WO2002022906A1 - Procede conferant une plus haute ductilite aux alliages amorphes - Google Patents

Procede conferant une plus haute ductilite aux alliages amorphes Download PDF

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Publication number
WO2002022906A1
WO2002022906A1 PCT/JP2000/006367 JP0006367W WO0222906A1 WO 2002022906 A1 WO2002022906 A1 WO 2002022906A1 JP 0006367 W JP0006367 W JP 0006367W WO 0222906 A1 WO0222906 A1 WO 0222906A1
Authority
WO
WIPO (PCT)
Prior art keywords
amorphous alloy
ductility
alloy
band
amorphous
Prior art date
Application number
PCT/JP2000/006367
Other languages
English (en)
Japanese (ja)
Inventor
Akihisa Inoue
Original Assignee
Tohoku Techno Arch Co., Ltd.
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 Tohoku Techno Arch Co., Ltd. filed Critical Tohoku Techno Arch Co., Ltd.
Priority to JP2002527341A priority Critical patent/JPWO2002022906A1/ja
Priority to PCT/JP2000/006367 priority patent/WO2002022906A1/fr
Priority to TW089119748A priority patent/TW491907B/zh
Publication of WO2002022906A1 publication Critical patent/WO2002022906A1/fr

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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
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/186—High-melting or refractory metals or alloys based thereon of zirconium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/10—Amorphous alloys with molybdenum, tungsten, niobium, tantalum, titanium, or zirconium or Hf as the major constituent
    • 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

Definitions

  • the present invention relates to a method for increasing ductility, which can increase the ductility of an amorphous alloy having high hardness, high strength, and high toughness, but relatively poor ductility.
  • amorphous alloys including these Zr-based alloys, have no or very low crystallinity. In most fracture tests, fractures occur without elongation, and these small ductility may be an obstacle to practical application. Longed for.
  • a method for increasing ductility of an amorphous alloy according to the present invention is a method for increasing ductility of an amorphous alloy, and the method includes: The method is characterized by including at least a step of applying an appropriate deformation force for forming a band inside the alloy.
  • the ductility of the amorphous alloy is obtained.
  • the plastic deformability can be greatly improved.
  • the step of applying the deformation force is a cold rolling step.
  • the band by applying a deformation force by cold rolling, the band can be efficiently generated inside the alloy, and the application of the deformation force can be easily controlled as appropriate.
  • the control of the amount of the band and the like can be easily performed.
  • the rolling reduction in the cold rolling step is preferably in a range of less than 10%.
  • FIG. 1 is a diagram showing the shape of a tensile test piece used in this example.
  • FIG. 2 is a graph showing a test result of a tensile test on each test piece manufactured in this example.
  • Fig. 3 shows an electron microscope of the tensile fracture surface of the test piece subjected to the rolling process.
  • (B) is an electron microscope showing the tensile fracture surface of the test piece that has not been subjected to rolling treatment.
  • FIG. 4 is a graph showing the Pickers hardness of the test pieces at each rolling reduction manufactured in this example.
  • Fig. 5 shows the stress of the compression test on the specimens with and without the rolling treatment of this example. It is a graph which shows a distortion curve.
  • Figure 6 is an SEM photograph of the fracture surface of the test piece that fractured in the compression test.
  • Figure 7 is an SEM photograph of a rolled material that has undergone 9% plastic deformation by compression.
  • FIG. 8 is a conceptual diagram showing the state of shear stress applied to the band inside the alloy.
  • the molten alloy ⁇ to prepare a Zr 55 Ali 0 Cu 30 Ni 5 Balta glass alloy by clamping ⁇ method for rapidly cooled mold.
  • the reason for this decrease is that the deformation in the lateral direction becomes remarkable when the rolling reduction is 80% or more, and the amount of plastic deformation becomes extremely large. From this, it is considered that the introduction number of the t-band is rapidly increasing at the rolling reduction of 60 to 90%, and as a result, the Young's modulus is also rapidly reduced.
  • the fracture strain of each sample was about 2%, and the tensile strength of the rolled material was the same or lower than that of the unrolled material. From these facts, as the rolling reduction during cold rolling, when this rolling reduction becomes large, the number of bands formed inside the alloy increases rapidly as described above, and the Young's modulus begins. If the mechanical properties of the alloy change significantly, and if the rolling reduction is small, the desired improvement in ductility cannot be obtained, it is preferable that the alloying ratio be less than 10%, more preferably less than 10%. preferable.
  • Fig. 3 shows the tensile fracture surfaces of the rolled material and the unrolled material observed by an electron microscope (SEM).
  • SEM electron microscope
  • Fig. 4 shows the Pickers hardness of each rolled material. In all samples, the hardness was 460 to 480, and there was no significant change due to the rolling reduction.
  • Figure 5 shows the stress-strain curve of the compression test. The breaking strain was 2-3% for the unrolled material, while it was as large as 10% or more for the rolled material.
  • the compressive strength of unrolled material is 1642MPa because it breaks immediately after plastic deformation, but it is as high as 1819MPa for rolled material.
  • Figure 6 shows an SEM photograph of the fracture surface of the rolled material that fractured in the compression test. A vein pattern is also observed, but unlike the normal fracture surface along the fin belt, it is a very prominent and excavated fracture surface.
  • FIG. 7 is an SEM photograph of a rolled material that has undergone plastic deformation of 9%, which is less than 10% by compression. When a compression test is performed on a bulk glass alloy, it usually breaks along a certain fin band without showing any plastic deformation, but this rolled material is plastically deformed into a wavy shape I understand.
  • the stress applied to the band in the tensile test is the shear stress and the stress in the direction in which the band is peeled off.
  • shear stress is applied in the direction of crushing the band, that is, in the direction of restraining the band so that it does not peel.
  • breakage (peeling) along the band easily occurs, whereas in the compression test, such breakage (peeling) does not occur, and the slip in each band progresses. It is considered that large plastic deformation was realized.

