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EP1111079A1 - Übersättigte Aluminium-Legierung - Google Patents

Übersättigte Aluminium-Legierung Download PDF

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Publication number
EP1111079A1
EP1111079A1 EP99125437A EP99125437A EP1111079A1 EP 1111079 A1 EP1111079 A1 EP 1111079A1 EP 99125437 A EP99125437 A EP 99125437A EP 99125437 A EP99125437 A EP 99125437A EP 1111079 A1 EP1111079 A1 EP 1111079A1
Authority
EP
European Patent Office
Prior art keywords
dispersoid
aluminum alloy
forming element
forming
alloy
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP99125437A
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English (en)
French (fr)
Inventor
Men Glenn Chu
Gregory J. Hildeman
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Alcoa Corp
Original Assignee
Alcoa Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Alcoa Corp filed Critical Alcoa Corp
Priority to EP99125437A priority Critical patent/EP1111079A1/de
Publication of EP1111079A1 publication Critical patent/EP1111079A1/de
Withdrawn legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—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

Definitions

  • This invention relates to the addition of alloying elements to aluminum alloys. More particularly, it relates to methods of adding alloying elements to molten aluminum to maintain high levels in solid solution.
  • dispersoid-forming elements such as Zr, Mn, Cr, V, Ti, Sc and Hf are used to increase recrystallization temperature and to control the grain structure in cast and wrought products.
  • Many different methods have been employed to add these types of alloying elements to molten metals.
  • master alloys which contain the desired elements are added directly to the melt in the forms of a cast lump, bar, waffle or added as briquettes composed of mixtures of aluminum and elemental powders or chips.
  • the alloying elements in the master alloys are normally present in a form of coarse intermetallics such as for example Al 3 Zr. These intermetallics require superheat and a long period of holding time to be dissolved in the melt. The heavy intermetallics also tend to settle to the bottom of the holding furnace due to gravity. Thus, master alloys are generally added in the melting or holding furnace to allow sufficient time for the intermetallics to dissolve in the superheated melt which is occasionally stirred.
  • the level of these desirable dispersoid-forming elements in the commercial aluminum alloys has been limited to the liquid solubility at peritectic reaction temperature.
  • the maximum liquid solubility of Zr, Cr, V and Hf is 0.12, 0.37, 0.2 and 0.2 wt.%, respectively.
  • these maximum limits of liquid solubility at peritectic temperatures will be reduced even further. Casting of aluminum alloys containing dispersoid elements at levels above their natural saturation limit can result in formation of undesirable coarse primary intermetallics in the molten metal.
  • coarse intermetallics are not filtered out of the molten metal, they will adversely affect the ability to cast the metal as well as the mechanical properties of the end product by reducing ductility, fracture toughness, or fatigue properties. Since coarse primary intermetallics can rapidly nucleate and grow in melts which exceed the maximum solubility limit, the conventional alloying approach is to add dispersoid-forming elements in the melting or holding furnace in amounts below the liquid saturation limit.
  • a fine grain unrecrystallized microstructure has a better combination of strength, elongation and toughness than a coarse grain recrystallized alloy.
  • a high volume fraction of fine dispersoids which are less than about 0.1 microns in size are useful for retaining a fine grain unrecrystallized microstructure.
  • Another object of the invention is to provide a method to increase the volume fraction of dispersoids formed by precipitating from a supersaturated solid solution.
  • Yet another object of the present invention is to provide a method for casting aluminum alloys with supersaturated levels of dispersoid-forming elements.
  • a process of achieving a high level of dispersoid-forming elements in solidified aluminum alloys by the addition of a supersaturated master alloy to a molten aluminum alloy which is immediately solidified comprises (a) forming a supersaturated master alloy containing dispersoid-forming elements in solid solution by rapidly solidifying a master alloy containing at least one dispersoid-forming element; (b) providing a body of molten aluminum alloy: (c) adding said rapidly solidified master alloy to the molten aluminum alloy at a rate sufficient to raise the wt.% of at least one dispersoid-forming element above its liquid saturation limit; and then (d) solidifying the molten aluminum alloy to form a solidified aluminum alloy possessing dispersoid-forming elements in solid solution above the liquid saturation limit.
  • a second aspect of the invention is a cast metal product in which the level of dispersoid-forming elements in solid solution is greater than the liquid saturation limit of the elements.
