nickel or cupronickel.
  • the composite part which is thus obtained is then pressextruded at 950 C. At this temperature, it is possible to reach an extrusion ratio of the order of 1:30, or in other words, it is possible to prepare rods of 11 mm. diameter from machined ingots of 60 mm. diameter.
  • a similar process makes it possible to obtain tubes having a thickness which is less than one millimeter.
  • the lathe turning operation is performed with a view to producing a hollow cylinder which is then clad both internally and externally.
  • the separation of the alloy and its steel jacket can be carried out in accordance with any one of the processes which have already been referred toin Example 'I, for example, by chemical dissolution in a solution composed of 50% water and.50% nitric acid which rapidly dissolves the jacket, by oxidation of the jacket, by air heating or in an oxidizing atmosphere. In the latter case, the jacket disappears whereas the alloy is not attacked by virtue of its high resistance to oxidation.
  • the extruded product obtained may, in certain cases, be employed as it stands, inasmuch as it has a good surface to. finish. However, it may, if necessary, be subjected to a further cold working treat ment and may, for example, be threaded on a threadcutting lathe. In fact, the grain size after extrusion is reduced to 20 or 30 microns and accordingly permits of machining.
  • the part which has been either machined or extruded may besubjected to a heat treatment for a period of 8 one hour at 800 C.; after this heat treatment, the extruded product has the following characteristics:
  • Tempera- Ultimate Yield Elongation titre Tensile Strength, at Fracture, 0. Strength, kgsJmm. Percent kgsJmrn.
  • Example III The same operations as in Example II (melting, casting, machiningQjacketing, extrusion and elimination of the jacket) have also been applied to an alloy cont-aining 25% aluminum by Weight, the composition of which is as follows:
  • the product obtained has the characteristics which are given in the table below:
  • Tempera- Ultimate Yield Elongation ture Tensile Strength. at Fracture, 0. Strength, kgs./mrn. Percent kgs/mmfl 1 Brittle fracture.
  • EXAMPLE V (a) Melting and casting. The same operations of melting and casting are applied to an alloy containing 25% aluminum having the following composition by weight:
  • a reduction value of less than 90% can be obtained with final thicknesses of the order of one millimeter.
  • the Vickers hardness number of the product is 500 HV; heat treatments by annealing at 950 C. make it possible to reduce this hardness number to 280 HV.
  • a process for the preparation of an iron-aluminum alloy consisting essentially of between greater than 18% and about 40% by weight of aluminum, up to 1% by weight of an additive selected from the group consisting of zirconium, niobium, titanium, yttrium, the rare earths, boron and mixtures thereof and the balance iron, comprising the steps of:
  • a process for the preparation of a ternary ironaluminum base alloy consisting essentially of between greater than 18% and to about 40% by weight of aluminum, up to 2.8% by weight of berylliumand the balance iron, comprising the steps of:
  • a process for the preparation of an iron-aluminum base alloy consisting essentially of between greater than 18% and about 40% by weight of aluminum, up to 1% 'by weight of an additive selected from the group consisting of zirconium, niobium, titanium, yttrium, the rare earths, boron and mixtures thereof, up to 2.8% by weight of beryllium and the balance iron, comprising the steps of:
  • a process for the preparation of a binary iron-aluminum alloy consisting essentially of between 30% and about 40% by weight of aluminum and the balance iron, comprising the steps of:
  • a process for the preparation of an iron-aluminum alloy consisting essentially of between greater than 18% and about 40% by weight of aluminum, up to 1% by weight of an additive selected from the group consisting of zirconium, niobium, titanium, yttrium, the rare earths, boron and mixtures thereof and the balance iron, comprising the steps of:
  • a binary iron-aluminum alloy consisting essentially of between 30% and about 40% by weight of aluminum and the balance iron.
  • An iron-aluminum alloy consisting essentially of between greater than 18% and about 40% by weight of aluminum, up to 1% by weight of an additive selected from the group consisting of zirconium, niobium, titanium, yttrium, the rare earths, boron and mixtures thereof and the balance iron.
  • a relatively thin sheet composed of the iron-aluminum alloy of claim 11.
  • a ternary iron-aluminum base alloy consisting essentially of between :greater than 18% and about 40% by weight of aluminum, up to 2.8% by weight of beryllium and the balance iron.
  • An iron-aluminum base alloy consisting essentially of between greater than 18% and about 40% by weight of aluminum, up to 1% by weight of an additive selected from the group consisting of zirconium, niobium, titanium, yttrium, the rare earths, boron and mixtures thereof, up to 2.8% by weight of beryllium and the balance iron.
  • a ternary iron-aluminum base alloy consisting essentially of between greater than 18% and about 40% by weight aluminum, from about 1% to about 2.8% by Weight of berylli np and the balance iron.
  • An iron-aluminum base alloy consisting essentially of between greater than 18% and about 40% by weight of aluminum, up to 1% by weight of an additive selected from the group consisting of zirconium, niobium, titanium, yttrium, the rare earths, boron and mixtures thereof, from about 1% to about 2.8% by weight of silicon and the balance iron.
  • a ternary iron-aluminum base alloy consisting essentially of between greater than 18% and about 40% by weight of aluminum, at least 1% by weight of a material selected from the group consisting of beryllium and silicon andthe balance iron.
  • An iron-aluminum base alloy consisting essentially of between greater than 18% and about 40% by weight of aluminum, up to 1% by weight of an additive selected from the group consisting of zirconium, niobium, titanium, yttrium, the rare earths, boron and mixtures thereof, at least 1% by 'weight of a material selected from the group consisting of beryllium and silicon and the balance iron.
  • An iron-aluminum alloy consisting essentially of between greater than 18% and 31% by weight of aluminum, up to 1% by weight of an additive selected from the group consisting of zirconium, niobium, titanium, yttrium, the rare earths, boron and mixtures thereof and the balance iron, said alloy consisting solely of the Fe-Al phase.
  • Alprocess for the preparation of an at least binary iron-aluminum alloy consisting essentially of between greater than 18% and about 40% by weight of aluminum and the balance iron, said alloy being characterized by a relatively low brittleness permitting machining operations, comprising the steps of:

