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WO2004044249A2 - Articles intermetalliques de fabrication faisant preuve d'une aptitude au pliage elevee a temperature ambiante - Google Patents

Articles intermetalliques de fabrication faisant preuve d'une aptitude au pliage elevee a temperature ambiante Download PDF

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Publication number
WO2004044249A2
WO2004044249A2 PCT/US2003/035575 US0335575W WO2004044249A2 WO 2004044249 A2 WO2004044249 A2 WO 2004044249A2 US 0335575 W US0335575 W US 0335575W WO 2004044249 A2 WO2004044249 A2 WO 2004044249A2
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Prior art keywords
manufacture
article
component
tensile
specimens
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WO2004044249A3 (fr
Inventor
Karl A. Gschneidner, Jr.
Alexandra O. Pecharsky
Vitalij K. Pecharsky
Alan M. Russell
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Iowa State University Research Foundation Inc ISURF
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Iowa State University Research Foundation Inc ISURF
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Priority to AU2003287576A priority Critical patent/AU2003287576A1/en
Publication of WO2004044249A2 publication Critical patent/WO2004044249A2/fr
Priority to US11/120,547 priority patent/US20050274439A1/en
Anticipated expiration legal-status Critical
Publication of WO2004044249A3 publication Critical patent/WO2004044249A3/fr
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    • A—HUMAN NECESSITIES
    • A44—HABERDASHERY; JEWELLERY
    • A44C—PERSONAL ADORNMENTS, e.g. JEWELLERY; COINS
    • A44C27/00—Making jewellery or other personal adornments
    • A44C27/001—Materials for manufacturing jewellery
    • A44C27/002—Metallic materials
    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
    • A61L27/00—Materials for grafts or prostheses or for coating grafts or prostheses
    • A61L27/02—Inorganic materials
    • A61L27/04—Metals or alloys
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
    • C01B3/0005—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes
    • C01B3/001—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes characterised by the uptaking medium; Treatment thereof
    • C01B3/0031—Intermetallic compounds; Metal alloys; Treatment thereof
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
    • C01B3/0005—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes
    • C01B3/001—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes characterised by the uptaking medium; Treatment thereof
    • C01B3/0031—Intermetallic compounds; Metal alloys; Treatment thereof
    • C01B3/0036—Intermetallic compounds; Metal alloys; Treatment thereof only containing iron and titanium; Treatment thereof
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
    • C01B3/0005—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes
    • C01B3/001—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes characterised by the uptaking medium; Treatment thereof
    • C01B3/0031—Intermetallic compounds; Metal alloys; Treatment thereof
    • C01B3/0047—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
    • C01B3/0005—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes
    • C01B3/001—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes characterised by the uptaking medium; Treatment thereof
    • C01B3/0031—Intermetallic compounds; Metal alloys; Treatment thereof
    • C01B3/0047—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof
    • C01B3/0052—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof also containing titanium
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
    • C01B3/0005—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes
    • C01B3/001—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes characterised by the uptaking medium; Treatment thereof
    • C01B3/0031—Intermetallic compounds; Metal alloys; Treatment thereof
    • C01B3/0047—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof
    • C01B3/0057—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof also containing nickel
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
    • C01B3/0005—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes
    • C01B3/001—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes characterised by the uptaking medium; Treatment thereof
    • C01B3/0031—Intermetallic compounds; Metal alloys; Treatment thereof
    • C01B3/0047—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof
    • C01B3/0063—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof only containing a rare earth metal and only one other metal
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
    • C01B3/0005—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes
    • C01B3/001—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes characterised by the uptaking medium; Treatment thereof
    • C01B3/0031—Intermetallic compounds; Metal alloys; Treatment thereof
    • C01B3/0047—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof
    • C01B3/0063—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof only containing a rare earth metal and only one other metal
    • C01B3/0068—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof only containing a rare earth metal and only one other metal the other metal being nickel
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
    • C01B3/50—Separation of hydrogen or hydrogen containing gases from gaseous mixtures, e.g. purification
    • C01B3/501—Separation of hydrogen or hydrogen containing gases from gaseous mixtures, e.g. purification by diffusion
    • C01B3/503—Separation of hydrogen or hydrogen containing gases from gaseous mixtures, e.g. purification by diffusion characterised by the membrane
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
    • C01B3/50—Separation of hydrogen or hydrogen containing gases from gaseous mixtures, e.g. purification
    • C01B3/501—Separation of hydrogen or hydrogen containing gases from gaseous mixtures, e.g. purification by diffusion
    • C01B3/503—Separation of hydrogen or hydrogen containing gases from gaseous mixtures, e.g. purification by diffusion characterised by the membrane
    • C01B3/505—Membranes containing palladium
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
    • C01B3/50—Separation of hydrogen or hydrogen containing gases from gaseous mixtures, e.g. purification
    • C01B3/508—Separation of hydrogen or hydrogen containing gases from gaseous mixtures, e.g. purification by selective and reversible uptake by an appropriate medium, i.e. the uptake being based on physical or chemical sorption phenomena or on reversible chemical reactions
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C28/00—Alloys based on a metal not provided for in groups C22C5/00 - C22C27/00
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C5/00—Alloys based on noble metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/04—Single or very large crystals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
    • F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/38—Selection of substances as active materials, active masses, active liquids of elements or alloys
    • H01M4/383—Hydrogen absorbing alloys
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/04—Auxiliary arrangements, e.g. for control of pressure or for circulation of fluids
    • H01M8/04082—Arrangements for control of reactant parameters, e.g. pressure or concentration
    • H01M8/04201—Reactant storage and supply, e.g. means for feeding, pipes
    • H01M8/04216—Reactant storage and supply, e.g. means for feeding, pipes characterised by the choice for a specific material, e.g. carbon, hydride, absorbent
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/10—Energy storage using batteries
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/30—Hydrogen technology
    • Y02E60/32—Hydrogen storage
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/30—Hydrogen technology
    • Y02E60/50—Fuel cells
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
    • Y02P70/50—Manufacturing or production processes characterised by the final manufactured product

Definitions

  • the present invention relates to articles of manufacture made of intermetallic compounds having relatively high ductility at room temperature.