  • metal product is an aluminum alloy and the dispersoid-forming elements are zirconium (Zr), manganese (Mn), chromium (Cr), vanadium (V), titanium (Ti), scandium (Sc), niobium (Nb), yttrium (Y) and hafnium (Hf).
  • master alloy is used herein to mean an aluminum base alloy in remelt ingot form containing at least 50% aluminum and one or more added elements for use in making alloying additions.
  • master alloy is also used interchangeably in the art with the terms “rich alloy” and "hardener”.
  • dispersoid-forming elements is used herein to mean alloy elements that precipitate from solid solution to form intermetallic dispersoids in a base alloy.
  • examples of dispersoid-forming metals for aluminum alloys include, but are not limited to, manganese (Mn), zirconium (Zr), chromium (Cr), vanadium (V), titanium (Ti). scandium (Sc), hafnium (Hf), yttrium (Y) niobium (Nb) and combinations thereof.
  • Rapidly solidified is used herein to mean cooled from a liquid state into a solid state at rate of greater than about 100°C per second or preferably greater than about 1000°C per second. Rapidly solidified materials are preferably formed in the shape of thin ribbon, powder and flakes.
  • fine as it refers to intermetallic dispersoid particles which are precipitated from solid solution is a particle being less than about 0.1 microns.
  • continuous refers to the progressive and uninterrupted formation of a cast metal ingot in a mold which is open at both ends.
  • the pouring operation may continue indefinitely if the casting is cut into sections of suitable length at a location away from the mold. Alternatively, the pouring operation may be started and stopped in the manufacture of each casting. The latter process is commonly referred to as semi-continuous casting and is intended to be comprehended by the term "continuous”.
  • FIG. 1 there is illustrated a typical flow path for molten metal 10 from a furnace 12 to the casting mold 24 used for continuously casting ingots.
  • molten metal 10 is held at superheated temperatures in furnace 12. Alloying elements are typically added to furnace 12. Some of the alloying elements are added to the melt using master alloys that have high concentrations of alloying elements, that is, 10-15%. These alloying elements are normally present in a form of coarse intermetallics. These intermetallics require a long holding time in furnace 12 to be dissolved in the melt. The melt must also be stirred since the heavy intermetallics tend to settle to the bottom of the holding furnace due to gravity.
  • metal 10 is held in furnace 12 for several hours. During this time, coarse intermetallics are dissolved in the melt to form a liquid solution. Molten metal leaves furnace 12 via trough 14 and enters fluxing unit 16 to remove hydrogen, calcium and sodium by gas fluxing.
  • Flux unit 16 has impeller 17 for dispensing a flux gas. Impeller 17 is mounted on shaft 18. Impeller 17 is rotated, and simultaneously with the rotating, a fluxing gas is added to the molten aluminum adjacent the dispenser. Flux units are well known in the art.
  • baffle 19 After the molten metal travels beneath baffle 19, it then passes through a filter 20 under baffle 21 as it flows via trough 22 to casting mold 24 to form, in this case, ingot 26.
  • Mold 24 is a conventional direct chill casting apparatus and may be internally cooled, usually with a liquid coolant 27 such as water. Mold 24 is typically constructed of a material having high thermal conductivity, such as aluminum or copper, to insure that the coolant temperature is transferred as efficiently as possible through the inner mold wall to the metal to effect solidification.
  • Ingot 26 has a lower solidified section 28, a mushy region 30 and a molten pool 32 of aluminum above.
  • Molten metal pool 32 is supported by mold 24 incorporating cooling liquid 27.
  • Molten aluminum 12 is flowed to molten pool 32, and solidified ingot section 28 is removed from mold 24 at a controlled rate by the lowering of a bottom block (not shown).
  • dispersoid-forming elements can be added to the molten metal at levels above the natural solubility limit for the alloy without forming coarse primary aluminide intermetallic particles.
  • Figure 2 shows a rapidly solidified ribbon 40 of the material containing a dispersoid-forming element being added directly into molten metal pool 32 of ingot 26.
  • Ribbon 40 is fed from spool 42 into a fixture 44 for directing the ribbon into the molten pool.
  • the residence time between melting of ribbon 40 and solidification of the supersaturated alloy contained in molten metal pool 32 is sufficiently short as to permit dissolution of the master alloy ribbon containing at least one dispersoid-forming element in solid solution and subsequent freezing of the molten metal at the bottom of the crater without growing into larger particles, thereby maintaining high levels of dispersoid-forming elements in solid solution in the solidified ingot.
