EP1522600B1 - Geschmiedeter Aluminium Legierung, die ausgezeichnete Dauerfestigkeit Aufweist - Google Patents

Geschmiedeter Aluminium Legierung, die ausgezeichnete Dauerfestigkeit Aufweist Download PDF

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Publication number
EP1522600B1
EP1522600B1 EP20030021819 EP03021819A EP1522600B1 EP 1522600 B1 EP1522600 B1 EP 1522600B1 EP 20030021819 EP20030021819 EP 20030021819 EP 03021819 A EP03021819 A EP 03021819A EP 1522600 B1 EP1522600 B1 EP 1522600B1
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Prior art keywords
high temperature
alloy
forged material
alloy forged
temperatures
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EP20030021819
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English (en)
French (fr)
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EP1522600A1 (de
Inventor
Yasuki Daian Plant Kamitakahara
Toshihiro Daian Plant Katsura
Manabu Kobe Corporate Research Labs. Nakai
Yasuaki Daian Plant Watanabe
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Kobe Steel Ltd
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Kobe Steel Ltd
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Priority to EP20030021819 priority Critical patent/EP1522600B1/de
Priority to DE2003609711 priority patent/DE60309711T2/de
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper 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 A 2000-series Aluminum alloy forged material (hereinafter, Aluminum referred only to Al) , and particularly to an Al alloy forged material having an excellent high temperature fatigue strength, and other excellent high temperature characteristics (heat resistance and high temperature proof stress).
  • Al alloy forging materials having excellent high temperature characteristics are used in materials for aviation and space equipments, such as rockets and airplanes; materials for transportation equipments, such as railroad vehicles, cars, and vessels; or materials for machine parts, such as engine parts and compressors; specifically, in parts made fromAl alloy used in service conditions of particularly high temperatures exceeding 100°C, such as in rotation rotors, and rotation impellers or pistons.
  • the high temperature characteristics here include a creep resistance and a high temperature proof stress under high temperatures.
  • 2000-series Al alloys of AA standard or JIS standard have been used for these so-called heat-resistant Al alloy forging materials.
  • This kind of Al alloy includes 2219, 2618, etc.
  • prolonged use at high temperatures exceeding 120°C gives remarkable strength reduction in these 2000-series Aluminums alloys.
  • 2219Al alloy including 0.3% of Mg added that is, 2519Al alloy (Al / 6.1 Cu; 0.3 Mn; 0.15 Zr; 0.1 V) was developed.
  • 2519 (Ag) Al alloy in which Ag is added in 2519Al alloy was also developed.
  • many Al alloys in relation to these 2519Al alloys and 2519(Ag) Al alloys are also proposed (for example, refer to JP-A No. 1987-112748, and U.S. Pat. No.4610733).
  • the present inventors also proposed heat-resistant Al alloys enabling guarantee of improved high temperature characteristics with sufficient reproducibility.
  • microstructures after solution heat treatment of Al alloy forged materials have ⁇ ' phase and/or ⁇ phase; and crystal grain diameter is of isometric recrystallized particles of no more than 500 ⁇ m (Refer to JP-A No.2000-119786) .
  • the present inventors pay attention to influence of hardening speed after solution heat treatment, and proposed that when a slow (low) hardening speed (low cooling rate) is used, such as in the case where an average cooling rate between 400°C and 290°C is no more than 30000°C / minute, especially, Zr, Cr, and Mn in the Al alloy forged materials are regulated to Zr: no more than 0.09%, Cr: no more than 0.05%, and Mn: no more than 0.6%, respectively (refer to JP-A No. 2001-181771).
  • a slow (low) hardening speed low cooling rate
  • Al alloy forged materials such as those described in US 5512112 which have excellent high temperature characteristics, such as the heat resistances and high temperature proof stress, have furthermore a room for improvement in high temperature fatigue strength. That is, even improved Al alloy forged materials shown in JP-A No. 2000-119786, JP-A No. 2001-181771, etc. have only numbers of fracture repetitions of (3 - 6) ⁇ 10 6 times in a rotating bending fatigue test (under a condition of maximum stress 130 MPa, stress ratio 1, and 150°C) in a fatigue strength under an operating condition of stress load at high temperatures (high temperature fatigue strength). Therefore, further improvement has been required for product application in which a higher high temperature fatigue strength is required.
