EP0584596A2 - Rostfeste und hochfeste Aluminiumlegierung - Google Patents

Rostfeste und hochfeste Aluminiumlegierung Download PDF

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Publication number
EP0584596A2
EP0584596A2 EP93112487A EP93112487A EP0584596A2 EP 0584596 A2 EP0584596 A2 EP 0584596A2 EP 93112487 A EP93112487 A EP 93112487A EP 93112487 A EP93112487 A EP 93112487A EP 0584596 A2 EP0584596 A2 EP 0584596A2
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EP
European Patent Office
Prior art keywords
aluminum
alloy
duc
fcc
based 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Withdrawn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
EP93112487A
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English (en)
French (fr)
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EP0584596A3 (en
Inventor
Tsuyoshi Masumoto
Akihisa Inoue
Yuma C/O Yamaha Corporation Horio
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.)
INOUE, AKIHISA
MASUMOTO, TSUYOSHI
Yamaha Corp
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Yamaha Corp
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Publication date
Priority claimed from JP4209116A external-priority patent/JP2941571B2/ja
Priority claimed from JP4209115A external-priority patent/JP2583718B2/ja
Priority claimed from JP5041528A external-priority patent/JP2703480B2/ja
Application filed by Yamaha Corp filed Critical Yamaha Corp
Publication of EP0584596A2 publication Critical patent/EP0584596A2/de
Publication of EP0584596A3 publication Critical patent/EP0584596A3/en
Withdrawn legal-status Critical Current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
    • C22C45/00—Amorphous alloys
    • C22C45/08—Amorphous alloys with aluminium as the major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium

Definitions

  • the present invention relates to an aluminum-based alloy for use in a wide range of applications such as in aircraft, vehicles and ships, as well as, in the structural material for the engine portions thereof.
  • the present invention may be employed as sash, roofing material and exterior material for use in construction, or as material for use in sea water equipment, nuclear reactors, and the like.
  • alloys incorporating various components such as Al-Cu, Al-Si, Al-Mg, Al-Cu-Si, Al-Cu-Mg, and Al-Zn-Mg are known.
  • superior anti-corrosive properties are obtained at a light weight, and thus the aforementioned alloys are being widely used as structural material for machines in vehicles, ships and aircraft, in addition to being employed as sash, roofing material, exterior material for use in construction, structural material for use in LNG tanks, and the like.
  • the prior art aluminum-based alloys generally exhibit disadvantages such as a low hardness and poor heat resistance when compared to material incorporating Fe.
  • some materials have incorporated elements such as Cu, Mg and Zn for increased hardness, disadvantages remain such as low anti-corrosive properties.
  • an aluminum-based alloy which can be utilized as material with a high hardness, high strength, high electrical resistance, anti-abrasion properties, or as soldering material.
  • the disclosed aluminum-based alloy has a superior heat resistance, and may undergo extruding or press processing by utilizing the superplastic phenomenon observed near liquid crystallization temperatures.
  • This aluminum-based alloy comprises a composition A1M*X with a special composition ratio (wherein M* signifies an element such as V, Cr, Mn, Fe, Co, Ni, Cu, Zr and the like, and X represents a rare earth element such as La, Ce, Sm and Nd, or an element such as Y, Nb, Ta, Mm (misch metal) and the like), and has an amorphous or a combined amorphous/fine crystalline structure.
  • M* signifies an element such as V, Cr, Mn, Fe, Co, Ni, Cu, Zr and the like
  • X represents a rare earth element such as La, Ce, Sm and Nd, or an element such as Y, Nb, Ta, Mm (misch metal) and the like
  • this aluminum-based alloy is disadvantageous in that high costs result from the incorporation of large amounts of expensive rare earth elements and/or metal elements with a high activity such as Y. Namely, in addition to the aforementioned use of expensive raw materials, problems also arise such as increased consumption and labor costs due to the large scale of the manufacturing facilities required to treat materials with high activities. Furthermore, the aforementioned aluminum-based alloy tends to display insufficient restance to oxidation and corrosion.