  • Intermetallic compounds such as TiAl, Ni 3 Al, FeAl, ZrCo 2 and others, are superior in several ways to conventional metals and alloys . Certain intermetallic compounds are stronger and stiffer at elevated temperature and provide better corrosion resistance than conventional metals and alloys. Some intermetallic compounds also possess exceptional magnetic properties and low densities. However, at room temperature, intermetallic compounds generally are brittle and have low fracture toughness compared to pure metals and solid solution alloys. Hundreds of scientists have worked for more than 50 years to address the problem of room temperature brittleness of intermetallic compounds.
  • An embodiment of the invention provides an article of manufacture fabricated of an intermetallic compound comprising R and M having a CsCl-type ordered crystal structure wherein R is one or more rare earth elements and M is one or more non- rare earth metals and having high ductility at ambient (room) temperature, such as for purposes of illustration only, at least about 5% tensile elongation prior to fracture when tensile tested at room temperature in ambient air.
  • One embodiment of the present invention relates to articles of manufacture fabricated of intermetallic compounds selected from the group consisting of an RM compound and a higher order compound thereof having a B2 (CsCl-type) ordered crystal structure wherein R is one or more rare earth elements and M is one or more non-rare earth metals.
  • the articles of manufacture have high ductility at ambient (room) temperature, such as for purposes of illustration only, at least about 5%, preferably about 10% and greater, tensile elongation prior to fracture when tensile tested at room temperature in ambient air.
  • the articles of manufacture exhibit high compressive ductilities and fracture toughness at room temperature in ambient air.
  • Another embodiment of the present invention relates to articles of manufacture fabricated of intermetallic compounds selected from the group consisting of a M'M compound and a higher order compound thereof having a B2 (CsCl-type) ordered crystal structure wherein M' and M are one or more different non-rare earth metals .
  • the articles of manufacture have high ductility at ambient (room) temperature, such as for purposes of illustration only, at least about 5%, preferably about 10% and greater, tensile elongation prior to fracture when tensile tested at room temperature in ambient air.
  • the articles of manufacture exhibit high compressive ductilities and fracture toughness at room temperature in ambient air.
  • Still another embodiment involves a method of making an article of manufacture by plastically deforming a body (e.g. an ingot or casting) comprising a ductile intermetallic compound of the type described above .
  • a body e.g. an ingot or casting
  • Figure 1 is a diagram of a CsCl-type (B2) crystal structure of an RM intermetallic compound wherein the corners of the unit cell cube are occupied by the M element and the atom in the cube center is the R element. Atom sizes have been reduced for clarity. The ⁇ 100 ⁇ and ⁇ 101 ⁇ planes and (010) direction for dislocation slip in the YCu intermetallic compound are labeled.
  • Figure 2 is a stress-strain curve for a polycrystalline YAg tensile specimen tested in air at 22 degrees C. The specimen was ductile in having elongation of 20% at onset of fracture and 27% at final fracture. A plot for a commercially available 3105 Al alloy tested under the same conditions is also shown for comparison.
  • Figure 3 is a transmission electron micrograph of dislocation structures in a plastically deformed YAg tensile specimen.
  • Figure 4 is a stress-strain curve for polycrystalline YCu x 005 tensile specimen tested in air at 22 degrees C.
  • Figure 5 is an optical photomicrograph of slip bands on the surface of an YCu single crystal tensile specimen deformed 6% in tension at 22 degrees C.
  • the intersecting lines are slip bands resulting from dislocation motion on the ⁇ 100 ⁇ and ⁇ 101 ⁇ crystal planes.
  • Scale bar is 0.4 mm high with 0.04 mm graduations .
  • Figure 6 is a stress-strain curve for polycrystalline DyCu tensile specimen tested in air at 22 degrees C.
  • Figure 7 is a comparison of the as-received (a) and deformed (b and c) specimens of ErCu compression tested in air at 22 degrees C. Specimen (b) was deformed at 14.1% true strain and specimen at (c) at 20.5% true strain.
