EP0524527A1 - Verdichtete und verfestigte Werkstoffe auf Aluminiumbasis und Verfahren zur Herstellung dieser Werkstoffe - Google Patents

Verdichtete und verfestigte Werkstoffe auf Aluminiumbasis und Verfahren zur Herstellung dieser Werkstoffe Download PDF

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Publication number
EP0524527A1
EP0524527A1 EP92111993A EP92111993A EP0524527A1 EP 0524527 A1 EP0524527 A1 EP 0524527A1 EP 92111993 A EP92111993 A EP 92111993A EP 92111993 A EP92111993 A EP 92111993A EP 0524527 A1 EP0524527 A1 EP 0524527A1
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EP
European Patent Office
Prior art keywords
aluminum
consolidated
compacted
based alloy
matrix
Prior art date
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EP92111993A
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English (en)
French (fr)
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EP0524527B1 (de
Inventor
Katsuyuki Taketani
Hidenobu Nagahama
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YKK Corp
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YKK Corp
Yoshida Kogyo KK
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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
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • C22C1/0416—Aluminium-based alloys

Definitions

  • the present invention relates to a compacted and consolidated aluminum-based alloy material having not only high strength but also elongation sufficient to withstand practically-employed working, and also to a process for the production of the material.
  • Aluminum-based alloys having high strength and high heat resistance have been produced to date by liquid quenching or the like.
  • the aluminum alloys disclosed in Japanese Patent Application Laid-Open (Kokai) No. 1 - 275732 and obtained by liquid quenching are amorphous or microcrystalline and are excellent alloys having high strength, high heat resistance and high corrosion resistance.
  • the aluminum-based alloys referred to above exhibit high strength, high heat resistance and high corrosion resistance and are excellent alloys.
  • they are each obtained in the form of powder or flakes by liquid quenching and the powder or flakes are then processed or worked as a raw material in one way or another to obtain a final product, in other words, the powder or flakes are converted into a final product by primary processing or working, they are excellent in processability or workability.
  • to form the powder or flakes as a raw material into a consolidated material and then to work the consolidated material, namely, to subject the consolidated material to secondary working there is still room for improvements in their workability and also in the retention of their excellent properties after the working.
  • An object of the present invention is, therefore, to provide a compacted and consolidated aluminum-based alloy material having a particular composition that permits easy working upon subjecting the material to secondary working (extrusion, machining or the like) and allows to retain excellent properties of the material even after the working.
  • the present invention provides a compacted and consolidated aluminum-based alloy material, which is characterized in that said material has been obtained by compacting and consolidating a quench-solidified material in the form of powder or flakes whose composition is represented by the general formula: Al a Ni b X c wherein X is one or more elements selected from La and Ce or an Mm (mischmetal) and a, b and c satisfy the following equations by atom percent: 87.5 ⁇ a ⁇ 92.5, 5 ⁇ b ⁇ 10, and 0.5 ⁇ c ⁇ 2.5.
  • a, b and c satisfy the following equations by atom percent: 89 ⁇ a ⁇ 91, 7 ⁇ b ⁇ 10, and 1 ⁇ c ⁇ 2.
  • the matrix is formed of aluminum or a supersaturated aluminum solid solution, whose average crystal grain size is 40 - 400 nm, grains made of a stable or metastable phase of various intermetallic compounds formed of the matrix element and the other alloying elements and/or of various intermetallic compounds formed of the other alloying elements are distributed evenly in the matrix, and the intermetallic compounds have an average grain size of 10 - 200 nm.
  • the present invention also provides a process characterized in that a material represented by the general formula is molten, then quenched and solidified into powder or flakes and, thereafter, the powder or flakes are compacted and then compressed, formed and consolidated by conventional plastic working.
  • the powder or flakes as the raw material are required to be amorphous or microcrystalline such that the average crystal grain size of the matrix is 400 nm or less and the average grain size of intermetallic compounds is 200 nm or less or to be in a mixed phase thereof.
  • the raw material is amorphous, it can be converted into such a microcrystalline phase or mixed phase as defined above by heating it to 200 °C to 300 °C upon compaction.
  • FIG. 1 is a graph showing variations in tensile strength and elongation among the consolidated materials in the example.
  • FIG. 2 is also a graph depicting variations in tensile strength and elongation at 200 °C among the consolidated materials in the example.
  • FIG. 3 is also a graph showing variations in tensile strength and elongation at 300 °C among the consolidated materials in the example.
  • FIG. 4 is a graph illustrating relationships between the content of Mm and the grain sizes of Al matrix and La3Al11.
  • the proportions a, b and c are limited by atom percent to the ranges of 87.5 - 92.5%, 5 - 10% and 0.5 - 2.5%, respectively, in the above general formula, because the alloys within the above ranges have higher strength than conventional (commercial) high-strength aluminum alloys over the temperature range of from room temperature to 200 °C and are also equipped with ductility sufficient to withstand practically-employed working.
  • Ni is an element having relatively small ability to diffuse into the Al matrix.
  • various stable or metastable, fine intermetallic compounds are formed and distributed as fine grains in the Al matrix.
  • Ni is therefore effective not only in strengthening the matrix but also in inhibiting extraordinary coarsening of crystal grains.