  • the present invention is made paying attention to such a situation, and a purpose thereof is providing Al alloy forged materials having not only high temperature characteristics, such as heat resistance and high temperature proof stress, but an excellent high temperature fatigue strength.
  • an Aluminum alloy forged material of the present invention in order to attain the purpose is that the material includes Cu: 4.0 - 7.0%; Mg: 0.2 - 0.4%; Ag: 0.05 - 0.7%; V: 0.05% - 0.15%, Al-V based precipitates in a forged material structure have a distribution density of no less than 1.5 piece/ ⁇ m 3 and wherein the crystal grain size of the alloy forged material is equiaxed and the average grain diameter is in the range of 10-500 ⁇ m.
  • an Aluminum alloy cast material including Cu: 4.0 - 7.0%; Mg: 0.2 - 0.4%; Ag: 0.05 - 0.7%; V: 0.05% - 0.15% is preferably hot forged at a temperature of 280 - 430°C after homogenized heat treatment at a temperature of 500 - 535°C for no less than 15 hours, and subsequently solution heat treatment at a temperature of 510 - 545°C is performed to give a hardening processing.
  • % representations of an alloying element contents represent a mass %.
  • definition of the distribution density of Al-V based compounds in the above-mentioned forged material structure is specified for thermally refined Aluminum alloy forged materials.
  • a high temperature fatigue strength indicated by the above-mentioned Japanese patent application No. 2003-90660 shows a number of (3 - 6) ⁇ 10 6 times [represented also as (3 -6)e6] of fracture repetitions in rotating bending fatigue test (under a conditions of maximum stress 130 MPa and a stress ratio of 1, and 150°C).
  • an Al-V based compound is precipitated in a forged material structure so that V included satisfies a sufficient amount (number) in order to increase high temperature fatigue strength.
  • a high temperature fatigue strength is remarkably improved as compared in a forged material including comparatively small amount of Al-V based compound precipitated in a forged material structure in spite of similar content of V.
  • a distribution density of Al-V based precipitate in a forged material structure is set no less than 1.5 piece/ ⁇ m 3 .
  • a distribution density of Al-V based precipitate of less than 1.5 piece/ ⁇ m 3 may not remarkably improve the high temperature fatigue strength.
  • the distribution density definition of such Al-V based precipitate may be satisfied over whole of the forged material structure, or at least in a forged material region that requires a high temperature fatigue strength.
  • Observation using a transmission electron microscope (TEM) having 10,000 times of magnification for the forged material structure after thermal refining processing (heat treatment) mentioned later may give the distribution density of Al-V based precipitate.
  • TEM transmission electron microscope
  • the above-mentioned observation for a plurality of regions over whole of structures of each region of the forged material or for the forged material region that at least requires high temperature fatigue strength may give a number of Al-V based precipitates within a microscopic field (dispersed grain), which may be converted into a number per ⁇ m 3 .
  • distribution density measurement of the Al-V based precipitate may be performed to one point of the forged material region that particularly requires a high temperature fatigue strength, in order to satisfy reproducibility, measurement in two or more points is preferable. In measurement in two or more points, the distribution density of Al-V based precipitate are of course expressed by an average value of measured values of a plurality of measurement points.
  • a homogenized heat treatment is performed to this kind of cast material at temperatures of 500 - 535°C, for less than 15 hours at the maximum and in many cases for a processing time of about 8 hours.
  • Even a homogenized heat treatment conditions on such a short period enable homogenization of the cast material itself.
  • V has a very slow diffusion rate as compared with other elements. Therefore, under such short-time homogenized heat treatment conditions, V included as alloying elements keeps a state of solid solution during the homogenized heat treatment, which disables precipitation to give an actual mass sufficient to remarkably improve high temperature fatigue strength as an Al-V based compound, that is, to give no less than 1.5 piece/ ⁇ m 3 of distribution density in the forged material structure of an Al-V based precipitate.
  • Manufacturing conditions and manufacturing method of an Al alloy forged material in the present invention are fundamentally same as conventional methods except for a period of the above-mentioned homogenized heat treatment. In other words, it is also an advantage of the present invention to avoid large modification of manufacturing conditions or manufacture methods of an Al alloy forged material.