  • Figure 8 shows specimen geometry used for K 1C and J ⁇ C testing. Dimension W was 24 mm, and the specimen thickness, B, was 10 mm.
  • Figure 9 shows examples of conventional tensile test results for polycrystalline YAg, YCu, and DyCu. The strain rate was 2xl0 _4 /second for all specimens.
  • Figure 10 shows K ⁇ C test result for polycrystalline YCu.
  • COD crack opening displacement.
  • the straight line superimposed on the data indicates the 5% secant deviation.
  • Figure 11 shows load versus load-line-displacement plot for J IC testing of YAg.
  • Figure 12 shows load versus load-line-displacement plot for Jic testing of DyCu.
  • Figure 13 shows J- ⁇ a curve determined for YAg as required by the ASTM standard.
  • Figure 14a shows bright field TEM image and Figure 14b shows conical scan dynamic dark field TEM image of DyCu J IC fracture toughness test specimen.
  • the mean grain size determined by the linear intercept method for this specimen was 0.20 ⁇ m.
  • Figure 15 is a SEM micrograph of fracture surface from a YAg compact tension specimen. Note the absence of intergranular fracture.
  • Figure 16 is design drawing of the single crystal tensile specimen dimensions produced by electrodischarge machining.
  • the major face of the tensile specimen gauge length is seen here in true shape.
  • the specimen thickness was 1.3 mm.
  • Figure 17 is a SEM micrograph of the fracture surface from a single crystal (Tb 088 Dy 012 ) Zn tensile test specimen.
  • Figure 18 shows stress-strain plots for four YCu single crystal tensile test specimens oriented with the [142] direction parallel to the tensile axis.
  • Figure 19 is an optical micrograph of slip lines on the
  • Figure 20 shows YCu single crystal compression stress- strain plots. Compression of the specimen labeled "1" was halted shortly after the first serrations in the stress-strain plot appeared. Specimen #1 showed no slip lines on the polished surfaces. Compression of the specimen labeled "2" was continued well beyond the first serrations in the stress- strain plot, and this specimen underwent extensive surface distortion, as shown in Figure 21. The serrations in the curves are thought to result from a stress-induced transformation to the B27 structure.
  • Figure 21 is a SEM micrograph of YCu compression test specimen #2 showing topographic displacement of the initially flat ⁇ 100 ⁇ surfaces.
  • the feature running vertically through the center of the micrograph is the corner of the specimen where two specimen faces meet at right angles .
  • the compression axis was parallel to this corner.
  • the specimen faces Prior to the compression test, the specimen faces were perpendicular ⁇ 100 ⁇ planes that had been polished flat. The distortion of these surfaces is thought to be the result of a stress-induced transformation from the B2 crystal structure to the B27 crystal structure .
  • Figure 22 shows a comparison of the anisotropy factor, A "12 , versus the Poisson ratio for YAg, YCu, and DyCu as well as for body-centered cubic (bcc) transition metals, ionic compounds, and non-RM intermetallic compounds for comparison.
  • One embodiment of the present invention involves articles of manufacture fabricated of ordered intermetallic compounds comprising R and M having a B2 (CsCl-type) ordered crystal structure wherein R is one or more rare earth elements and M is one or more non-rare earth metals, preferably one or more late transition metals or early p-group metals from Groups I, II, or III) of the Periodic Table.
  • R is one or more rare earth elements
  • M is one or more non-rare earth metals, preferably one or more late transition metals or early p-group metals from Groups I, II, or III) of the Periodic Table.
  • the intermetallic compound can be selected from the group consisting of an RM compound and a higher order RM compound thereof having the B2 (CsCl-type) ordered crystal structure where a higher order compound means that instead of a single rare earth element, R, two, three, four or more different rare earth elements are taken in various proportions; and instead of a single non-rare earth element M, two, three, four, or more different non-rare earth elements are taken in different proportions thus forming a (R l f R 2 , R 3 , . . .) (M 1 M 2 , M 3 , . . .) compound, i.e. a first order compound is a binary one (e.g.
  • a second order compound has three components [e.g. R(M-,M 2 )] or (R X ,R 2 )M
  • a third order compound has four components [e.g. (R.,R 2 ) (M X ,M 2 )] and so forth.
  • An illustrative B2 (CsCl-type) ordered crystal structure is illustrated in Figure 1 wherein the corners of the unit cell cube are occupied by the M element and the atom in the cube center is the R element.
  • the R element is selected from one or more rare earth elements.
  • the R element is selected from the group consisting of Sc, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu and combinations thereof.
  • the M element is selected from one or more non-rare earth metals and preferably is selected from the group consisting of Mg, Al, Co, Ni, Cu, Zn, Ru, Rh, Pd, Ag, Cd, In, Ir, Pt, Au, Hg, and Tl and combinations thereof.
  • Table 1 lists the binary RM CsCl-type intermetallic compounds formed by rare earth elements and non-rare earth metals.