  • Ni improves the hardness and strength of the alloy to significant extent, stabilizes the microcrystalline phase at elevated temperatures, to say nothing of room temperature, and imparts heat resistance.
  • element X stands for one or more elements selected from La and Ce or Mm. It is an element having small ability to diffuse in the Al matrix. As it is contained together with element Ni, it forms stable intermetallic compounds, thereby contributing to the stabilization of the microcrystalline structure. Further, its combination with the above element can impart ductility required to apply conventional working.
  • Mm is the common name for metal consisting of La and Ce as principal elements and, in addition, containing rare earth (lanthanoid) elements other than La and Ce described above and inevitable impurities (Si, Fe, Mg, Al, etc.). Mm can substitute for La and/or Ce at the ratio of approximately 1 to 1 ( by atom percent) and is economical, whereby Mm has a substantial advantage in economy.
  • the average crystalline grain size of the matrix is preferably in the range of 40 - 400 nm for the following reasons. Average crystalline grain sizes smaller than 40 nm are too small to provide sufficient ductility despite high strength. To obtain ductility required for conventional working, an average crystalline grain size of at least 40 nm is therefore desirable. If the average crystalline grain size exceeds 400 nm, on the other hand, the strength drops abruptly, thereby making it impossible to obtain a consolidated material having high strength. To obtain a consolidated material having high strength, an average crystalline grain size not greater than 400 nm is hence needed.
  • the average grain size of the intermetallic compounds is preferably in the range of 10 - 200 nm because intermetallic compounds with an average grain size outside the above range cannot serve as strengthening elements for the Al matrix. If the intermetallic compounds have an average grain size smaller than 10 nm, they do not contribute to the strengthening of the Al matrix and, if distributed in an amount greater than that needed, there is the potential problem of embrittlement. Average grain sizes exceeding 200 nm, on the other hand, result in unduly large grains distributed in the Al matrix so that the Al matrix cannot retain its strength and the intermetallic compounds cannot serve as strengthening elements. The restriction to the above ranges, therefore, provides great improvements in Young's modulus, high-temperature strength and fatigue strength.
  • its average crystal grain size of the matrix and the average grain size of its intermetallic compounds can be controlled by choosing suitable conditions for its production.
  • the average crystal grain size of the matrix and the average grain size of the intermetallic compounds should be controlled small where an importance is placed on the strength. In contrast, they should be controlled large where the ductility is considered important. In this manner, it is possible to obtain consolidated aluminum-based alloy materials which are suited for various purposes, respectively.
  • control of the average crystal grain size of the matrix to the range of 100 - 400 nm makes it possible to impart properties so that the resulting material can be used as an excellent superplastic working material.
  • Aluminum-based alloy powder having a desired composition (Al 92-x Ni8Mm x ) was produced by a gas atomizing apparatus.
  • the aluminum-based alloy powder so produced was filled in a metal capsule and, while being degassed, was formed into an extrusion billet by vacuum hot-pressing.
  • the billet was extruded at 200 - 550 °C through an extruder.
  • Mechanical properties (tensile strength and elongation) of the extruded material (consolidated material) obtained under the above production conditions are shown in FIG. 1.
  • the tensile strength of a conventional, consolidated high-strength aluminum-based alloy material was also measured at room temperature.
  • the tensile strength was found to be about 650 MPa. It is also understood from this value that the above consolidated material of the present invention is excellent in strength at the Mm content of 0.5 at.%.
  • the Young's moduli of consolidated materials obtained under the above production conditions were also investigated.
  • the Young's moduli of the consolidated materials according to the present invention were as high as 8900 - 9300 kgf/mm2 as opposed to about 7000 kg/mm2 of the conventional high-strength Al alloy (duralumin).
  • the consolidated materials according to the present invention therefore exhibit the advantages that their deflection and deformation are smaller under the same load.
  • the average crystal grain size of the Al matrix was found to range from 100 nm to 125 nm while the average grain size of the intermetallic compound (La3Al11) was found to range from 20 nm to 30 nm. It is now understood that the above good results at room temperature were obtained when the average crystal grain size of the matrix and the average grain size of the intermetallic compound fell within the above ranges, respectively. Needless to say, these sizes vary depending on the composition and also depending on whether the extruded material is held at 200 °C or 300 °C. In the latter temperature, especially, grains grow so that the average crystal grain size of the matrix and the average grain size of the intermetallic compound become greater.
  • Consolidated aluminum-based alloy material according to the present invention are excellent in elongation (toughness) so that they can withstand secondary working when the secondary working is applied.
  • the secondary working can therefore be performed with ease while retaining the excellent properties of their raw material as they are.
  • such consolidated materials can be obtained by a simple process, that is, by simply compacting powder or flakes, which have been obtained by quench solidification, and then subjecting the thus-compacted powder or flakes to plastic working.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
EP19920111993 1991-07-22 1992-07-14 Verdichtete und verfestigte Werkstoffe auf Aluminiumbasis und Verfahren zur Herstellung dieser Werkstoffe Expired - Lifetime EP0524527B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP3181065A JPH0525578A (ja) 1991-07-22 1991-07-22 アルミニウム基合金集成固化材並びにその製造方法
JP181065/91 1991-07-22

