US3297435A - Production of heat-treatable aluminum casting alloy - Google Patents

Production of heat-treatable aluminum casting alloy Download PDF

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Publication number
US3297435A
US3297435A US267239A US26723963A US3297435A US 3297435 A US3297435 A US 3297435A US 267239 A US267239 A US 267239A US 26723963 A US26723963 A US 26723963A US 3297435 A US3297435 A US 3297435A
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alloys
alloy
aluminum
copper
silicon
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US267239A
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English (en)
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James E Hanafee
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Huntington Alloys Corp
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International Nickel Co Inc
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Priority to US267239A priority Critical patent/US3297435A/en
Priority to GB10534/64A priority patent/GB996804A/en
Priority to AT238364A priority patent/AT248129B/de
Priority to DEP1267852A priority patent/DE1267852B/de
Priority to BE645514A priority patent/BE645514A/xx
Priority to FR968159A priority patent/FR1397473A/fr
Priority to NL6403037A priority patent/NL6403037A/xx
Priority to ES297860A priority patent/ES297860A1/es
Priority to LU45719D priority patent/LU45719A1/xx
Priority to CH374264A priority patent/CH419621A/fr
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
    • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
    • B01J23/00—Catalysts comprising metals or metal oxides or hydroxides, not provided for in group B01J21/00
    • B01J23/38—Catalysts comprising metals or metal oxides or hydroxides, not provided for in group B01J21/00 of noble metals
    • B01J23/54—Catalysts comprising metals or metal oxides or hydroxides, not provided for in group B01J21/00 of noble metals combined with metals, oxides or hydroxides provided for in groups B01J23/02 - B01J23/36
    • B01J23/66—Silver or gold
    • C—CHEMISTRY; METALLURGY
    • C07—ORGANIC CHEMISTRY
    • C07D—HETEROCYCLIC COMPOUNDS
    • C07D301/00—Preparation of oxiranes
    • C07D301/02—Synthesis of the oxirane ring
    • C07D301/03—Synthesis of the oxirane ring by oxidation of unsaturated compounds, or of mixtures of unsaturated and saturated compounds
    • C07D301/04—Synthesis of the oxirane ring by oxidation of unsaturated compounds, or of mixtures of unsaturated and saturated compounds with air or molecular oxygen
    • C07D301/08—Synthesis of the oxirane ring by oxidation of unsaturated compounds, or of mixtures of unsaturated and saturated compounds with air or molecular oxygen in the gaseous phase
    • C07D301/10—Synthesis of the oxirane ring by oxidation of unsaturated compounds, or of mixtures of unsaturated and saturated compounds with air or molecular oxygen in the gaseous phase with catalysts containing silver or gold
    • 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
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • H—ELECTRICITY
    • H03—ELECTRONIC CIRCUITRY
    • H03K—PULSE TECHNIQUE
    • H03K5/00—Manipulating of pulses not covered by one of the other main groups of this subclass
    • H03K5/01—Shaping pulses
    • H03K5/08—Shaping pulses by limiting; by thresholding; by slicing, i.e. combined limiting and thresholding