  • the M element also can be selected from a metal or a non-metal not mentioned above (e.g. Li, B, C, Si, P, Ga, Ge, etc.) to modify a particular property of the article of manufacture for a particular application and whose concentration is limited to the maximum solid solubility of that metal in the compound such that the compound retains the B2 (CsCl-type) ordered crystal structure.
  • a metal or a non-metal not mentioned above e.g. Li, B, C, Si, P, Ga, Ge, etc.
  • Articles of manufacture are made of binary RM compounds as well as ternary RM compounds, such as (R--R , 1 .
  • RM compounds such as ( - ⁇ R'i- x ) (-LM 1 .- x ) even including (R,R' ...R n ) (M,M ...M ⁇ ) , where the prime designates a different R or M element from the non-prime R or M and where n can be 3 , 4 or more and designates a different R or M element from the other R or M elements of the compound.
  • Table 2 lists binary intermetallic compounds pursuant to another embodiment of the invention, which compounds have the CsCl-type crystal structure and which do not have a rare earth element as a component .
  • Such compounds are selected from the group consisting of a M'M compound and a higher order M'M compound thereof having a B2 (CsCl-type) ordered crystal structure wherein M is one or more different non-rare earth metals.
  • the mechanical behavior of some of these compounds may exhibit high ductility in tension and compression at room (ambient) temperature in ambient air.
  • Most likely ductile candidate compounds include, but are not limited to HgMg, HgSr, LiPb, MgTl, and PuRu. Table 2.
  • the articles of manufacture have high ductility in tension and compression at room (ambient) temperature in ambient air.
  • the articles of manufacture preferably exhibit at least about 5%, more preferably about 10% and greater, tensile elongation prior to fracture when tensile tested at room
  • the invention is not limited to such stoichiometric, so-called line RM or M'M intermetallic compounds and envisions articles made of near-stoichiometric or off-stoichiometric intermetallic compounds as a result of the presence in the intermetallic compound of incidental impurities, such as for example interstitial impurities including H, B, C, N, 0, and F and/or as a result of loss of the R and/or M (or M' and/or M) constituent during melting and other manufacturing steps of the compound so long as the article of manufacture exhibits a high ductility at ambient
  • (room) temperature such as at least 5%, preferably 10% and greater, tensile elongation prior to fracture when tensile tested at room temperature in ambient air pursuant to ASTM test E8-82 and has an ordered CsCl B2 crystal structure.
  • the invention also envisions addition of one or more constituents other than R and M (or M' and M) to the intermetallic compound
  • specimens fabricated of the following binary and ternary RM intermetallic compounds were tested for ductility in a simple hammer and anvil test (if specimen deformed and did not shatter, it was ductile) conducted at room temperature in ambient air: YAg, YCu, CeAg, DyCu, ErAg, ErAu, ErCu, Erlr, HoCu, NdAg, (Tb 0.88 Dy 012 ) Zn, Yin, and YRh. Of these specimens, all were ductile with the exception of (Tb 088 Dy 012 ) Zn.
  • the specimens for ductility tests were prepared by arc-melting and solidifying the melted material on a water-cooled hearth to produce a disk-like shape with a rounded top and flat bottom and a diameter of about 10 mm.
  • a sealed crucible such as Ti, V, Zr, Nb, Mo, Hf, Ta, W, BN, refractory oxide materials, etc.
  • a sealed crucible such as Ti, V, Zr, Nb, Mo, Hf, Ta, W, BN, refractory oxide materials, etc.
  • RM and M M (and higher order compounds) which are polymorphic (including but not limited to ScAl, SmCu, ErPd, CeAg, YbAg, Gdln, RAu, LiPb) rapid solidification techniqures, such as splat cooling, melt spinning, roller quenching, liquid quenching, vapor quenching, sputtering, flash evaporation, etc., may be necessary to retain the high temperature B2 phase.
  • polymorphic including but not limited to ScAl, SmCu, ErPd, CeAg, YbAg, Gdln, RAu, LiPb
  • rapid solidification techniqures such as splat cooling, melt spinning, roller quenching, liquid quenching, vapor quenching, sputtering, flash evaporation, etc.
  • Articles of manufacture fabricated of ScM intermetallic compounds such as ScMg, ScAl, ScCo, ScNi, ScCu, ScZn, ScRu, ScRh, ScPd, ScAg, ScCd, Sclr, ScPt, ScAu, ScHg and ternary alloys such as Sc(M x M' 1 _ x ) and (Sc x R' 1 _ x )M have considerable interest since most of these compounds melt congruently above 1000 degrees C, making them attractive for fabrication into articles of manufacture for use at high temperatures . For example, all of these compounds melt congruently, except ScCo which melts incongruently.
  • ScAl melts at 1300 degrees C; ScCo melts at 1050 degrees C; ScNi melts at about 1300 degrees C; ScCu melts at 1125 degrees C; ScRu melts at 2200 degrees C; ScPd melts at 1600 degrees C; ScAg melts at 1230 degrees C; ScPt melts at about 2200 degrees C.