Publications (2)

Publication Number Publication Date
EP0524527A1 true EP0524527A1 (de) 1993-01-27
EP0524527B1 EP0524527B1 (de) 1997-11-19

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EP19920111993 Expired - Lifetime EP0524527B1 (de) 1991-07-22 1992-07-14 Verdichtete und verfestigte Werkstoffe auf Aluminiumbasis und Verfahren zur Herstellung dieser Werkstoffe

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Country Link
EP (1) EP0524527B1 (de)
JP (1) JPH0525578A (de)
DE (1) DE69223185T2 (de)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10356851B2 (en) 2014-08-08 2019-07-16 Saint-Gobain Glass France Transparent pane having an electrical heating layer, method for the production thereof, and use thereof
US10660161B2 (en) 2014-08-08 2020-05-19 Saint-Gobain Glass France Transparent pane having an electrical heating layer, method for its production, and its use

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07179974A (ja) * 1993-12-24 1995-07-18 Takeshi Masumoto アルミニウム合金およびその製造方法

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2015035A (en) * 1978-02-17 1979-09-05 Bicc Ltd Fabrication of Metallic Materials
GB2167442A (en) * 1984-11-28 1986-05-29 Honda Motor Co Ltd Heat-resisting, high-strength aluminium alloy
EP0265307A1 (de) * 1986-09-22 1988-04-27 Automobiles Peugeot Verfahren zur Herstellung von Gegenständen aus hypereutektischen Aluminium-Siliziumlegierungen, hergestellt aus extrem rasch abgekühlten Pulvern
EP0339676A1 (de) * 1988-04-28 1989-11-02 Tsuyoshi Masumoto Hochfeste, hitzebeständige Aluminiumlegierungen

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2015035A (en) * 1978-02-17 1979-09-05 Bicc Ltd Fabrication of Metallic Materials
GB2167442A (en) * 1984-11-28 1986-05-29 Honda Motor Co Ltd Heat-resisting, high-strength aluminium alloy
EP0265307A1 (de) * 1986-09-22 1988-04-27 Automobiles Peugeot Verfahren zur Herstellung von Gegenständen aus hypereutektischen Aluminium-Siliziumlegierungen, hergestellt aus extrem rasch abgekühlten Pulvern
EP0339676A1 (de) * 1988-04-28 1989-11-02 Tsuyoshi Masumoto Hochfeste, hitzebeständige Aluminiumlegierungen

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 12, no. 40 (C-474)(2887) 5 February 1988 & JP-A-62 188 738 ( HONDA MOTOR CO. ) *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10356851B2 (en) 2014-08-08 2019-07-16 Saint-Gobain Glass France Transparent pane having an electrical heating layer, method for the production thereof, and use thereof
US10660161B2 (en) 2014-08-08 2020-05-19 Saint-Gobain Glass France Transparent pane having an electrical heating layer, method for its production, and its use

Also Published As

Publication number Publication date
DE69223185D1 (de) 1998-01-02
DE69223185T2 (de) 1998-06-18
EP0524527B1 (de) 1997-11-19
JPH0525578A (ja) 1993-02-02

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