Definitions

  • the present invention relates to the production of aluminum alloys and, more particularly, to the production of cast aluminum alloys.
  • iron in an amount of 1% was added to an aluminum alloy nominally containing 10% copper and 0.2% magnesium.
  • This alloy is characterized by good resistance to hot-cracking so that it may be successfully produced in a permanent mold as well as in sand.
  • its mechanical properties and/or characteristics were such that it became a special purpose alloy, i.e., for pistons, and thus was uneconomical to produce.
  • an aluminum casting alloy that was heat-treatable, i.e., an alloy exhibiting a marked susceptibility to improvement of its mechanical properties, etc., by heat treatment, was developed. It contained about 4% to about 5% copper, but only small castings of simple design could be cast because this alloy exhibited a severe tendency to hot-crack and shrink in the sand mold. Silicon (about 0.8%) was added and this somewhat reduced the tendency to crack. However, this silicon content was not sufficient to permit casting in a permanent mold so that the silicon content was increased to about 2.5%. As in the case of the previously mentioned aluminum alloys, while this addition made the alloy more favorable from one standpoint (casting char- Q 3,297,435 Patented Jan. 10, 1967 acteristics), it made it less favorable from another standpoint (mechanical strength).
  • Another object of the present invention is the provision of a new process for producing unique aluminum alloy castings having good room temperature and elevated temperature mechanical properties and/or characteristics.
  • the invention also contemplates providing a new heattreatable aluminum alloy casting having a favorable microstructure.
  • FIGURE 1 is a reproduction of a photomicrograph taken at a magnification of diameters (100x) of an etched aluminum alloy within the scope of the present invention
  • FIGURES 2 and 3 are reproductions of photornicrographs taken at 100x of etched aluminum alloys not within the scope of the present invention.
  • the present invention contemplates the production of. unique aluminum casting alloys having microscopic aluminide morphologies that are favorable, i.e., the morphology, as viewed under a microscope, is such that the aluminum alloy has good mechanical properties and/or characteristics at room temperature and at temperatures up to about 600 F. or higher.
  • a favorable morphology is obtained by a process in which the massive, coarse aluminides which ordinarily form in aluminum alloys containing, by weight, to 25% silicon, 4% to 9% nickel and up to 1% each of copper and magnesium with the sum of copper and magnesium being 0.2% to 2% are substantially inhibited from forming by delimiting and/ or controlling unavoidable iron present to an amount which is correlated to the percentages of silicon (Si), nickel (Ni) and copper plus magnesium (Cu+Mg) such that the amount of iron is less than 1-0.1 (percent Ni) -0.02 (percent Si) +0.05[2percent(Cu+Mg)]
  • the aluminum alloys produced in accordance with the aforementioned control of iron which contain silicon, nickel, and copper plus magnesium in the previously mentioned ranges and controlled amounts are in themselves novel since these alloys are characterized by a refined aluminide microstructure as well as having some measure of room temperature ductility in combination with good mechanical properties and/ or characteristics at temperatures as high as 600 F. or
  • the alloys according to this invention contain aluminum, silicon, nickel and either copper or magnesium or both, and each of these elements in combination with each other element plays an important role in controlling the properties of the alloy providing the iron is delimited and/ or controlled in the aforesaid manner.
  • the silicon content is in the range of 5% to 25% and, advantageously, between and 16%.
  • the inclusion of silicon in the alloys of the present invention contributes importantly to the castability and other foundry characteristics of the alloy, improves wear characteristics, and beneficially lowers the thermal expansion characteristics thereof. However, if too much silicon (more than about 25%) is included, the alloy becomes very brittle, difficult to machine, and the pouring temperature for casting the alloy is much too high for economical practice.
  • too little silicon (less than about 5%) is also disadvantageous to the properties of the alloy.
  • the coefficient of linear thermal expansion becomes raised to the point at which the use of the alloy in high temperature applications is inhibited.
  • the wear resistance of an aluminum-nickel alloy containing too little silicon is materially decreased as are the castability characteristics of the alloy.
  • nickel when present in amounts of 4% to 9%, and advantageously 5% to 7%, improves the high temperature properties and/or characteristics of aluminum/silicon alloys.
  • the nickel if present in amounts of less than about 4%, there is no appreciable gain in hot hardness properties over nickel-free aluminumsilicon alloys.
  • the thermal expansion characteristics of such an alloy are undesirably high.
  • the foundry characteristics deteriorate, e.g., the feeding rate of the molten alloy to the mold,is reduced, the pouring temperature is raised, etc.
  • castings made of the alloy tend to be much too brittle and it is found that there is a detrimental great volume of aluminides present in such castings.
  • the casting alloys produced in accordance with the invention may contain up to 1% copper and up to 1% magnesium provided that at least 0.2% of copper plus magnesium is contained therein.
  • copper and .4 magnesium afford a measure of improved machinability to these alloys. If too little copper plus magnesium (less than about 0.2%) is present, their hardening or strengthening function would be lost.
  • the alloys of the invention may optionally contain alloying and/or incidental elements such as titanium, boron, phosphorus, sodium, cadmium, indium, tin, lithium, manganese and chromium.