  • the supersatured liquid solution which is produced by the dispersoid-forming element is distributed uniformly in the pool of molten aluminum.
  • the residence time of the dispersoid-forming element in the crater is short since the metal is immediately solidified into ingot.
  • the ribbon may be comprised of 2.0 wt.% Zr or higher, the remainder aluminum.
  • the feed rate of the ribbon can be controlled to provide the desired amount of Zr in the ingot.
  • the ribbon when the ribbon is formed from a melt of aluminum and zirconium, it may be cast onto a roll or drum where fast solidification occurs to freeze Zr in the aluminum ribbon as a solid solution.
  • Melt spun ribbon having a composition of Al-6% Zr was formed using standard rapid solidification techniques.
  • the ribbon was 0.009 inch thick and 1 inch wide.
  • the ribbon was continuously fed into a pool of molten alloy 7150 at the casting head of a DC ingot.
  • the ribbon was added to the melt at rate of 1000 inches per minute.
  • the 7150 alloy from the furnace had a Zr level of just below its natural solubility limit of 0.12% to avoid formation of coarse Zr intermetallics in the ingot.
  • the continuous addition of the ribbon to the molten melt in the pool enables the Zr concentration to be increased above the solubility limit.
  • the ingot was analyzed and the level of Zr in the cast ingot was measured to be at 0.21%.
  • the as-cast grain size of the ingot was found to be approximately 5 times smaller than the grain size of AA7150 ingot containing Zr levels approaching its natural solubility limit of 0.12%.
  • metal casting and “solidifying” are intended to include metal casting techniques used in any of the commercial solidification processes, including continuous casting, semi-continuously casting by the direct chill method, as well as strip or slab cast continuously by belts, block or roll casters.
  • the invention may be used in other solidification processes such as spray forming, spray casting, atomization, rapid solidification, and splating.
  • the present invention will also be valuable in producing products made of other aluminum alloys containing about 75% or more by weight of aluminum and one or more alloying elements.
  • suitable alloying elements is at least one element selected from the group of essentially character-forming alloying elements consisting of manganese, zinc, lithium, copper, silicon, and magnesium. These alloying elements are essentially character forming for the reason that the contemplated alloys containing one or more of them essentially derive their characteristic properties from such elements.
  • the amounts of each of the elements which impart such characteristics are, as to each of magnesium and copper, about 0.5 to about 10 wt.% of the total alloy if the element is present as an alloying element in the alloy; as to the element zinc, about 0.05 to about 12.0% of the total alloy if such element is present as an alloying element; as to the element lithium, about 0.2 to about 3.0% of the total alloy if such element is present as an alloying element; and as to the element manganese, if it is present as an alloying element, usually about 0.15 to about 2.0% of the total alloy.
  • the elements iron and silicon while perhaps not entirely or always accurately classifiable as essentially character-forming alloy elements, are often present in aluminum alloys in appreciable quantities and can have a marked effect upon the derived characteristic properties of certain alloys containing the same.
  • Iron for example. which if present and generally considered as an undesired impurity, is sometimes desirably adjusted in amounts of about 0.3 to 2.0 wt.% of the total alloy to perform specific functions in certain alloys.
  • Silicon may also be so considered, and while found in a range varying from about 0.05 to as much as 20% in casting alloys, is desirably added in the range of about 0.3 to 1.5% to perform specific functions in certain alloys.
  • the elements iron and silicon may, at least when desirably present in character-affecting amounts in certain alloys, be properly also considered as character-forming alloying ingredients.
  • aluminum alloys 2014, 2024, 6061, 7050, 7150 , 7055 and 7075 are the aluminum alloys 2014, 2024, 6061, 7050, 7150 , 7055 and 7075. These aluminum alloys generally include the generic designation 2000 series alloys, 5000 series alloys, 6000 series alloys, 7000 series alloys, and 8000 series alloys.
  • dispersoid-forming elements may also be alloyed into the molten metal in the trough adjacent the ingot that is being cast. The key is to alloy the dispersoid-forming element above the liquid saturation limit at a point in the process where there is insufficient time for the dispersoid-forming element to form large particles in the solidified metal.