  • an Al alloy molten metal is melted, adjusted within a component range of the present invention, and is cast to manufacture ingots using usual melting casting methods selected suitably, such as a continuous casting rolling method and a semicontinuous casting method (direct chill casting process).
  • temperatures of 280-430°C hot forging of the ingots is carried out after the above-mentioned prolonged homogenized heat treatment to manufacture an Al alloy forged material.
  • materials for forging extruding or rolling processed ingots, that is, extruded materials and rolled materials may be used.
  • Temperatures of less than 500°C in the above-mentioned homogenized heat treating may not give a solid solution of crystallized object of an ingot here, but provide an inadequate homogenization.
  • temperatures exceeding 535°C of the above-mentioned homogenized heat treatment increases a possibility of generation of burning. Therefore, a temperature of the above-mentioned homogenized heat treatment is set in a range of 500 - 535°C.
  • Temperature conditions of hot forging are important for manufacturing an Al alloy forged material with sufficient reproducibility according to designed high temperature characteristics.
  • well-known forging methods such as free forging and die forging (stretching forging)
  • a hot-forging temperature has been set about 380 - 430°C in order to obtain a microstructure having an equiaxial crystal grain after solution treatment of the Al alloy forged material, because there has been a recognition that a low hot-forging temperature tends to provide a locally mixed particle in the structure of the Al alloy forged material, leading to deterioration in high temperature characteristics.
  • hot-forging temperatures are preferably set in a range of 280 - 430°C, that is, below recrystallization temperatures. Hot-forging temperatures exceeding 430°C easily form coarse grains in Al alloy forged materials within a range of components of the present invention, which deteriorates the high temperature characteristics of the Al alloy forged materials, and disables manufacturing of Al alloy forged materials having excellent high temperature characteristics. On the other hand, hot-forging temperatures of less than 280°C tends to give a crack at the time of hot forging, and make the forging processing itself difficult.
  • the microstructures of the Al alloy forged materials are influenced by a forging ratio in the hot forging. Therefore, in order to obtain equiaxial crystal grain in the microstructures, preferably, a proper forging ratio for the hot forging is set preferably no less than 1.5 in the Al alloy forged materials. Forging ratios less than 1.5 easily provide mixed grains to structures of the Al alloy forged materials. More preferably, forging is performed not only in one direction but in at least two different directions, and forging ratios in each directions are set no less than 1.5.
  • solution treatment and hardening processing will be described. Processing is preferably performed within conditions specified in JIS H 4140, AMS-H -6088, etc. in order to transform soluble intermetallic compounds to solid solutions again and to suppress re-precipitation during cooling as much as possible in this solution treatment and hardening processing.
  • the heat treatment is performed based on standards of AMS-H-6088 etc.
  • solution treatment temperatures no more than minimum temperatures may not provide a proof stress of no less than 400 MPa at room temperatures after artificial ageing curing processing, and also make the solution treatment itself difficult. Therefore, a maximum of the solution treatment temperature is set 545°C, and a minimum is set 510°C.
  • artificial ageing curing processing is preferably performed after a solution treatment and a hardening processing to obtain thermally refined T6 materials.
  • a rate of compression is set to 1 - 5%.
  • Al alloy forged materials are processed to make application parts.
  • solution treatment, hardening processing, cold pressing, artificial ageing curing processing, etc. may suitably be performed.
  • furnaces used for thermal refining such as solution treatment and hardening processing
  • a batch type furnace, a continuous annealing furnace, a molten salt bath furnace, an oil furnace are suitably usable.
  • cooling methods for hardening methods, such as water immersion, warm water immersion, boiled water immersion, water injection, and air injection, may suitably be selected.
  • An average grain diameter of crystals of anAl alloy forged material of the present invention obtained in this way is no more than 1 mm, preferably in a range of 10 - 500 ⁇ m, and more preferably in a range of 50 - 300 ⁇ m, and the crystals are minute recrystallized grains (equiaxial recrystallized grain) having an almost fixed size.