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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)
  • Metal Rolling (AREA)
  • Continuous Casting (AREA)

Abstract

L'invention concerne un procédé destiné à conférer une plus haute ductilité à un alliage amorphe. Ledit procédé consiste à appliquer, au verre brut d'un alliage amorphe, une force de déformation appropriée de façon à former une zone coulissante à l'intérieur de l'alliage.
PCT/JP2000/006367 2000-09-18 2000-09-18 Procede conferant une plus haute ductilite aux alliages amorphes WO2002022906A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
JP2002527341A JPWO2002022906A1 (ja) 2000-09-18 2000-09-18 非晶質合金の高延性化方法
PCT/JP2000/006367 WO2002022906A1 (fr) 2000-09-18 2000-09-18 Procede conferant une plus haute ductilite aux alliages amorphes
TW089119748A TW491907B (en) 2000-09-18 2000-09-25 Method of providing amorphous alloy with high ductility

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2000/006367 WO2002022906A1 (fr) 2000-09-18 2000-09-18 Procede conferant une plus haute ductilite aux alliages amorphes

Publications (1)

Publication Number Publication Date
WO2002022906A1 true WO2002022906A1 (fr) 2002-03-21

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Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2000/006367 WO2002022906A1 (fr) 2000-09-18 2000-09-18 Procede conferant une plus haute ductilite aux alliages amorphes

Country Status (3)

Country Link
JP (1) JPWO2002022906A1 (fr)
TW (1) TW491907B (fr)
WO (1) WO2002022906A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2005017219A2 (fr) * 2003-08-13 2005-02-24 Liquidmetal Technologies Structures haute durabilite en alliage amorphe et procede de formation associe

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1994023078A1 (fr) * 1993-04-07 1994-10-13 California Institute Of Technology Formation de verres metalliques contenant du beryllium
WO2000032833A1 (fr) * 1998-12-03 2000-06-08 Japan Science And Technology Corporation Verre metallique a ductilite elevee contenant des nanoparticules dispersees et procede de production

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001262291A (ja) * 2000-03-21 2001-09-26 Yoshihiko Yokoyama アモルファス合金およびその製造方法ならびにそれを用いたゴルフクラブヘッド

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1994023078A1 (fr) * 1993-04-07 1994-10-13 California Institute Of Technology Formation de verres metalliques contenant du beryllium
WO2000032833A1 (fr) * 1998-12-03 2000-06-08 Japan Science And Technology Corporation Verre metallique a ductilite elevee contenant des nanoparticules dispersees et procede de production

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
Takeshi MASUMOTO ed., "Amorphous Kizoku no Kiso", 25 November, 1982 (25.11.82 ), Kabushiki Kaisha Ohmsha, pages 210 to 211 *

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2005017219A2 (fr) * 2003-08-13 2005-02-24 Liquidmetal Technologies Structures haute durabilite en alliage amorphe et procede de formation associe
WO2005017219A3 (fr) * 2003-08-13 2009-04-30 Liquidmetal Technologies Structures haute durabilite en alliage amorphe et procede de formation associe
US10214800B2 (en) 2003-08-13 2019-02-26 Crucible Intellectual Property, Llc High durability structures of amorphous alloy and a method of forming

Also Published As

Publication number Publication date
JPWO2002022906A1 (ja) 2004-01-22
TW491907B (en) 2002-06-21

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