  • the invention has been described in terms of alloying a single'dispersoid-forming element at supersatured levels, it will be apparent to those skilled in the art that the same technique can be use for creating a product with multiple dispersoid-forming elements at supersatured levels.
  • the same technique can be used to create supersatured levels of any combination of manganese, chromium, vanadium, titanium, scandium, hafnium, yttrium, niobium, and zirconium.
  • the invention has been described in terms of casting ingot, the invention is not intended to be so limited and applies to all forms of casting.
  • the invention is intended to be equally applicable to products such as sheet, plate, wire, rod, bar, forging or extrusions. It is contemplated that the invention will be especially useful for tubular sporting goods products such as ball bats, lacrosse sticks, hockey sticks, polo sticks, field hockey sticks, ice hockey sticks, pool cues, arrows, gun scopes, wind surfing frames, sail board booms, inline skate components, wheelchairs, golf club shafts, bicycle frames and components such as handlebars, seat posts and suspension systems, ski poles, javelins, bowling pins and the like.
  • Vehicular panels are described in U.S. Patent 4,082,578, incorporated herein by reference, and include floor panels, side panels, or other panels for cars, trucks, trailers, railroad vehicles and canoe or boat panels, aerospace panels and other shaped sheet and extrusion members, forgings and other members such as, for example, drive shafts.
  • the improved aluminum extrusion, pipe and tube stock made in accordance with the present invention will be especially useful in automotive and aerospace applications.
  • the aerospace applications include airplane wing and fuselage structural members such as, for example, stringer extrusions.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Continuous Casting (AREA)
EP99125437A 1999-12-20 1999-12-20 Übersättigte Aluminium-Legierung Withdrawn EP1111079A1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP99125437A EP1111079A1 (de) 1999-12-20 1999-12-20 Übersättigte Aluminium-Legierung

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Application Number Priority Date Filing Date Title
EP99125437A EP1111079A1 (de) 1999-12-20 1999-12-20 Übersättigte Aluminium-Legierung

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Cited By (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1728881A3 (de) * 2005-05-31 2007-02-21 United Technologies Corporation Hochtemperatur-Legierungen auf Aluminiumbasis
US7871477B2 (en) 2008-04-18 2011-01-18 United Technologies Corporation High strength L12 aluminum alloys
US7875133B2 (en) 2008-04-18 2011-01-25 United Technologies Corporation Heat treatable L12 aluminum alloys
US7875131B2 (en) 2008-04-18 2011-01-25 United Technologies Corporation L12 strengthened amorphous aluminum alloys
US7879162B2 (en) 2008-04-18 2011-02-01 United Technologies Corporation High strength aluminum alloys with L12 precipitates
US7909947B2 (en) 2008-04-18 2011-03-22 United Technologies Corporation High strength L12 aluminum alloys
US8002912B2 (en) 2008-04-18 2011-08-23 United Technologies Corporation High strength L12 aluminum alloys
US8017072B2 (en) 2008-04-18 2011-09-13 United Technologies Corporation Dispersion strengthened L12 aluminum alloys
RU2458170C1 (ru) * 2011-01-31 2012-08-10 Общество с ограниченной ответственностью "Объединенная Компания РУСАЛ Инженерно-технологический центр" Алюминиевый сплав
US8409496B2 (en) 2009-09-14 2013-04-02 United Technologies Corporation Superplastic forming high strength L12 aluminum alloys
US8409373B2 (en) 2008-04-18 2013-04-02 United Technologies Corporation L12 aluminum alloys with bimodal and trimodal distribution
US8409497B2 (en) 2009-10-16 2013-04-02 United Technologies Corporation Hot and cold rolling high strength L12 aluminum alloys
RU2480852C2 (ru) * 2011-01-17 2013-04-27 Закрытое акционерное общество "Москабельмет" Катанка из алюминиевого сплава
