[go: up one dir, main page]

US20050013723A1 - Formation of metallic thermal barrier alloys - Google Patents

Formation of metallic thermal barrier alloys Download PDF

Info

Publication number
US20050013723A1
US20050013723A1 US10/776,473 US77647304A US2005013723A1 US 20050013723 A1 US20050013723 A1 US 20050013723A1 US 77647304 A US77647304 A US 77647304A US 2005013723 A1 US2005013723 A1 US 2005013723A1
Authority
US
United States
Prior art keywords
group
metal
alloying element
atomic
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.)
Abandoned
Application number
US10/776,473
Inventor
Daniel Branagan
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.)
Individual
Original Assignee
Individual
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 Individual filed Critical Individual
Priority to US10/776,473 priority Critical patent/US20050013723A1/en
Publication of US20050013723A1 publication Critical patent/US20050013723A1/en
Priority to US11/324,576 priority patent/US7803223B2/en
Abandoned legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • B22F2009/088—Fluid nozzles, e.g. angle, distance
    • 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
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/31504—Composite [nonstructural laminate]
    • Y10T428/31678—Of metal

Definitions

  • This invention is directed at metallic alloys, and more particularly at unique metallic alloys having low electrical and thermal conductivity. In coating form, when applied, such alloys present the ability to provide thermal barrier characteristics to a selected substrate.
  • Metals and metallic alloys have metallic bonds consisting of metal ion cores surrounded by a sea of electrons. These free electrons which arise from an unfilled outer energy band allow the metal to have high electrical and thermal conductivity which makes this class of materials conductors. Due to the nature of the metallic bonds, metals and metallic alloys may exhibit a characteristic range of properties such as electrical and thermal conductivity. Typical metallic materials may exhibit values of electrical resistivity that generally fall in a range of between about 1.5 to 145 10 ⁇ 8 ⁇ m, with iron having an electrical resistivity of about 8.6 10 ⁇ 8 ⁇ m. Typical values of thermal conductivity for metallic materials may be in a range of between about 0.2 to 4.3 watts/cm° C., with iron exhibiting a thermal conductivity of about 0.8 watts/cm° C.
  • ceramics are a class of materials which typically contain positive ions and negative ions resulting from electron transfer from a cation atom to an anion atom. All of the electron density in ceramics is strongly bonded resulting in a filled outer energy band. Ceramic alloys, due to the nature of their ionic bonding, will exhibit a different characteristic range of properties such as electrical and thermal conductivity. Because of the lack of free electrons, ceramics generally have poor electrical and thermal conductivity and are considered insulators. Thus, ceramics may be suitable for use in applications such as thermal barrier coatings while metals are not.
  • a metal alloy comprising an alloy metal and greater than about 4 atomic % of at least one P-group alloying element.
  • a method of reducing the thermal and/or electrical conductivity of a metal alloy composition comprising supplying a base metal with a free electron density, supplying a P-group alloying element and combining said P-group alloying element with said base metal and decreasing the free electron density of the base metal.
  • a metallic alloy which exhibits relatively low thermal conductivity and a low electrical conductivity.
  • the alloy may include primary alloying metals, such as iron, nickel, cobalt, aluminum, copper, zinc, titanium, zirconium, niobium, molybdenum, tantalum, vanadium, hafnium, tungsten, manganese, and combinations thereof, and increased fractions of P-Group elemental additions in the alloy composition.
  • P-group elements are the non-metal and semi-metal constituents of groups IIIA, IVA, VA, VIA, and VIIA found in the periodic table, including but not limited to phosphorous, carbon, boron, silicon, sulfur, and nitrogen.
  • the metallic alloy exhibiting relatively low thermal conductivity and electrical conductivity may be provided as a coating suitable for thermal and/or electrical barrier applications on a variety of substrates.
  • metallic alloys are provided that exhibit relatively low thermal and electrical conductivity.
  • the alloys according to the present invention may include relatively high fractions of P-group elemental alloying additions in admixture with a metal.
  • the added P-group elements may include, but are not limited to, carbon, nitrogen, phosphorus, silicon, sulfur and boron.
  • the P-group elements may be alloyed with the metal according to such methods as by the addition of the P-group elements to the metal in a melt state.