  • the first preferred embodiment of the present invention provides an aluminum-based alloy, essentially consisting of an amorphous structure or a multiphase amorphous/fine crystalline structure, represented by the general formula Al x M y R z (wherein M is at least one metal element selected from the group consisting of Ti, V, Cr, Mn, Fe, Co, Cu, Zr, Nb, Mo and Ni, and R is at least one element or mixture selected from the group consisting of Y, Ce, La, Nd and Mm (misch metal)).
  • the second preferred embodiment of the present invention provides an aluminum-based alloy, essentially consisting of an amorphous structure or a multiphase amorphous/fine crystalline structure, represented by the general formula Al x Ni y M' z (wherein M' is at least one metal element selected from the group consisting of Ti, V, Mn, Fe, Co, Cu and Zr).
  • M' is at least one metal element selected from the group consisting of Ti, V, Mn, Fe, Co, Cu and Zr.
  • the fine crystalline component of the multiphase structure described in the aforementioned first and second embodiments comprises at least one phase selected from the group consisting of an aluminum phase, a stable or metastable intermetallic compound phase, and a metal solid solution comprising an aluminum matrix.
  • the individual crystal diameter of this fine crystalline component is approximately 30 to 50 nm.
  • the fourth preferred embodiment of the present invention provides an aluminum-based alloy represented by the general formula Al x Co y M'' z (wherein M'' is at least one metal element selected from the group consisting of Mn, Fe and Cu).
  • the fifth preferred embodiment of the present invention provides an aluminum-based alloy represented by the general formula Al a Fe b L c (wherein L is at least one metal element selected from the group consisting of Mn and Cu).
  • the sixth preferred embodiment of the present invention substitutes Ti or Zr in place of element M'' or L, in an amount corresponding to one-half or less of the atomic percentage of M'' or L.
  • the atomic percentages of Al, element M, and element R are restricted to 64.5 - 95%, 0.5 - 35% and 0 - 0.5% respectively.
  • Element M which represents one or more metal elements selected from the group consisting of Ti, V, Cr, Mn, Fe, Co, Cu, Zr, Nb, Mo and Ni, coexists with R and improves the amorphous forming properties, as well as, raising the crystallization temperature of the amorphous phase. Most importantly, this element markedly improves the hardness and strength of the amorphous phase.
  • these elements also stabilize the fine crystalline phase, form stable or metastable intermetallic compounds with aluminum or other additional elements, distperse uniformly in the aluminum matrix ( ⁇ -phase), phenomenally increase the hardness and strength of the alloy, suppress coarsening of the fine crystal at high temperatures, and impart a resistance to heat.
  • an atomic percentage for element M of less than 0.5% is undesirable, as this reduces the strength and hardness of the alloy.
  • an atomic percentage exceeding 35% is also undesirable as this results in intermetallic compounds forming easily, which in turn lead to embrittlement of the alloy.
  • Element R is one or more elements selected from the group consisting of Y, Ce, La, Nd and Mm (misch metal).
  • a misch metal mainly comprises La and/or Ce, and may also include additional complexes incorporating other rare earth metals, excluding the aforementioned La and Ce, as well as, unavoidable impurities (Si, Fe, Mg, etc.).
  • element R enhances the amorphous forming properties, and also raises the crystallization temperature of the amorphous phase. In this manner, the anti-corrosive properties can be improved, and the amorphous phase can be stabilized up to a high temperature.
  • element R coexists with element M, and stabilizes the fine crystalline phase.
  • the atomic percentages of Al, Ni, and element M' are restricted to 50 - 95%, 0.5 - 35% and 0.5 - 20% respectively.
  • An atomic percentage for Al of less than 50% is undesirable, as this results in significant embrittlement of the alloy.
  • an atomic percentage for Al exceeding 95% is also undesirable, as this results in reduction of the strength and hardness of the alloy.
  • the atomic percentage for Ni is within the range of 0.5 - 35%. If the incorporated amount of Ni is less than 0.5%, the strength and hardness of the alloy are reduced. On the other hand, an atomic percentage exceeding 35% results in intermetallic compounds forming easily, which in turn leads to embrittlement of the alloy. Thus both of these situations are undesirable.
  • the atomic percentage for element M' lies within the range of 0.5 - 20%.