  • articles of manufacture fabricated of ScAl, ScNi, ScCu, ScRu, and ScAg appear to be candidates for high temperature service applications.
  • An article of manufacture fabricated of ScAl is attractive for aerospace applications because of its low density (about 3.0 g/cm 3 for ScAl) .
  • Articles of manufacture fabricated of ScRu and ScPt are attractive for high temperature service applications as a result of the extremely high melting points (about 2200 degrees C for ScRu and ScPt) .
  • An article of manufacture fabricated of LuRu having a melting point of 2200 degrees C is also attractive for high temperature service applications as a result of the extremely high melting point of LuRu.
  • the articles of manufacture pursuant to the invention thus may be used over wide ranges of temperatures depending upon the particular RM or M'M intermetallic compound from which the article is fabricated. From an engineering perspective, such articles of manufacture can provide improved high temperature strength, stiffness, and oxidation resistance, yet they would be deformable at room temperature and resist brittle fracture as a result of their high ductility.
  • Articles of manufacture pursuant to the invention can be fabricated of the ordered RM intermetallic compounds by melting the pure R element (s) and pure M element (s) together to form a melt and casting the melt into a mold or die to form a shaped polycrystalline or single crystal article of manufacture.
  • M'M compounds can be conducted using conventional arc-melting procedures under vacuum or under inert gas atmosphere in crucibles comprising any suitable refractory, ceramic or other material that is not adversely reactive with the melt.
  • the melt can be conventionally cast into a mold, which may comprise a metal mold or die, a refractory mold, a ceramic mold, or any other suitable mold.
  • Ingots or other bodies of the RM or M'M intermetallic compound can be made and forged, rolled, or otherwise plastically hot or cold worked or deformed to a suitable shape of an article of manufacture as a result of the ductility of the RM or M'M material.
  • Powders of the RM or M'M intermetallic compound can be made by standard techniques, such as including but not limited to gas atomization and plasma rotating electrode processes and consolidated by conventional processes such as hot or cold isostatic compression, pressing and other powder consolidation processes into a suitable shape of an article of manufacture as a result of the ductility of the RM or M'M material.
  • Example 1 Polycrystalline specimens of equiatomic YAg were produced by arc-melting the pure elements on a water-cooled copper hearth in an inert gas (Ar) atmosphere to form an ingot in the shape of a finger or disk depending on the shape of the mold in the copper hearth.
  • the specimens comprised 50 atomic % Y and 50 atomic % Ag.
  • X-ray diffraction and metallography studies of the cast specimens confirmed that they were single- phase with fully ordered CsCl-type crystal structure.
  • the cast specimens were annealed for 86 kiloseconds at 800 degrees C and machined into cylindrical tensile test specimens, which were tensile tested to failure in room temperature air at a strain rate of 2xl ⁇ "4 /second.
  • Figure 2 is a representative stress-strain curve for the machined YAg specimens. Also shown in Figure 2 is a stress- strain curve for a commercially available aluminum alloy (3105) widely used for gutters, downspouts, window frames and siding.
  • the machined YAg specimen unexpectedly and surprisingly exhibited a large tensile elongation (more than 20% increase in length prior to fracture) comparable to that exhibited by the Al 3105 alloy.
  • Figure 3 is a transmission electron micrograph of dislocation structures in a plastically deformed (27% elongation) YAg specimen.
  • Example 2 Polycrystalline specimens of nearly equiatomic YCu- 005 were produced by arc-melting the pure elements on a water-cooled copper hearth in an inert gas (Ar) atmosphere to form an ingot in the shape of a finger or disk depending on the shape of the mold in the copper hearth.
  • This specimen was made with a starting composition of Y ⁇ . 000 Cu 1 D05 because small losses of Cu occur during arc-melting through vaporization, and this starting composition yields a final cast specimen that is close to the perfect 1:1 stoichiometry.
  • X-ray diffraction and metallography studies of the cast specimens confirmed that they were single-phase with fully ordered CsCl-type crystal structure.
  • the cast specimens were annealed for 36 kiloseconds at 700 degrees C and machined into cylindrical tensile test specimens, which were tensile tested to failure in room temperature air at a strain rate of 2xl0 " /second.
  • Figure 4 is a representative stress-strain curve for the machined YCu specimens .
  • the machined YCu specimens unexpectedly and surprisingly exhibited a large tensile elongation (more than 12% increase in length prior to fracture) .
  • Example 3 Eight single crystal YCu tensile specimens were produced by the well known Bridgman (power-down) technique where a YCu melt in a mold or crucible is directionally solidified therein by gradually reducing induction heating power along the length of the melt to form a single crystal body.
  • the tensile specimens were machined from the single crystal cast bodies and polished by 0.25 micron diamond abrasive in an oil suspension. All eight tensile specimens had a tensile axis of direction [142] with polished surfaces corresponding to the (-812) and (-2 6 -11) planes.
  • the specimens were pulled in tension at room temperature (22 degrees C) in air at a strain rate of lxlO ' Vsecond.