US8728389B2 (en) 2009-09-01 2014-05-20 United Technologies Corporation Fabrication of L12 aluminum alloy tanks and other vessels by roll forming, spin forming, and friction stir welding
US8778099B2 (en) 2008-12-09 2014-07-15 United Technologies Corporation Conversion process for heat treatable L12 aluminum alloys
US8778098B2 (en) 2008-12-09 2014-07-15 United Technologies Corporation Method for producing high strength aluminum alloy powder containing L12 intermetallic dispersoids
RU2538247C1 (ru) * 2013-10-24 2015-01-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "МАТИ-Российский государственный технологический университет имени К.Э. Циолковского" Литейный композиционный материал на основе алюминия и его сплавов
RU2538246C1 (ru) * 2013-10-24 2015-01-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "МАТИ-Российский государственный технологический университет имени К.Э. Циолковского" Способ получения литейного композиционного материала на основе алюминия и его сплавов
US9127334B2 (en) 2009-05-07 2015-09-08 United Technologies Corporation Direct forging and rolling of L12 aluminum alloys for armor applications
US9194027B2 (en) 2009-10-14 2015-11-24 United Technologies Corporation Method of forming high strength aluminum alloy parts containing L12 intermetallic dispersoids by ring rolling
DE102015200632A1 (de) 2015-01-16 2016-07-21 Federal-Mogul Nürnberg GmbH Verfahren zur Herstellung eines Motorbauteils, Motorbauteil und Verwendung eines Kornfeiners zur Herstellung eines Motorbauteils
CN106282696A (zh) * 2015-05-19 2017-01-04 沈阳万龙源冶金新材料科技有限公司 一种高强高韧铝合金
US9611522B2 (en) 2009-05-06 2017-04-04 United Technologies Corporation Spray deposition of L12 aluminum alloys
WO2023198788A1 (en) 2022-04-12 2023-10-19 Nano Alloys Technology Method for producing a solidified lightweight aluminium or magnesium alloy

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3634075A (en) * 1969-01-15 1972-01-11 Kawecki Berylco Ind Introducing a grain refining or alloying agent into molten metals and alloys
US3991810A (en) * 1974-07-15 1976-11-16 Caterpillar Tractor Co. Method and apparatus for introducing additives into a casting mold
EP0185540A2 (de) * 1984-12-18 1986-06-25 Sumitomo Light Metal Industries Limited Verfahren zur Kornfeinung des primären Siliziums in hypereutektischen Al-Si-Legierungen
EP0244255A1 (de) * 1986-05-01 1987-11-04 Alform Alloys Limited Kontinuierliche Herstellung von Legierungen
GB2243617A (en) * 1990-03-09 1991-11-06 Masumoto Tsuyoshi High strength amorphous alloy
EP0564814A2 (de) * 1992-02-28 1993-10-13 Ykk Corporation Verdichteter und verfestigter Werkstoff aus einer hochfesten, hitzebeständigen Legierung auf Aluminiumbasis und Verfahren zu seiner Herstellung
WO1995005490A1 (de) * 1993-08-13 1995-02-23 Schaedlich Stubenrauch Juergen Schmelzebehandlungsmittel, seine herstellung und verwendung
EP0796925A1 (de) * 1996-03-29 1997-09-24 Ykk Corporation Hochfeste und hochduktile Legierung auf Aluminiumbasis
EP0875593A1 (de) * 1997-04-30 1998-11-04 Sumitomo Electric Industries, Ltd. Aluminium-Legierung und Verfahren zu ihrer Herstellung

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3634075A (en) * 1969-01-15 1972-01-11 Kawecki Berylco Ind Introducing a grain refining or alloying agent into molten metals and alloys
US3991810A (en) * 1974-07-15 1976-11-16 Caterpillar Tractor Co. Method and apparatus for introducing additives into a casting mold
EP0185540A2 (de) * 1984-12-18 1986-06-25 Sumitomo Light Metal Industries Limited Verfahren zur Kornfeinung des primären Siliziums in hypereutektischen Al-Si-Legierungen
EP0244255A1 (de) * 1986-05-01 1987-11-04 Alform Alloys Limited Kontinuierliche Herstellung von Legierungen
GB2243617A (en) * 1990-03-09 1991-11-06 Masumoto Tsuyoshi High strength amorphous alloy
EP0564814A2 (de) * 1992-02-28 1993-10-13 Ykk Corporation Verdichteter und verfestigter Werkstoff aus einer hochfesten, hitzebeständigen Legierung auf Aluminiumbasis und Verfahren zu seiner Herstellung