  • the alloys produced within the scope of the present invention may tolerate up to 1% titanium without adversely affecting the beneficial properties and/or characteristics.
  • between 0.1% and 0.3% titanium in the castings has an advantageous effect in that it contributes to grain refinement.
  • Up to 0.05% and, advantageously, up to 0.01%, boron may be included in the alloys of the present invention without adversely affecting their properties and/ or characteristics and may even be advantageously included since it appears to afford some measure of grain refinement.
  • Phosphorus in amounts of up to 0.03% contributes to hard particle refinement of the hypereutectic aluminum-silicon-nickel alloys within the scope of this invention.
  • excessive sodium causes overmodification with a resultant coarse microstructure.
  • Cadmium, indium, tin and/or lithium may be usefully present in the age hardenable aluminum-nickel-silicon alloys containing copper plus magnesium since each of these elements improves the aging characteristics.
  • up to 0.5% cadmium, up to 0.5% indium, up to 0.5% tin and up to 1% lithium may be incorporated into the alloys of this invention.
  • the amounts of such elements are minimized
  • the alloy may contain, by weight, up to 0.2% cadmium, up to 0.2% indium, up to 0.2% tin and up to 0.8% lithium.
  • lithium it is important that excessive lithium is not employed as its inclusion may cause the casting characteristics of the alloy to deteriorate.
  • Manganese and chromium may be tolerated in amounts of up to 0.5% manganese and up to 0.5% chromium.
  • each of these elements tends to form undesirable aluminides and should be controlled.
  • the aluminum alloys of this invention do contain silicon, nickel, copper and/ or magnesium in the controlled amounts and for the reasons hereinbefore set forth and while these alloys may optionally and/or incidentally contain restricted amounts of titanium, boron, phosphorus, sodium, cadmium, indium, tin, lithium, chromium and/0r manganese, no combination of such ingredients, even Within the aforementioned ranges, produces satisfactory alloys unless the iron content in weight percent of such alloys is less than 1-0. 1 (percent Ni)0.02 (percent Si) +0.05 [2-percent(Cu+Mg)] and all commercially practical forms of aluminum and aluminum alloys for ordinary applications contain some lIOIl, i.e., at least about 0.05% by weight of the alloy.
  • each alloy set forth in the following example was air inor elements.
  • any change in silicon or nickel duction melted and, when adjusted to the required comor both greatly afie-cts the permissible iron content of such position with regard to iron, nickel, silicon and copper alloys.
  • Copper plus magnesium has a similar but lesser plus magnesium, cast into a 1" X 2" x 14" permanent effect.
  • the alloy contains more than the maximum wedge mold which was at about 450 F. and which had iron (which depends on the contents of nickel, silicon and a bottom aluminum chill plate at room temperature.
  • the copper plus magnesium the alloy has poor ductility at pouring temperatures varied between about 1250 F.
  • the alloys have adequate room hours, water quenching and following with a stabilizing temperature ductility and are characterized by having a treatment comprising heating to about 400 F. and holdmicrostructure of refined aluminides. Since the formation ing at that temperature for approximately 8 hours.
  • the alloys of the present invention exhibit good mechanirates as well as by iron content, the iron content should cal properties and/ or characteristics, including ultimate be at the lower end of the permissible range whenever it tensile strength (U.T.S.), 0.1% offset yield strength (Y.S.) is difiicult to impress a chill completely through the crossand elongation, at room temperature-s, as is illustrated in section of the solidifying molten metal in the mold. Table II.
  • the alloys produced within the contemplation of the processes of the present invention are heat-treatable and are advantageously heat-treated to provide castings having superior properties and/ or characteristics.
  • Advantageous heat treatments include 1) a stabilizing (overaging) at about 400 F. to 700 F. for about 2 hours to 20 hours, advantageously at about 400 F. to 650 F. for about 3 hours to 16 hours; (2) a solution heat treatment at about 900 F. to 1050 F. for about 3 hours to 20 hours followed by a water quench and a stabilization at about 400 F. to 700 F. for about 2 hours to 20 hours; and (3) a solution treatment and water quench as in (2) followed by an aging treatment at about 300 F. to 500 F. for about 1 hour to 20 hours.
  • the process of the present invention and the iron-containing aluminum alloys produced thereby may be made by any of the known foundry procedures as those skilled in the art will readily understood.
  • the alloys may be air induction melted and cast, e.g., into a permanent mold at about 450 F. with or without a chill plate although an aluminum chill plate is advantgeously employed so that the formation of harmful aluminides is abated by the faster solidification rate.
  • the pouring temperature is a function of the silicon and nickel levels but does lie between about 1200 F. and 1500 F. Standard commercial degassing, e.g., with dry chlorine, and silicon refining and modifying techniques may also be used when appropriate.
  • alloys produced according to the processes of this invention have acceptable room temperature properties and/or characteristics, particularly since there was no evidence of brittle fracture.
  • these alloys have good elevate-d temperature properties and characteristics.
  • alloys C, D and E were held at 600 F. for about hours and then mechanically tested. It was found that at 600 F. their ultimate tensile strengths were 10,800, 10,900, 11,800 p.s.i., respectively, and their elongations were 7.8%, 10% and 5.7%, respectively.
  • the Rockwell H hot hardnesses of alloys C, D, and B were determined. It was found that after about 24 hours at 600 F. the Rockwell H hardnesses at 600 F.