  • the specimens exhibited a yield stress of 45 MPa and fractured at 6% to 8% elongation at a stress of 75 to 90 MPa.
  • Figure 5 is an optical photomicrograph of slip bands on the surface of an YCu single crystal test specimen deformed 6% in tension at 22 degrees C.
  • the intersecting lines are slip bands resulting from dislocation motion on the ⁇ 100 ⁇ and ⁇ 101 ⁇ crystal planes. On both slip planes, the slip direction was
  • Example 4 Polycrystalline specimens of equiatomic DyCu were produced by arc-melting the pure elements on a water-cooled copper hearth in an inert gas (Ar) atmosphere to form an ingot in the shape of a finger or disk depending on the shape of the mold in the copper hearth.
  • the specimens comprised 50 atomic % Dy and 50 atomic % Cu.
  • X-ray diffraction and metallography studies of the cast specimens confirmed that they were single- phase with fully ordered CsCl-type crystal structure.
  • the cast specimens were annealed for 43 kiloseconds at 600 degrees C and machined into cylindrical tensile test specimens, which were tensile tested to failure in room temperature air at a strain rate of 2xl0 "4 /second.
  • Figure 6 is a representative stress-strain curve for the machined DyCu specimens .
  • the machined DyCu specimen unexpectedly and surprisingly exhibited a large tensile elongation (more than 14% increase in length prior to fracture) .
  • Example 5) Polycrystalline specimens of equiatomic ErCu were produced by arc-melting the pure elements on a water-cooled copper hearth in an inert gas atmosphere (Ar) to form an ingot in the shape of a finger or disk depending on the shape of the mold in the copper hearth.
  • the specimens comprised 50 atomic % Er and 50 atomic % Cu.
  • X-ray diffraction and metallography studies of the cast specimens confirmed that they were single- phase with fully ordered CsCl-type crystal structure.
  • the cast specimens were machined into cylindrical compressive test specimens, which were subjected in room temperature air to the true strains of 10.4%, 14.1%, and 20.5% at a strain rate of 2.8xl0 "4 /second.
  • Figure 7 shows the comparison of the deformed specimens at 14.1% (b) and 20.5% (c) true strains with the undeformed specimen (a) .
  • the most remarkable feature is the fact that although ErCu was deformed to greater than 20% true strain (c) , no macroscopic cracks were generated.
  • a summary of the mechanical properties of the deformed ErCu is given in Table 3.
  • Example 6 Fracture toughness is an important mechanical property when assessing possible engineering applications for intermetallic compounds.
  • K IC plane strain fracture toughness
  • J IC material toughness near the onset of crack extension from a preexisting fatigue crack
  • the few measurements that have been reported have been taken from composite materials comprised of mixed ductile and intermetallic phases or from intermetallic compounds that are off-stoichiometry .
  • toughness is usually estimated by the Palmqvist method or by Charpy testing rather than the more time consuming ASTM standard tests (i.e. ASTM E 399-90 or ASTM E 813-89) used on conventional metals.
  • ASTM tests are poorly suited to measurement of brittle materials, and most intermetallics have low tensile ductility in air at ambient temperature .
  • the room temperature fracture toughness was measured for YCu, DyCu, and YAg specimens. Standard tensile tests indicated that YCu was the least ductile of these three intermetallics (11% elongation at failure) ; DyCu had an intermediate ductility (16% elongation at failure) ; while YAg was the most ductile (20% elongation at failure) .
  • the K IC value was determined directly for YCu using ASTM test method E 399- 90; J IC values were measured using ASTM test method E 813-89 for DyCu and YAg, and these J IC values were converted to K IC values. The K IC values were found to be 12.0 MPa m for YCu,
  • buttons of YCu, DyCu, and YAg were prepared from high-purity Dy (99.94 wt.%), Y (99.94 wt.%), Cu (99.99 wt.%), and Ag (99.994 wt.%).
  • the top of each button was milled slightly to produce a flat for rolling, and each button was encapsulated in a stainless steel can that was welded shut inside a dry Ar atmosphere glove box.
  • the canned buttons were then hot rolled at 700 C to reduce specimen thickness from 16 mm to 13 mm. After rolling the stainless steel cans were removed, and fracture toughness compact tension specimens (CT) were cut from the rolled buttons by electrodischarge machining (EDM) to the dimensions shown in Figure 8.
  • CT fracture toughness compact tension specimens
  • the specimens were extracted from the T-L position (i.e. the specimen is machined to align the crack plane parallel to the rolling direction) .
  • the finished specimens had overall dimensions of 30 mm x 29 mm x 10 mm, with W equal to 24 mm and thickness (B) equal to 10 mm.
  • After machining, specimens were wet polished to 800-grit finish, followed by a final polishing step using 1 ⁇ m diamond paste.
  • EDM line cutting was then used to produce a notch with root radius, r, equal to 0.125 mm.
  • Samples were then fatigue precracked using a servo-hydraulic MTS machine in room air in cyclic loading using a sinusoidal wave of 5 Hz. During the fatigue pre-cracking a nominal stress intensity range was 5-10 MPa with an R ratio of 0.1. The final fatigue crack lengths were in the range of a/W -0.45-0.55. Fatigue crack advance was monitored by a traveling optical microscope.