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US261152A 1962-03-02 1963-02-26 Process for the preparation of an ironaluminum alloy Expired - Lifetime US3303561A (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR889735A FR1323724A (fr) 1962-03-02 1962-03-02 Procédé de préparation d'un alliage fer-aluminium
FR967787A FR85480E (fr) 1962-03-02 1964-03-17 Procédé de préparation d'un alliage fer-aluminium

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GB (2) GB1030613A (fr)
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Cited By (2)

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US3386819A (en) * 1962-03-02 1968-06-04 Commissariat Energie Atomique Iron-aluminum alloys containing less than 84% by weight iron and an additive and process for preparing the same
US4988488A (en) * 1989-10-19 1991-01-29 Air Products And Chemicals, Inc. Iron aluminides and nickel aluminides as materials for chemical air separation

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US4419130A (en) * 1979-09-12 1983-12-06 United Technologies Corporation Titanium-diboride dispersion strengthened iron materials
US5620651A (en) * 1994-12-29 1997-04-15 Philip Morris Incorporated Iron aluminide useful as electrical resistance heating elements
CN111455279A (zh) * 2020-02-28 2020-07-28 深圳市新星轻合金材料股份有限公司 铁铝合金及其制备方法

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US2804387A (en) * 1955-11-14 1957-08-27 Ford Motor Co Preparation of iron aluminum alloys
US2846494A (en) * 1955-11-30 1958-08-05 Rca Corp Thermoelectric devices
US2859143A (en) * 1954-08-06 1958-11-04 Edward A Gaugler Ferritic aluminum-iron base alloys and method of producing same
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US3144330A (en) * 1960-08-26 1964-08-11 Alloys Res & Mfg Corp Method of making electrical resistance iron-aluminum alloys

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US2859143A (en) * 1954-08-06 1958-11-04 Edward A Gaugler Ferritic aluminum-iron base alloys and method of producing same
US2768915A (en) * 1954-11-12 1956-10-30 Edward A Gaughler Ferritic alloys and methods of making and fabricating same
US2804387A (en) * 1955-11-14 1957-08-27 Ford Motor Co Preparation of iron aluminum alloys
US2846494A (en) * 1955-11-30 1958-08-05 Rca Corp Thermoelectric devices
US3026197A (en) * 1959-02-20 1962-03-20 Westinghouse Electric Corp Grain-refined aluminum-iron alloys
US3144330A (en) * 1960-08-26 1964-08-11 Alloys Res & Mfg Corp Method of making electrical resistance iron-aluminum alloys

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3386819A (en) * 1962-03-02 1968-06-04 Commissariat Energie Atomique Iron-aluminum alloys containing less than 84% by weight iron and an additive and process for preparing the same
US4988488A (en) * 1989-10-19 1991-01-29 Air Products And Chemicals, Inc. Iron aluminides and nickel aluminides as materials for chemical air separation
DE4033338A1 (de) * 1989-10-19 1991-04-25 Air Prod & Chem Eisen-aluminide und nickel-aluminide als stoffe fuer die chemische auftrennung von luft

Also Published As

Publication number Publication date
DE1251039B (fr)
NO116549B (fr) 1969-04-14
BE629096A (fr)
LU48204A1 (fr) 1965-05-17
US3386819A (en) 1968-06-04
GB1030613A (en) 1966-05-25
GB1083083A (en) 1967-09-13
OA01988A (fr) 1970-05-05
BE660989A (fr) 1965-07-01
IL23129A (en) 1968-12-26
NL6503371A (fr) 1965-09-20
CH503794A (fr) 1971-02-28
NL289214A (fr)
DE1258608B (de) 1968-01-11

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