  • the alloys of this invention have ultimate tensile strengths of at least 10,000 psi. together with acceptable ductility at 600 F. and also have high hot hardness of at least 55 Rockwell H at this temperature. At room temperature the alloys of this invention are characterized by ultimate tensile strengths of at least 32,000 psi. together with acceptable ductility.
  • alloys Z, Y, X, W, V, U, T, S and R did not satisfy the correlation or iron to nickel, silicon and copper plus magnesium and, when tested at room temperature, they exhibited substantially no elongation and were characterized by brittle fracture.
  • Alloy Q contained no nickel and had an ultimate tensile strength of only 7,100 after 100 hours at 600 F.
  • Alloy P although low in iron, was outside of this invention in the nickel content. This alloy had an ultimate tensile strength of only 8,700 p.s.i. after 100 hours at 600 F.
  • Alloy 0 contained no nickel and had a Rockwell H hardness at 600 F. of only 38 after 24 hours at 600 F.
  • Alloys E, X and Y were each etched with 0.5% hydrofluoric acid and examined under a microscope at a magnification of 100 diameters (100x) and these photomicrographs are depicted in FIGURES 1, 2 and 3, respectively, wherein the dark (appearing as black in the drawing), constituents are aluminides.
  • the gray constituents, of generally polygonal configuration in FIGURES 1 and 2, and of eutectic-like configuration in FIGURE 3, are silicon.
  • FIGURE 1 illustrating an alloy produced within the scope of this invention
  • FIGURES 2 and 3 illustrating alloys not produced in accordance with this invention
  • FIGURE 1 the aluminides are of a refined configuration.
  • the aluminides depicted in FIGURES 2 and 3 are coarse and massive. Accordingly, the mechanical properties of the aluminum casting alloy having a refined microstructure are superior to those having the coarse, massive microstructure as shown hereinbefore.
  • the process of the present invention permits the use of a commercial form of aluminum and aluminum alloys which contain iron as an impurity. In addition, it allows for the production of aluminum castings which because of their sizes and/ or shapes do not allow rapid solidification throughout the entire cross section of the solidifying molten metal.
  • the alloys prepared in accordance with the present invention are particularly useful whenever a strong, lightweight component having good mechanical properties at high temperatures, e.g., about 600 F., as well as at room temperature is needed.
  • the present invention is usefully employed in the materials of construction for pistons, engine blocks and other internal combustion engine parts and components.
  • the alloys of the present invention have relatively low coefiicients of thermal expansion, their attractiveness for use in engine blocks and pistons is considerably enhanced.
  • the alloys prepared in accordance with the present invention are particularly adapted to be utilized in conjunction with iron compo nents requiring close tolerances between the aluminum between the aluminum alloys of this invention and iron and iron alloys is quite similar.
  • a process for refining massive, coarse aluminides present in an ironcontaining aluminum casting alloy consisting essentially by weight, 4% to 9% nickel, 5% to 25% silicon and up to 1% of copper and up to 1% of magnesium with the sum of copper and magnesium being 0.2% to 2% and increasing the high temperature mechanical properties and characteristics without sacrificing any of the room temperature properties and characteristics of the alloys which comprises delimiting unavoidable iron present such that the iron content in the alloy to be cast is less than 10.1 (percent Ni) 0.02 (percent Si) +0.05 [2-percent (Cu+Mg)] casting the alloy, and thereafter heat treating said cast alloy at a temperature of about 400 F. to about 700 F.
  • a process for producing a heat-treatable iron-containing aluminum alloy which comprises preparing a melt consisting essentially by weight, of 4% to 9% nickel, 5% to 25% silicon, up to 1% copper, up to 1% magnesium, the sum of copper and magnesium being between 0.2% and 2%, up to 1% titanium, up to 0.05% boron, up to 0.03% phosphorus, up to 0.05% sodium, up to 0.5% cadmium, up to 0.5% indium, up to 0.5% tin, up to 1% lithium, up to 0.5% chromium, up to 0.5% manganese with the balance essentially aluminum, delimiting unavoidable iron present in the melt to an amount that is less than 10.l (percent Ni) 0.02 (percent Si) 1 +0.05 [2percent (Cu+Mg)] casting said melt and thereafter solidifying said melt, whereby the formation of coarse, massive aluminides is substantially inhibited.
  • a process for producing a heat-treatable, iron-containing aluminum alloy which comprises preparing a melt consisting essentially, by weight, of 5% to 7% nickel,
  • a heat-treatable, iron-containing aluminum casting alloy consisting essentially, by weight, of 4% to 9% nickel, 5% to 25% silicon, up to 1% copper, up to 1% magnesium, the sum of copper and magnesium being between 0.2% and 2%, iron in an amount which is correlated to nickel, silicon and copper plus magnesium and which is less than l-0.1 (percent Ni) 0.02 (percent Si) +0.05 [2percent (Cu+Mg)] up to 1% titanium, up to 0.05% boron, up to 0.03% phosphorus, up to 0.05% sodium added, up to 0.5% cadmium, up to 0.5% indium, up to 0.5% tin, up to 1% lithium, up to 0.5% chromium, up to 0.5% manganese, with the balance essentially aluminum; said alloy being characterized by having a microstructure that is substantially devoid of harmful, coarse, massive aluminides.
  • a heat-treatable, iron-containing aluminum casting alloy consisting essentially, by weight, of 5% to 7% nickel, 10% to 16% silicon, 0.5% to 1% copper, 0.5% to 1% magnesium, iron in an amount which is correlated to nickel, silicon, copper and magnesium and which is less than 10.1 (percent Ni) 0.02 (percent Si) +0.05 [2percent (Cu+Mg)] 10 0.1% to 0.3% titanium, up to 0.01% boron, up to 0.2% cadmium, up to 0.2% indium, up to 0.2% tin, up to 0.8% lithium, up to 0.03% phosphorus, up to 0.05 sodium added, up to 0.5% chromium, up to 0.5% manganese, with the balance essentially aluminum; said alloy being characterized by having a microstructure that is substantially devoid of harmful, coarse, massive aluminides.