  • K IC Fracture toughness
  • the specimen was first pulled to determine the initial crack length, and then loaded by a repeated loading and partial- unloading scheme.
  • the tests were performed in air under displacement control, with the displacement rate of 0.002 mm/s as recommended in the standard.
  • a clip gauge was used to detect front-face crack opening displacement, and this value was later converted to load-line displacement for the J IC calculation.
  • the K IC testing result for YCu is shown in Figure 10.
  • the critical Load P Q was obtained using the 5% secant deviation technique specified by the standard. From the P Q value, the K Q value was determined using the standard stress intensity factor calibration function for compact tension specimens as described in the standard:
  • P Q is the load at fracture instability
  • B is the specimen thickness
  • W is the specimen width
  • a is the notch plus crack length
  • f (a/W) is a dimensionless function:
  • the K IC and J IC values determined in this example are summarized in the Table 4 below.
  • K IC values for YAg and DyCu were calculated from the J IC values .
  • Figure 14a and 14b show the mean grain size in DyCu J IC specimen was quite small, e.g. 0.2 ⁇ m. Fine grain size tends to increase fracture toughness by minimizing dislocation pile- up stresses. It is significant to note that the CT specimen fracture surfaces shown in Figure 15 display no evidence of intergranular fracture .
  • Example 7 Further single crystal specimens of YCu with the B2-type crystal structure were tested in tension and in compression, and isostructural single crystal specimens of B2 (Tb 088 Dy 012 ) Zn were tested in tension.
  • single crystals of YCu and (Tb 088 Dy 012 ) Zn were grown in sealed Ta crucibles by the conventional Bridgman (power down) technique.
  • the rare earth metals used in this study were obtained from the Department of Energy, Ames Laboratory Materials Preparation Center, Ames, Iowa, and they were 99.9 at . % pure.
  • the Cu and Zn (both 99.99% purity) were purchased from Copper and Brass Sales, and Cerac, respectively.
  • YCu the starting ingots for single crystal growth were prepared by arc-melting appropriate quantities of Y and Cu under an Ar atmosphere. The buttons were remelted several times, turning the button between melts. Finally, the alloy was drop cast into a Cu chill cast mold to ensure compositional homogeneity throughout the ingot.
  • the YCu was placed inside the Ta Bridgman crucible and then sealed by electron beam welding a Ta lid onto the crucible.
  • Tb, Dy, and Zn were co-melted in a sealed Ta crucible under slightly less than 100 kPa of Ar. This crucible was then heated to 1475 K, cooled, and inverted before re-heating. This sequence of melting was repeated twice before crystal growth began to provide a complete and homogeneous mixing of the elemental constituents.
  • the crucibles containing the alloys were heated under a pressure of 1.3 x 10 "4 Pa up to 1075 K to degas H from the crucible.
  • the chamber was then backfilled to a pressure of 275 kPa with high purity Ar.
  • the ingot was then further heated to the growth temperature and held for 3.6 ks (1 hr) to allow thorough mixing before withdrawing the sample from the heat zone at a rate of 1.1 ⁇ m/s.
  • X-ray diffraction analysis confirmed the crystals' single-phase, fully ordered B2 structure.
  • the single crystals' orientations were determined using Laue X-ray back reflection analysis, and the specimens were cut into tensile specimens (Figure 16) and compression specimens by electro-discharge machining. Following machining the orientations of the specimens were again checked by Laue X-ray back reflection analysis, and the sides of the specimens' gauge length were polished using 1 ⁇ m diamond paste in an oil suspension.
  • the serrations from discontinuous yielding on the stress- strain plots and the acoustic reports could be caused by twinning, kink band formation, or by a stress-induced transformation to another crystal structure.
  • the YCu B2 crystal structure has been reported as the equilibrium structure at room temperature; however, at low temperature
  • X-ray diffraction (XRD) analysis was performed on the compression specimen labeled "2" in Figure 20 in an effort to determine the cause of the discontinuous yielding.
  • Laue X-ray back reflection analysis was inconclusive due to the similarity in the diffraction patterns of single crystal B2 (cubic) and B27 (orthorhombic) structures.
  • Differential scanning calorimetry (DSC) was performed from 300 K to 1475 K on the material taken from the distorted region of specimen #2, and an exothermic event at 455 K was observed that could be associated with the transformation from B27 phase to B2 phase.
  • the B2 phase is the more stable phase at elevated temperature.
  • DSC was also performed on an YCu single crystal not subjected to tensile or compression testing and on an YCu single crystal specimen that had been tensile tested. Neither of those DSC patterns displayed an exothermic event at 455 K, findings that are consistent with the conclusion that the discontinuous yielding was caused by transformation to the B27 phase induced by the high compressive stress. This issue requires further study before the cause of the discontinuous yielding can be determined with certainty.