  • the strength and hardness of the alloy are reduced.
  • an atomic percentage exceeding 20% results in embrittlement of the alloy. Both of these situations are likewise undesirable.
  • Element M' coexists with other elements, and improves the amorphous forming properties, in addition to raising the crystallization temperature of the amorphous phase. Most importantly, this element phenomenally improves the hardness and strength of the amorphous phase. As well, under the fine crystal manufacturing conditions, element M' also stabilizes the fine crystalline phase, forms stable or metastable intermetallic compounds with aluminum or other additional elements, disperses uniformly in the aluminum matrix ( ⁇ -phase), phenomenally increases the hardness and strength of the alloy, suppresses coarsening of the fine crystal at high temperatures, and imparts a resistance to heat.
  • the aforementioned aluminium-based alloys according to the present invention represented by the formulae Al x Co y M'' z and Al a Fe b L c , by adding predetermined amounts of Co and/or Fe to Al, the effect of quenching is enhanced, the amorphous and fine crystalline phases are more easily obtained, and the thermal stability of the overall structure is improved. In addition, the strength and hardness of the resulting alloy are also increased.
  • the effect of quenching is enhanced, the amorphous and fine crystalline phases are more easily obtained, and the thermal stability of the overall structure is improved.
  • the atomic percentage of Al is in the 50 - 95% range.
  • An atomic percentage for Al of less than 50% is undesirable, as this results in embrittlement of the alloy.
  • an atomic percentage for Al exceeding 95% is also undesirable, as this results in reduction of the strength and hardness of the alloy.
  • the atomic percentage of Co and/or Fe lies in the 0.5 - 35% range.
  • the strength and hardness are not improved, while, on the other hand, when this atomic percentage exceeds 35%, embrittlement is observed, and the strength and toughness are reduced.
  • embrittlement of the alloy begins to occur.
  • the atomic percentage of Mn (manganese) and/or Cu (copper) lies in the 0.5 - 20% range.
  • Mn manganese
  • Cu copper
  • the atomic percentage of Ti (titanium) and/or Zr (zirconium) lies in the range of up to one-half the atomic percentage of element M'' or L.
  • the quench effect is not improved, and, in the case when a crystalline state is incorporated into the alloy composition, the crystalline grains are not finely crystallized.
  • this atomic percentage exceeds 10%, embrittlement occurs, and toughness is reduced.
  • the melting point rises, and melting become difficult to achieve.
  • the viscosity of the liquid-melt increases, and thus, at the time of manufacturing, it becomes difficult to discharge this liquid-melt from the nozzle.
  • All of the aforementioned aluminum-based alloys according to the present invention can be manufactured by quench solidification of the alloy liquid-melts having the aforementioned compositions using a liquid quenching method.
  • This liquid quenching method essentially entails rapid cooling of the melted alloy.
  • Single roll, double roll, and submerged rotational spin methods have proved to be particularly effective.
  • a cooling rate of 104 to 106 K/sec is easily obtainable.
  • the liquid-melt is first poured into a storage vessel such as a silica tube, and then discharged, via a nozzle aperture at the tip of the silica tube, towards a copper roll of diameter 30 to 300 mm, which is rotating at a fixed velocity in the range of 300 to 1000 rpm.
  • a storage vessel such as a silica tube
  • a nozzle aperture at the tip of the silica tube towards a copper roll of diameter 30 to 300 mm, which is rotating at a fixed velocity in the range of 300 to 1000 rpm.
  • fine wire-thin material can be easily obtained through the submerged rotational spin method by discharging the liquid-melt in order to quench it, via the nozzle aperture, into a refrigerant solution layer of depth 1 to 10 cm, maintained by means of centrifugal force inside an air drum rotating at 50 to 500 rpm, under argon gas back pressure.
  • the angle between the liquid-melt discharged from the nozzle, and the refrigerant surface is preferably 60 to 90°C, and the relative velocity ratio of the the liquid-melt and the refrigerant surface is preferably 0.7 to 0.9.
  • thin layers of aluminum-based alloy of the aforementioned compositions can also be obtained without using the above methods, by employing layer formation processes such as the sputtering method.