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  • Chemical & Material Sciences (AREA)
  • Organic Chemistry (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Mechanical Engineering (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Physics & Mathematics (AREA)
  • Nonlinear Science (AREA)
  • Conductive Materials (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Silicon Compounds (AREA)
  • Molds, Cores, And Manufacturing Methods Thereof (AREA)
  • Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
US267239A 1963-03-22 1963-03-22 Production of heat-treatable aluminum casting alloy Expired - Lifetime US3297435A (en)

Priority Applications (10)

Application Number Priority Date Filing Date Title
US267239A US3297435A (en) 1963-03-22 1963-03-22 Production of heat-treatable aluminum casting alloy
GB10534/64A GB996804A (en) 1963-03-22 1964-03-12 Aluminium alloys
AT238364A AT248129B (de) 1963-03-22 1964-03-19 Aluminiumgußlegierung
BE645514A BE645514A (fr) 1963-03-22 1964-03-20 Alliages a base d'aluminium
DEP1267852A DE1267852B (de) 1963-03-22 1964-03-20 Verwendung einer Aluminium-Silizium-Legierung mit hoher Duktilitaet und Waermehaerte
FR968159A FR1397473A (fr) 1963-03-22 1964-03-20 Alliages d'aluminium
NL6403037A NL6403037A (nl) 1963-03-22 1964-03-20 Werkwijze ter bereiding van aluminiumlegeringen en gegoten voorwerpen vervaardigd onder toepassing van een dergelijke legering
ES297860A ES297860A1 (es) 1963-03-22 1964-03-21 Un procedimiento de hacer una aleación
LU45719D LU45719A1 (fr) 1963-03-22 1964-03-21 Alliages d'aluminium
CH374264A CH419621A (fr) 1963-03-22 1964-03-23 Alliage d'aluminium