  • an alloy according to the present invention may include P-group alloying constituents. Such constituents are preferably present at a level of at least 4 at % (atomic percent) of the alloy. Desirably, the alloy consistent with the present invention may include more than one alloying component selected from P-group elements, such that the collective content of all of the P-group elements is between about 4 at % to 50 at %.
  • the alloy may include relatively large fractions of silicon in the alloy composition.
  • an iron/silicon coating alloy can be prepared according to the present invention which coating may be applied, e.g., to any given substrate.
  • the metal alloy may be applied as coating using a thermal spray process.
  • the resulting coating maybe employed to provide a thermal and/or electrical barrier coating.
  • the coating provides thermal and/or electrical barrier properties exhibited similar to a ceramic material, however without the associated brittleness of conventional ceramic coatings.
  • the alloy of the present invention may also be processed by any know means to process a liquid melt including conventional casting (permanent mold, die, injection, sand, continuous casting, etc.) or higher cooling rate, i.e. rapid solidification, processes including melt spinning, atomization (centrifugal, gas,. water, explosive), or splat quenching.
  • a liquid melt including conventional casting (permanent mold, die, injection, sand, continuous casting, etc.) or higher cooling rate, i.e. rapid solidification, processes including melt spinning, atomization (centrifugal, gas,. water, explosive), or splat quenching.
  • melt spinning centrifugal, gas,. water, explosive
  • splat quenching atomization to produce powder in the target size range for various thermal spray coating application devices.
  • the present invention provides a metal alloy that behaves similar to a ceramic with respect to electrical and thermal conductivity.
  • An exemplary alloy consistent with the present invention was prepared containing a combination of several alloying elements present at a total level of 25.0 atomic % P-group alloying elements in combination with, e.g. iron.
  • the experimental alloy was produced by combining multiple P group elements according to the following distribution: 16.0 atomic % boron, 4.0 atomic % carbon, and 5.0 atomic % silicon with 54.5 atomic % iron, 15.0 atomic % chromium, 2.0 atomic % manganese, 2.0 atomic % molybdenum, and 1.5 atomic % tungsten.
  • the experimental alloy was prepared by mixing the alloying elements at the disclosed ratios and then melting the alloying ingredients using radio frequency induction in a ceramic crucible. The alloy was then process into a powder form by first aspirating molten alloy to initiate flow, and then supplying high pressure argon gas to the melt stream in a close coupled gas atomization nozzle. The power which was produced exhibited a Gaussian size distribution with a mean particle size of 30 microns. The atomized powder was further air classified to yield preferred powder sized either in the range of 10-45 microns or 22-53 microns. These preferred size feed stock powders were then sprayed onto selected metal substrates using high velocity oxy-fuel thermal spray systems to provide a coating on the selected substrates.
  • conventional metals and metallic alloys typically cool rapidly from a melt state on a conventional water cooled copper arc-melter, and can be safely handled in a matter of a few minutes.
  • the experimental alloy prepared as described above required in excess of 30 minutes to cool from a melt state down to a safe handling temperature after being melted on a water cooled copper hearth arc-melter.
  • the experimental alloy powder does not transfer heat sufficiently using conventional operating parameters due to its relatively low conductivity and inability to absorb heat.
  • conventional alloys can be sprayed with equivalence ratios (kerosene fuel/oxygen fuel flow rate) equal to 0.8. Because of the low thermal conductivity of the modified experimental alloys, much higher equivalence ratios, in the range of 0.9-1.2, are necessary in order to provide sufficient heating of the power.
  • the very thin deposit (225 ⁇ m thick weld) took excessive time before another layer can be deposited since it glows red hot for an extended time.
  • alloy compositions of the following are to be noted, with the numbers reflecting atomic %: SHS717 Powder, with an alloy composition of Fe (52.3), Cr (19.0), Mo (2.5), W (1.7), B (16.0), C (4.0), Si (2.5) and Mn (2.0); SHS717 wire, with an alloy composition of Fe (55.9), Cr (22.0), Mo (0.6), W (0.4), B (15.6), C (3.5), Si (1.2) and Mn (0.9).
  • the thermal conductivity data for the SHS717 coatings was measured by a Laser Flash method and the results are given in Table 1. Note that the wire-arc conductivity is generally lower than the HVOF due to the higher porosity in the wire-arc coating. Note that the conductivity of the coatings is lower than that of titanium which is the lowest thermal conductivity metal and at room temperature are even lower than alumina ceramic (see Table 2).