  • the Al alloy forged material of the present invention obtained in this way has high temperature characteristics and machinability, such as excellent creep characteristics, and does not have groups obtained by aggregation of minute recrystallized grains (or subgrains) having grain diameters of no more than 1 ⁇ m as found in the above-mentioned mixed grain structure, coarse recrystallized grains having grain diameters of about several mm - several cm, or remaining ingots structures.
  • a structure of preferable equiaxial recrystallized grain in the present invention does not only necessarily represent a structure including 100% of equiaxial recrystallized grain having a fixed size, and allows intermixing of cast structures or mixed grain structures within a range in which high temperature characteristics, such as machinability, creep rupture strength, are not adversely affected.
  • high temperature characteristics such as machinability, creep rupture strength
  • existence in a dispersed state of single crystal grains of minute recrystallized grains (or subgrains) having grain diameters of no more than 1 ⁇ m does not deteriorate high temperature characteristics, such as the machinability, creep rupture strength.
  • a rate of area of aggregate of minute recrystallized grains having no more than 1 ⁇ m of diameter in the microstructure after solution treatment is preferably set no more than 10%.
  • sample is treated by a micro etching processing, such as electrolytic etching, and may be observed or measured with an optical microscope having 50 to 400 times of magnification.
  • a micro etching processing such as electrolytic etching
  • ⁇ ' phase is precipitated in a plane (100) of Al alloy, and ⁇ phase in a plane (111) under conditions selected from a range of 7 - 60 hours at 160 - 190°C in an artificial ageing curing processing after a solution treatment and a hardening processing. Missing of these precipitation by artificial ageing curing processing lowers a high temperature proof stress at temperatures of about 180°C, even when the artificial ageing curing processing is provided.
  • identification of a precipitation state of ⁇ ' phase and ⁇ phase in the Al alloy forged-material structure may be enabled by a structure observation using a transmission electron microscope (TEM) having 50000 times of magnification and, if necessary, using the above-mentioned EPMA.
  • TEM transmission electron microscope
  • a chemical component composition of the Al alloy of the present invention has fundamentally a component standard of Al alloys, such as 2519 or 2618, and 2519 (Ag) based Al alloy in which Ag is added into 2519, it may suitably be selected from a component composition range described below. First, elements positively included will be described.
  • Cu is a fundamental component of the present invention Al alloy forged material, and it demonstrates both functions of solid solution strengthening and precipitation strengthening, and furthermore it is indispensable in order to secure creep characteristics at normal temperatures and high temperatures, and a high temperature proof stress, and further a high temperature fatigue strength that is required mainly in applications of the Al alloy forged material of the present invention. More specifically, as mentioned above, Cu precipitates ⁇ ' phases and ⁇ phases in a plane (100) and a plane (111) of the Al alloy in a minute state with high density during a hot artificial ageing curing processing, improving a strength of the Al alloy forged material after the artificial ageing curing processing.
  • Mg as well as Cu demonstrates both function of solid solution strengthening and precipitation strengthening, and is indispensable in order to mainly secure sufficient creep characteristics at normal temperatures and high temperatures, and a high temperature proof stress, and also a high temperature fatigue strength of the Al alloy forged material. More specifically, Mg as well as Cu precipitates ⁇ ' phases and ⁇ phases in a plane (100) and a plane (111) of the Al alloy in a minute state and with high density during a hot artificial ageing curing processing, improving a strength of the Al alloy forged material after the artificial ageing curing processing.
  • V precipitates in forged material structures as Al-V based compounds and is indispensable element in order to improve a high temperature fatigue strength.
  • V precipitates Al-V based dispersed grains that are thermally stable compounds in the Al alloy forged material structures.
  • This precipitate has a function for disturbing grain boundary migration after recrystallization, and thus may demonstrate an effect of prevention of coarsening, that is refining a diameter of average crystal grain in a range of no more than 500 ⁇ m.
  • it forms fiber structures of microstructures of the Al alloy forged material, which improves a strength at normal temperatures, and a strength at high temperatures and particularly a high temperature fatigue strength.
  • V has comparatively small function for precipitating stable and coarse phase as compared with Zr, Cr, and Mn.
  • V is included in a range of 0.05% - 0.15%.