  • aluminum alloy powder of the aforementioned compositions can be obtained by quenching the liquid-melt using various atomizer and spray methods such as a high pressure gas spray method.
  • the fine crystalline phase of the present invention represents a crystalline phase in which the crystal particles have an average maximum diameter of 1 ⁇ m.
  • An alloy of the structural state (amorphous phase) described in (1) above has a high strength, superior bending ductility, and a high toughness.
  • Alloys possessing the structural phases (multiphase structures) described in (2) and (3) above have a high strength which is greater than that of the alloys of (amorphous) structural state (1) by a factor of 1.2 to 1.5.
  • Alloys possessing the structural phases (multiphase structure and solid solution) described in (4) and (5) above have a greater toughness and higher strength than that of the alloys of structural states (1), (2) and (3).
  • Each of the aforementioned structural states can be determined by a normal X-ray diffraction method or by observation using a transmission electron microscope.
  • a halo pattern characteristic of this amorphous phase is evident.
  • a diffraction pattern formed from a halo pattern and characteristic diffraction peak, attributed to the fine crystalline phase is displayed.
  • a pattern formed from a halo pattern and characteristic diffraction peak, attributed to the intermetallic compound phase is displayed.
  • amorphous and fine crystalline substances as well as, amorphous/fine crystalline complexes can be obtained by means of various methods such as the aforementioned single and double roll methods, submerged rotational spin method, sputtering method, various atomizer methods, spray method, mechanical alloying method and the like.
  • the amorphous/fine crystalline multiphase can be obtained by selecting the appropriate manufacturing conditions as necessary.
  • any of the structural states described in (1) to (3) above can be obtained.
  • any of the structural states described in (4) and (5) can be obtained.
  • the aforementioned amorphous phase structure is heated above a specific temperature, it decomposes to form crystal.
  • This specific temperature is referred to as the crystallization temperature.
  • the aluminum-based alloy of the present invention displays superiplasticity at temperatures near the crystallization temperature (crystallization temperature ⁇ 100°C), as well as, at the high temperatures within the fine crystalline stable temperature range, and thus processes such as extruding, pressing and hot forging can easily be performed. Consequently, aluminum-based alloys of the above-mentioned compositions obtained in the aforementioned thin tape, wire, plate and/or powder states can be easily formed into bulk materials by means of extruding, pressing and hot forging processes at the aforementioned temperatures. Furthermore, the aluminum-based alloys of the aforementioned compositions possess a high ductility, thus bending of 180° is also possible.
  • the aluminum-based alloys having an amorphous phase or an amorphous/fine crystalline multiphase structure according to the present invention do not display structural or chemical non-uniformity of crystal grain boundary, segregation and the like, as seen in crystalline alloys. These alloys cause passivation due to formation of an aluminum oxide layer, and thus display a high resistance to corrosion.
  • the tape alloy manufactured by means of the aforementioned quench process is pulverized in a ball mill, and then powder pressed in a vacuum hot press under vacuum (e.g. 10 ⁇ 3 Torr) at a temperature slightly below the crystallization temperature (e.g. approximately 470K), thereby forming a billet for use in extruding with a diameter and length of several centimeters.
  • This billet is set inside a container of an extruder, and is maintained at a temperature slightly greater than the crystallization temperature for several tens of minutes. Extruded materials can then be obtained in desired shapes such as round bars, etc. by extruding.
  • the aluminum-based alloy according to the present invention is useful as materials with a high strength, hardness and resistance to corrosion. Furthermore, it is possible to improve the mechanical properties by heat treatment; this alloy also stands up well to bending, and thus possesses superior properties such as the ability to be mechanically processed.
  • the aluminum-based alloys according to the present invention can be used in a wide range of applications such as in aircraft, vehicles and ships, as well as, in the structural material for the engine portions thereof.
  • the aluminum-based alloys of the present invention may also be employed as sash, roofing material and exterior material for use in construction, or as material for use in sea water equipment, nuclear reactors, and the like.
  • Fig. 1 shows a construction of an example of a single roll apparatus used at the time of manufacturing a tape of an alloy of the present invention following quench solidification.