  • a given slip system (e.g. the ⁇ l0l ⁇ 010>) contains several individual planes (e.g. the (101), (110), (101), etc.), and each of those planes contains two or more possible slip directions (e.g. the [010], [001], etc.). Since the critical resolved shear stress ( ⁇ CRSS ) for slip is the same for every member of a given slip family, the particular plane and direction of that slip system that actually does slip as plastic flow begins in the tensile test will be the combination with the highest Schmid factor.
  • [111] (101) is considerably smaller than the Schmid factors of other possible candidates in Table 9c, indicating that the ⁇ 111> is an unlikely slip direction for the ⁇ 101 ⁇ planes.
  • the [142] tensile axis orientation produces high Schmid factors for the ⁇ 100 ⁇ 010> and ⁇ ll ⁇ 010> slip systems. If a second test could be performed on single crystal YCu with an orientation that produced a zero Schmid factor for these two slip systems, it might be possible to determine whether other, secondary slip systems are also active at room temperature (possibly with higher values of ⁇ CRSS ) . If additional slip system (s) were found to be active, the total number of independent slip systems in YCu could be sufficient to satisfy the von Mises criterion.
  • Figure 22 shows a comparison of the anisotropy factor
  • the RM intermetallic compounds, YAg, YCu, and DyCu, pursuant to the invention are more isotropic in having an elastic anisotropy value A "12 of about 1 (e.g. 0.8 to 1.0) compared with the strong anisoptropy (e.g. A "12 greater than 1.2 or less than 0.75) of the ionic compounds and the non-RM intermetallic compounds shown in Figure 22.
  • the present also involves a method of making an article of manufacture by plastically deforming a body comprising an intermetallic compound described above; for example, wherein the compound is selected from the group consisting of an RM compound and a higher order compound thereof having a CsCl-type ordered crystal structure wherein R is one or more rare earth elements and M is one or more non-rare earth metals and is also selected from the group consisting of a M'M compound and a higher order compound thereof having a CsCl-type ordered crystal structure wherein M' and M are one or more different non-rare earth metals.
  • the compound is selected from the group consisting of an RM compound and a higher order compound thereof having a CsCl-type ordered crystal structure wherein R is one or more rare earth elements and M is one or more non-rare earth metals and is also selected from the group consisting of a M'M compound and a higher order compound thereof having a CsCl-type ordered crystal structure wherein M' and M are one or more different non-rare earth metals.
  • a specimen of YAg intermetallic compound was deformed by rolling at room temperature from an initial thickness of 0.094 inch (2.39 mm) to a final thickness of 0.011 inch (0.28 mm). This deformation is an 88% reduction by cold rolling. The plastic deformation was conducted with no stress relief annealing to provide for recrystallization. The specimen strip showed only a modest amount of edge cracking of the sort typically seen in cold rolled copper or steel. The central 80% of the rolled specimen strip was free of cracks .
  • a specimen of YCu intermetallic compound was deformed by rolling at elevated temperature (700 degrees C) from an initial thickness of 0.35 inch (9.0 mm) to a final thickness of 0.079 inch (2.0 mm). This deformation is a 78% reduction by hot rolling.
  • the specimen was enclosed in a Ta-lined stainless steel can to prevent oxidation of the surface of the YCu. After hot rolling, the specimen was cold rolled an additional 15% to a final thickness of 0.067 inch (1.7 mm); the cold rolled specimen strip was 5.3 inches (135 mm) long and 0.79 inch (20 mm) wide. When the specimen strip was removed from the stainless steel can, it was almost completely free of any edge cracks. A few very small edge cracks approximately 0.1 inch (2.5 mm) deep were visible; the center section of the specimen strip had no cracks or flaws at all.

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Abstract

L'invention concerne un article de fabrication obtenu par déformation plastique d'un composé intermétallique comprenant R et M, notamment un composé intermétallique RM et son composé d'ordre supérieur, présentant une structure cristalline ordonnée de type CsCl, dans laquelle R désigne un ou plusieurs lanthanides et M désigne un ou plusieurs non-lanthanides. L'article de fabrication fait preuve d'un allongement à la tension d'au moins environ 5 % avant fracture, lorsque la tension est testée à température ambiante dans l'air ambiant. L'article de fabrication peut également être fabriqué par déformation plastique d'un composé intermétallique comprenant un composé M′M et son composé d'ordre supérieur ayant une structure cristalline ordonnée de type CsCl, dans laquelle M' et M désignent un ou plusieurs non-lanthanides différents.
PCT/US2003/035575 2002-11-13 2003-11-10 Articles intermetalliques de fabrication faisant preuve d'une aptitude au pliage elevee a temperature ambiante Ceased WO2004044249A2 (fr)

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WO2009116867A3 (fr) * 2008-03-21 2009-11-12 Asml Netherlands B.V. Matériau cible, source, appareil lithographique euv et procédé de fabrication du dispositif l’utilisant
CN101978791B (zh) * 2008-03-21 2014-06-25 Asml荷兰有限公司 靶材、源、euv光刻设备和使用该设备的器件制造方法

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