  • Zr, Cr, and Mn precipitate Al-Zr based, Al-Cr based, and Al-Mn based dispersed grains that are thermally stable compounds, respectively, in Al alloy forged material structures like the above-mentioned V at the time of homogenized heat-treatment. And this dispersed grains form fiber structures with microstructures of the Al alloy forged material, and has an effect for improving a strength at normal temperatures and a strength at high temperatures.
  • Fe is preferably regulated to no more than 0.15%. However, since contamination from scraps etc. is unavoidable and it is effective in improving high temperature characteristics of the Al alloy forgedmaterial, content of Fe up to 0.15% may be allowed. A content exceeding 0.15% forms insoluble intermetallic compounds, and tends to become defects of molding and of breakage.
  • Si combines with Mg to form Mg 1 Si and Al-Fe-Si based crystallized matter in the Al alloy forged material structure. Therefore, this Si precipitates ⁇ ' phases and ⁇ phases at the time of artificial ageing curing processing at high temperatures, and consumes Mg required for improving a strength of the Al alloy forged material after artificial ageing curing processing, which deteriorates a strength of the Al alloy after artificial ageing curing processing. Since Mg is originally included fewer as compared with Cu, this influence induced by the Si is significant. In addition, although most of the crystallized matter enters into solid solution state by the solution treatment, excessive formation of Mg 2 Si remains also in solution treatment, and forms starting points of fracture to deteriorate moldability. Therefore, Si is preferably regulated no more than 0.1%.
  • following elements in the Al alloy forged material are preferably regulated: Si: no more than 0.1%; Fe: no more than 0.15%; Zr: no more than 0.09%; Cr: no more than 0.05%; Mn: no more than 0.8%; and Ti: no more than 0.1%, respectively, in order to prevent deterioration of a proof stress after artificial ageing curing processing and a proof stress in use at high temperatures of an Al alloy forged material in a preferable embodiment of the present invention.
  • content may be allowed in a range that does not deteriorate high temperature characteristics or other characteristics of the Al alloy forged material concerning the present invention, or content about a maximum standard for 2000-series Aluminum.
  • Al alloy ingots 500 mm ⁇ ⁇ 2000 mml were ingoted that have mainly different V content as shown in Table 1, and that have chemical component compositions of A - C within a range of the present invention, and chemical component compositions of D and E outside of a range of the present invention, respectively. Subsequently, only processing periods were varied, as shown in Table 2, and homogenized heat treatment (air furnace) was performed at a temperature of 510°C.
  • ingots after the homogenized heat treatment were processed so that no less than 1.5 of forging ratios in all directions may be given to obtain square bars of 150 mm per side (thickness), and square bars of 80 mm per side (thickness) .
  • Those square bars were cut by a length of 300 mml, and Al alloy forged materials were manufactured.
  • the Al alloy forged materials were heated by a heating rate of 200°C / hr with air furnace, and after a solution treatment of 528°C ⁇ 6 hr, water hardening was performed at various hardening temperatures, respectively, shown in Table 2 (average cooling rate between 400°C and 290°C, more than 30000°C /minute) , and then they were taken out after maintenance underwater for 10 minutes.
  • Table 2 shows average distribution density measurement results of the Al-V based precipitates.
  • Examples 1 - 6 having chemical component compositions within the range of A-C including V of the present invention, and the samples have a distribution density of 1.5 piece/ ⁇ m 3 of Al-V based precipitate in a forged material structure.
  • a fatigue strength at room temperature and a fatigue strength at high temperature of no less than 8.0e6 (8.0 ⁇ 10 6 ) are shown, and it is clear that these are excellent in these physical properties.
  • Example 1 gives a comparatively higher distribution density of Al-V based precipitate in a forged material structure as compared with Example 2, as a result, it shows a comparatively excellent fatigue strength at high temperatures.
  • Comparative examples 7-10 in which short homogenized heat treatment time of 8 hours or 12 hours are adopted and alloys within a range of A-C shown in Table 1 of the present invention are used, they show notably lower distribution densities of less than 1. 5 piece/ ⁇ m 3 of Al-V based precipitate in the forged material structure as compared with the above-mentioned Examples, which shows that a fatigue strength particularly at high temperatures is markedly inferior.