  • Fig. 2 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al88Ni 11.6 Ce 0.4 .
  • Fig. 3 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 89.7 Ni5Fe5Ce 0.3 .
  • Fig. 4 shows the thermal properties of an alloy having the composition of Al 89.6 Ni5Co5Ce 0.4 .
  • Fig. 5 shows the thermal properties of an alloy having the composition of Al88Ni 11.6 Y 0.4 .
  • Fig. 6 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al87Ni12Mn1.
  • Fig. 7 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al88Ni9Co3.
  • Fig. 8 shows the thermal properties of an alloy having the composition of Al88Ni11Zr1.
  • Fig. 9 shows the thermal properties of an alloy having the composition of Al88Ni11Fe1.
  • Fig. 10 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al89Co8Mn3.
  • Fig. 11 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al90Co6Fe4.
  • Fig. 12 shows the thermal properties of an alloy having the composition of Al90Co9Cu1.
  • Fig. 13 shows the thermal properties of an alloy having the composition of Al90Co9Mn1.
  • a molten alloy having a predetermined composition was manufactured using a high frequency melting furnace. As shown in Fig. 1, this melt was poured into a silica tube 1 with a small aperture 5 (aperture diameter: 0.2 to 0.5 mm) at the tip, and then heat dissolved, following which the aforementioned silica tube 1 was positioned directly above copper roll 2. This roll 2 was then rotated at a high speed of 4000 rpm, and argon gas pressure (0.7 kg/cm3) was applied to silica tube 1. Quench solidification was subsequently performed by discharging the liquid-melt from small aperture 5 of silica tube 1 onto the surface of roll 2 and quenching to yield an alloy tape 4.
  • the samples according to the present invention display an extremely high hardness from 260 to 340 DPN.
  • Fig. 2 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al88Ni 11.6 Ce 0.4 .
  • the crystal peak appears as a broad peak pattern with the alloy sample displaying an amorphous single phase structure.
  • Fig. 3 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 89.7 Ni5Fe5Ce 0.3 .
  • a two-phase structure is displayed in which fine Al particles having an fcc structure of the nano-scale are dispersed into the amorphous phase.
  • (111) and (200) display the crystal peaks of Al having an fcc structure.
  • Fig. 4 shows the DSC (Differential Scanning Calorimetry) curve in the case when an alloy having the composition of Al 89.6 Ni5Co5Ce 0.4 is heated at an increase temperature rate of 0.67 K/s.
  • Fig. 5 shows the DSC curve in the case when an alloy having the composition of Al88Ni 11.6 Y 0.4 is heated at an increase temperature rate of 0.67 K/s.
  • the broad peak appearing at lower temperatures represents the crystallization peak of Al particles having an fcc structure, while the sharp peak at higher temperatures represents the crystallization peak of the alloys. Due to the existence of these two peaks, when performing heat treatment such as quench hardening at an appropriate temperature, the volume percentage of the Al particles dispersed into the amorphous matrix phase can be controlled. As a result, it is clear that the mechanical properties can be improved through heat treatment.
  • a molten alloy having a predetermined composition was manufactured using a high frequency melting furnace. As shown in Fig. 1, this melt was poured into a silica tube 1 with a small aperture 5 (aperture diameter: 0.2 to 0.5 mm) at the tip, and then heat dissolved, following which the aforementioned silica tube 1 was positioned directly above copper roll 2. This roll 2 was then rotated at a high speed of 4000 rpm, and argon gas pressure (0.7kg/cm3) was applied to silica tube 1. Quench solidification was subsequently performed by discharging the liquid-melt from small aperture 5 of silica tube 1 onto the surface of roll 2 and quenching to yield an alloy tape 4.
  • the 180° contact bending test was conducted by bending each alloy tape sample 180° and contacting the ends thereby forming a U-shape.
  • the samples according to the present invention shown in Tables 3 and 4 display an extremely high hardness ranging from 260 to 400 DPN.
  • Fig. 6 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al87Ni12Mn1.
  • the crystal peak appears as a broad peak pattern with the alloy sample displaying an amorphous single phase structure.
  • Fig. 7 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al88Ni9Co3.