WO1995005490A1 (de) * 1993-08-13 1995-02-23 Schaedlich Stubenrauch Juergen Schmelzebehandlungsmittel, seine herstellung und verwendung
EP0796925A1 (de) * 1996-03-29 1997-09-24 Ykk Corporation Hochfeste und hochduktile Legierung auf Aluminiumbasis
EP0875593A1 (de) * 1997-04-30 1998-11-04 Sumitomo Electric Industries, Ltd. Aluminium-Legierung und Verfahren zu ihrer Herstellung

Cited By (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7875132B2 (en) 2005-05-31 2011-01-25 United Technologies Corporation High temperature aluminum alloys
EP1728881A3 (de) * 2005-05-31 2007-02-21 United Technologies Corporation Hochtemperatur-Legierungen auf Aluminiumbasis
US8409373B2 (en) 2008-04-18 2013-04-02 United Technologies Corporation L12 aluminum alloys with bimodal and trimodal distribution
US8017072B2 (en) 2008-04-18 2011-09-13 United Technologies Corporation Dispersion strengthened L12 aluminum alloys
US7875131B2 (en) 2008-04-18 2011-01-25 United Technologies Corporation L12 strengthened amorphous aluminum alloys
US7879162B2 (en) 2008-04-18 2011-02-01 United Technologies Corporation High strength aluminum alloys with L12 precipitates
US7883590B1 (en) 2008-04-18 2011-02-08 United Technologies Corporation Heat treatable L12 aluminum alloys
US7909947B2 (en) 2008-04-18 2011-03-22 United Technologies Corporation High strength L12 aluminum alloys
US7871477B2 (en) 2008-04-18 2011-01-18 United Technologies Corporation High strength L12 aluminum alloys
US8002912B2 (en) 2008-04-18 2011-08-23 United Technologies Corporation High strength L12 aluminum alloys
US7875133B2 (en) 2008-04-18 2011-01-25 United Technologies Corporation Heat treatable L12 aluminum alloys
US8778099B2 (en) 2008-12-09 2014-07-15 United Technologies Corporation Conversion process for heat treatable L12 aluminum alloys
US8778098B2 (en) 2008-12-09 2014-07-15 United Technologies Corporation Method for producing high strength aluminum alloy powder containing L12 intermetallic dispersoids
US9611522B2 (en) 2009-05-06 2017-04-04 United Technologies Corporation Spray deposition of L12 aluminum alloys
US9127334B2 (en) 2009-05-07 2015-09-08 United Technologies Corporation Direct forging and rolling of L12 aluminum alloys for armor applications
US8728389B2 (en) 2009-09-01 2014-05-20 United Technologies Corporation Fabrication of L12 aluminum alloy tanks and other vessels by roll forming, spin forming, and friction stir welding
US8409496B2 (en) 2009-09-14 2013-04-02 United Technologies Corporation Superplastic forming high strength L12 aluminum alloys
US9194027B2 (en) 2009-10-14 2015-11-24 United Technologies Corporation Method of forming high strength aluminum alloy parts containing L12 intermetallic dispersoids by ring rolling
US8409497B2 (en) 2009-10-16 2013-04-02 United Technologies Corporation Hot and cold rolling high strength L12 aluminum alloys
RU2480852C2 (ru) * 2011-01-17 2013-04-27 Закрытое акционерное общество "Москабельмет" Катанка из алюминиевого сплава
RU2458170C1 (ru) * 2011-01-31 2012-08-10 Общество с ограниченной ответственностью "Объединенная Компания РУСАЛ Инженерно-технологический центр" Алюминиевый сплав
RU2538246C1 (ru) * 2013-10-24 2015-01-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "МАТИ-Российский государственный технологический университет имени К.Э. Циолковского" Способ получения литейного композиционного материала на основе алюминия и его сплавов
RU2538247C1 (ru) * 2013-10-24 2015-01-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "МАТИ-Российский государственный технологический университет имени К.Э. Циолковского" Литейный композиционный материал на основе алюминия и его сплавов
DE102015200632A1 (de) 2015-01-16 2016-07-21 Federal-Mogul Nürnberg GmbH Verfahren zur Herstellung eines Motorbauteils, Motorbauteil und Verwendung eines Kornfeiners zur Herstellung eines Motorbauteils
CN106282696A (zh) * 2015-05-19 2017-01-04 沈阳万龙源冶金新材料科技有限公司 一种高强高韧铝合金
WO2023198788A1 (en) 2022-04-12 2023-10-19 Nano Alloys Technology Method for producing a solidified lightweight aluminium or magnesium alloy

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