  • Comparative example 11 in which an alloy example D having a V content lower than a limit is used shows a distribution density of less than 1.5 piece/ ⁇ m 3 , notably lower than in the above-mentioned Example, of Al-V based precipitate in the forged material structure in spite of 20 hours of long homogenized heat treatment period, which shows a markedly inferior fatigue strength particularly at high temperatures.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
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Claims (1)

  1. Aluminiumlegierungsschmiedematerial, umfassend: Cu: 4,0% - 7,0%, Mg: 0,2% - 0,4%, Ag: 0,05 - 0,7% und V: 0,05% - 0,15%, und gegebenenfalls: Si: nicht mehr als 0,1%, Fe: nicht mehr als 0,15%, Zr: nicht mehr als 0,09%, Cr: nicht mehr als 0,05%, Mn: nicht mehr als 0,8% und Ti: nicht mehr als 0,1%, wobei der Rest Al ist, wobei eine Verteilungsdichte von Ausscheidungen auf Al-V-Basis in der Struktur des Schmiedematerials nicht weniger als 1,5 Stück/µm3 beträgt, und wobei ein Kristallkorn des Aluminiumlegierungsschmiedematerials äquiaxial ist und ein mittlerer Korndurchmesser des Kristallkorns in einem Bereich von 10 bis 500 µm liegt.
EP20030021819 2003-09-26 2003-09-26 Geschmiedeter Aluminium Legierung, die ausgezeichnete Dauerfestigkeit Aufweist Expired - Lifetime EP1522600B1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP20030021819 EP1522600B1 (de) 2003-09-26 2003-09-26 Geschmiedeter Aluminium Legierung, die ausgezeichnete Dauerfestigkeit Aufweist
DE2003609711 DE60309711T2 (de) 2003-09-26 2003-09-26 Aluminiumlegierungsschmiedematerial mit ausgezeichneter Hochtemperaturermüdungsfestigkeit

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Application Number Priority Date Filing Date Title
EP20030021819 EP1522600B1 (de) 2003-09-26 2003-09-26 Geschmiedeter Aluminium Legierung, die ausgezeichnete Dauerfestigkeit Aufweist

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EP1522600B1 true EP1522600B1 (de) 2006-11-15

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Publication number Priority date Publication date Assignee Title
WO2008110270A1 (en) * 2007-03-09 2008-09-18 Aleris Aluminum Koblenz Gmbh Aluminium alloy having high- strength at elevated temperature
WO2011129431A1 (ja) * 2010-04-16 2011-10-20 昭和電工株式会社 アルミニウム合金鍛造部材の製造方法
US9163304B2 (en) 2010-04-20 2015-10-20 Alcoa Inc. High strength forged aluminum alloy products
CN103668017A (zh) * 2013-12-28 2014-03-26 无锡透平叶片有限公司 一种航空发动机铝合金叶片的锻造及热处理工艺
US20150322556A1 (en) 2014-05-06 2015-11-12 Goodrich Corporation Lithium free elevated temperature aluminum copper magnesium silver alloy for forged aerospace products
CN104259781B (zh) * 2014-09-19 2018-03-09 广西柳州银海铝业股份有限公司 货运火车车厢用铝合金板材的制造方法
JP2016079454A (ja) * 2014-10-16 2016-05-16 株式会社神戸製鋼所 アルミニウム合金鍛造材およびその製造方法

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CH668269A5 (de) * 1985-10-31 1988-12-15 Bbc Brown Boveri & Cie Aluminium-knetlegierung des typs al/cu/mg mit hoher festigkeit im temperaturbereich zwischen 0 und 250 c.
US5211910A (en) * 1990-01-26 1993-05-18 Martin Marietta Corporation Ultra high strength aluminum-base alloys
US5376192A (en) * 1992-08-28 1994-12-27 Reynolds Metals Company High strength, high toughness aluminum-copper-magnesium-type aluminum alloy
JPH11302764A (ja) * 1998-04-17 1999-11-02 Kobe Steel Ltd 高温特性に優れたアルミニウム合金
JP3997009B2 (ja) * 1998-10-07 2007-10-24 株式会社神戸製鋼所 高速動部品用アルミニウム合金鍛造材
JP2001181771A (ja) * 1999-12-20 2001-07-03 Kobe Steel Ltd 高強度耐熱アルミニウム合金材

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