  • a two-phase structure is displayed in which fine Al particles having an fcc structure of the nano-scale are dispersed into the amorphous phase.
  • (111) and (200) display the crystal peaks of Al having an fcc structure.
  • Fig. 8 shows the DSC (Differential Scanning Calorimetry) curve in the case when an alloy having the composition of Al88Ni11Zr1 is heated at an increase temperature rate of 0.67 K/s.
  • Fig. 9 shows the DSC curve in the case when an alloy having the composition of Al88Ni11Fe1 is heated at an increase temperature rate of 0.67 K/s.
  • the broad peak appearing at lower temperatures represents the crystallization peak of Al particles having an fcc structure, while the sharp peak at higher temperatures represents the crystallization peak of the alloys. Due to the existence of these two peaks, when performing heat treatment such as quench hardening at an appropriate temperature, the volume percentage of the Al particles dispersed into the amorphous matrix phase can be controlled. As a result, it is clear that the mechanical properties can be improved through heat treatment.
  • a molten alloy having a predetermined composition was manufactured using a high frequency melting furnace. As shown in Fig. 1, this melt was poured into a silica tube 1 with a small aperture 5 (aperture diameter: 0.2 to 0.5 mm) at the tip, and then heat dissolved, following which the aforementioned silica tube 1 was positioned directly above copper roll 2. This roll 2 was then rotated at a high speed of 4000 rpm, and argon gas pressure (0.7kg/cm3) was applied to silica tube 1. Quench solidification was subsequently performed by discharging the liquid-melt from small aperture 5 of silica tube 1 onto the surface of roll 2 and quenching to yield an alloy tape 4.
  • the samples according to the present invention shown in Tables 5 and 7 display an extremely high hardness ranging from 165 to 387 DPN.
  • Fig. 10 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al89Co8Mn3.
  • the crystal peak appears as a broad peak pattern with the alloy sample displaying an amorphous single phase structure.
  • Fig. 11 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al90Co6Fe4.
  • a multiphase structure is displayed which comprises an amorphous phase and a fine Al crystalline phase having an fcc structure of the nano-scale.
  • (111) and (200) display the crystal peaks of Al having an fcc structure.
  • Fig. 12 shows the DSC (Differential Scanning Calorimetry) curve in the case when an alloy having the composition of Al90Co9Cu1 is heated at an increase temperature rate of 0.67 K/s.
  • Fig. 13 shows the DSC curve in the case when an alloy having the composition of Al90Co9Mn1 is heated at an increase temperature rate of 0.67 K/s.
EP19930112487 1992-08-05 1993-08-04 High strength and anti-corrosive aluminum-based alloy Withdrawn EP0584596A3 (en)

Applications Claiming Priority (6)

Application Number Priority Date Filing Date Title
JP209115/92 1992-08-05
JP209116/92 1992-08-05
JP4209116A JP2941571B2 (ja) 1992-08-05 1992-08-05 高強度耐食性アルミニウム基合金およびその製造方法
JP4209115A JP2583718B2 (ja) 1992-08-05 1992-08-05 高強度耐食性アルミニウム基合金
JP5041528A JP2703480B2 (ja) 1993-03-02 1993-03-02 高強度高耐食性アルミニウム基合金
JP41528/93 1993-03-02

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EP0584596A2 true EP0584596A2 (de) 1994-03-02
EP0584596A3 EP0584596A3 (en) 1994-08-10

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Cited By (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0710730A2 (de) * 1994-11-02 1996-05-08 Masumoto, Tsuyoshi Hochfeste und hochsteife Aluminiumbasislegierung und deren Herstellungsverfahren
EP0819778A2 (de) * 1996-07-18 1998-01-21 Ykk Corporation Hochfeste Aluminiumlegierung
EP0866143A1 (de) * 1996-09-09 1998-09-23 Sumitomo Electric Industries, Ltd Hochfeste, hochzähe aluminiumlegierung und verfahren zu deren herstellung