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US267239A US3297435A (en) 1963-03-22 1963-03-22 Production of heat-treatable aluminum casting alloy

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US (1) US3297435A (de)
AT (1) AT248129B (de)
BE (1) BE645514A (de)
CH (1) CH419621A (de)
DE (1) DE1267852B (de)
ES (1) ES297860A1 (de)
FR (1) FR1397473A (de)
GB (1) GB996804A (de)
LU (1) LU45719A1 (de)
NL (1) NL6403037A (de)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3392015A (en) * 1965-08-24 1968-07-09 Int Nickel Co Aluminum-base alloy for use at elevated temperatures
US4432313A (en) * 1982-05-27 1984-02-21 Trw Inc. Aluminum base material with hard facing deposit
EP0144898A3 (en) * 1983-12-02 1985-07-24 Sumitomo Electric Industries Limited Aluminum alloy and method for producing same
GB2570026A (en) * 2018-01-04 2019-07-10 Jaguar Land Rover Ltd Aluminium alloy for casting

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19845279A1 (de) * 1998-10-01 2000-04-13 Alcan Gmbh Al-Ni-Si-Legierung

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1508556A (en) * 1921-01-04 1924-09-16 Aluminum Co Of America Making castings of aluminum alloys
US1848816A (en) * 1932-03-08 Robert s
GB373434A (en) * 1931-06-05 1932-05-26 C M D Engineering Company Ltd An improved alloy for use as a material for pistons for internal combustion engines
US2155651A (en) * 1937-06-17 1939-04-25 Hardy Metallurg Corp Manufacture of aluminum alloys
CA497450A (en) * 1953-11-03 Rolls-Royce Limited Aluminium alloy having low coefficient of expansion

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE518256C (de) * 1931-02-13 Schmidt Gmbh Karl Gleitlager
CH142802A (de) * 1928-12-22 1930-10-15 Limited Aluminium Aluminium-Legierung.
DE670570C (de) * 1928-12-22 1939-01-20 Metallgesellschaft Akt Ges Aluminiumlegierung
DE694471C (de) * 1934-08-22 1940-08-01 Schmidt Gmbh Karl g von Gleitlagern

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1848816A (en) * 1932-03-08 Robert s
CA497450A (en) * 1953-11-03 Rolls-Royce Limited Aluminium alloy having low coefficient of expansion
US1508556A (en) * 1921-01-04 1924-09-16 Aluminum Co Of America Making castings of aluminum alloys
GB373434A (en) * 1931-06-05 1932-05-26 C M D Engineering Company Ltd An improved alloy for use as a material for pistons for internal combustion engines
US2155651A (en) * 1937-06-17 1939-04-25 Hardy Metallurg Corp Manufacture of aluminum alloys

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3392015A (en) * 1965-08-24 1968-07-09 Int Nickel Co Aluminum-base alloy for use at elevated temperatures
US4432313A (en) * 1982-05-27 1984-02-21 Trw Inc. Aluminum base material with hard facing deposit
EP0144898A3 (en) * 1983-12-02 1985-07-24 Sumitomo Electric Industries Limited Aluminum alloy and method for producing same
US4702885A (en) * 1983-12-02 1987-10-27 Sumitomo Electric Industries, Ltd. Aluminum alloy and method for producing the same
GB2570026A (en) * 2018-01-04 2019-07-10 Jaguar Land Rover Ltd Aluminium alloy for casting

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AT248129B (de) 1966-07-11
DE1267852B (de) 1968-05-09
NL6403037A (nl) 1964-09-23
GB996804A (en) 1965-06-30
FR1397473A (fr) 1965-04-30
CH419621A (fr) 1966-08-31
LU45719A1 (fr) 1964-05-21
ES297860A1 (es) 1964-07-01
BE645514A (fr) 1964-09-21

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