EP2112241A1 (de) * 2008-04-18 2009-10-28 United Technologies Corporation L12-verstärkte amorphe Aluminiumlegierungen
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
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
US8409497B2 (en) 2009-10-16 2013-04-02 United Technologies Corporation Hot and cold rolling high strength L12 aluminum alloys
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
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
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
US9611522B2 (en) 2009-05-06 2017-04-04 United Technologies Corporation Spray deposition of L12 aluminum alloys
EP3933060A4 (de) * 2019-05-29 2022-05-11 Sumitomo Electric Industries, Ltd. Aluminiumlegierung, draht aus aluminiumlegierung und verfahren zur herstellung einer aluminiumlegierung

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Publication number Priority date Publication date Assignee Title
EP0136508A2 (de) * 1983-10-03 1985-04-10 AlliedSignal Inc. Legierungen aus Aluminium und Übergangsmetallen mit hoher Festigkeit bei höheren Temperaturen
EP0339676A1 (de) * 1988-04-28 1989-11-02 Tsuyoshi Masumoto Hochfeste, hitzebeständige Aluminiumlegierungen
EP0354391A1 (de) * 1988-07-22 1990-02-14 Yoshida Kogyo K.K. Dünner, korrosions- und hitzefester Film aus einer Aluminiumlegierung sowie Verfahren zu dessen Herstellung
GB2243617A (en) * 1990-03-09 1991-11-06 Masumoto Tsuyoshi High strength amorphous alloy
EP0460887A1 (de) * 1990-06-08 1991-12-11 Tsuyoshi Masumoto Teilchendispersionsartige amorphe Aluminiumlegierung mit guter Festigkeit
EP0475101A1 (de) * 1990-08-14 1992-03-18 Ykk Corporation Hochfeste Legierungen auf Aluminiumbasis

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0136508A2 (de) * 1983-10-03 1985-04-10 AlliedSignal Inc. Legierungen aus Aluminium und Übergangsmetallen mit hoher Festigkeit bei höheren Temperaturen
EP0339676A1 (de) * 1988-04-28 1989-11-02 Tsuyoshi Masumoto Hochfeste, hitzebeständige Aluminiumlegierungen
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EP0710730A2 (de) * 1994-11-02 1996-05-08 Masumoto, Tsuyoshi Hochfeste und hochsteife Aluminiumbasislegierung und deren Herstellungsverfahren
EP0710730A3 (de) * 1994-11-02 1996-11-27 Masumoto Tsuyoshi Hochfeste und hochsteife Aluminiumbasislegierung und deren Herstellungsverfahren
EP0819778A2 (de) * 1996-07-18 1998-01-21 Ykk Corporation Hochfeste Aluminiumlegierung
EP0819778A3 (de) * 1996-07-18 1998-02-11 Ykk Corporation Hochfeste Aluminiumlegierung
US6056802A (en) * 1996-07-18 2000-05-02 Ykk Corporation High-strength aluminum-based alloy
EP0866143A1 (de) * 1996-09-09 1998-09-23 Sumitomo Electric Industries, Ltd Hochfeste, hochzähe aluminiumlegierung und verfahren zu deren herstellung
EP0866143A4 (de) * 1996-09-09 1999-09-29 Sumitomo Electric Industries Hochfeste, hochzähe aluminiumlegierung und verfahren zu deren herstellung
US6149737A (en) * 1996-09-09 2000-11-21 Sumitomo Electric Industries Ltd. High strength high-toughness aluminum alloy and method of preparing the same
US7879162B2 (en) 2008-04-18 2011-02-01 United Technologies Corporation High strength aluminum alloys with L12 precipitates
US8409373B2 (en) 2008-04-18 2013-04-02 United Technologies Corporation L12 aluminum alloys with bimodal and trimodal distribution
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
EP2112241A1 (de) * 2008-04-18 2009-10-28 United Technologies Corporation L12-verstärkte amorphe Aluminiumlegierungen
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
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
US7871477B2 (en) 2008-04-18 2011-01-18 United Technologies Corporation High strength 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
EP3933060A4 (de) * 2019-05-29 2022-05-11 Sumitomo Electric Industries, Ltd. Aluminiumlegierung, draht aus aluminiumlegierung und verfahren zur herstellung einer aluminiumlegierung

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