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Other Surface Treatments For Metallic Materials (AREA)
  • Coating By Spraying Or Casting (AREA)
  • Conductive Materials (AREA)
  • Chemical Vapour Deposition (AREA)

Abstract

Metal alloys having low electrical and thermal conductivity including relatively large fractions of P-Group element additions. The P-Group elements may be selected from the group including phosphorous, carbon, boron, and silicon. The resultant alloys do not exhibit significantly increased brittleness, and are applied as a coating that provides a metallic thermal barrier coating.

Description

    CROSS REFERENCE TO RELATED APPLICATIONS
  • This application claims priority to U.S. Provisional Application No. 60/446,610 filed Feb. 11, 2003.
    • FIELD OF THE INVENTION
  • This invention is directed at metallic alloys, and more particularly at unique metallic alloys having low electrical and thermal conductivity. In coating form, when applied, such alloys present the ability to provide thermal barrier characteristics to a selected substrate.
    • BACKGROUND OF THE INVENTION
  • Metals and metallic alloys have metallic bonds consisting of metal ion cores surrounded by a sea of electrons. These free electrons which arise from an unfilled outer energy band allow the metal to have high electrical and thermal conductivity which makes this class of materials conductors. Due to the nature of the metallic bonds, metals and metallic alloys may exhibit a characteristic range of properties such as electrical and thermal conductivity. Typical metallic materials may exhibit values of electrical resistivity that generally fall in a range of between about 1.5 to 145 10−8 Ωm, with iron having an electrical resistivity of about 8.6 10−8 Ωm. Typical values of thermal conductivity for metallic materials may be in a range of between about 0.2 to 4.3 watts/cm° C., with iron exhibiting a thermal conductivity of about 0.8 watts/cm° C.
  • By contrast, ceramics are a class of materials which typically contain positive ions and negative ions resulting from electron transfer from a cation atom to an anion atom. All of the electron density in ceramics is strongly bonded resulting in a filled outer energy band. Ceramic alloys, due to the nature of their ionic bonding, will exhibit a different characteristic range of properties such as electrical and thermal conductivity. Because of the lack of free electrons, ceramics generally have poor electrical and thermal conductivity and are considered insulators. Thus, ceramics may be suitable for use in applications such as thermal barrier coatings while metals are not.
  • Designing a metal alloy to exhibit ceramic like electrical and thermal conductivities is unique. The only area where this has been utilized in material science is in the design of soft magnetic materials for transformer core applications. In such applications, extra silicon is added to iron in order to specifically reduce the electrical conductivity to minimize eddy current losses. However, iron-silicon alloys utilized for transformer cores typically contain a maximum of 2.5 at % (atomic percent) silicon because any additional silicon embrittles the alloy. Additionally, attempts to reduce electrical conductivity of iron transformer cores have not addressed reduced thermal conductivity.
    • SUMMARY OF THE INVENTION
  • A metal alloy comprising an alloy metal and greater than about 4 atomic % of at least one P-group alloying element. In method form, a method of reducing the thermal and/or electrical conductivity of a metal alloy composition comprising supplying a base metal with a free electron density, supplying a P-group alloying element and combining said P-group alloying element with said base metal and decreasing the free electron density of the base metal.
    • DESCRIPTION OF THE PREFERRED EMBODIMENT OF THE INVENTION
  • A metallic alloy is provided which exhibits relatively low thermal conductivity and a low electrical conductivity. The alloy may include primary alloying metals, such as iron, nickel, cobalt, aluminum, copper, zinc, titanium, zirconium, niobium, molybdenum, tantalum, vanadium, hafnium, tungsten, manganese, and combinations thereof, and increased fractions of P-Group elemental additions in the alloy composition. P-group elements are the non-metal and semi-metal constituents of groups IIIA, IVA, VA, VIA, and VIIA found in the periodic table, including but not limited to phosphorous, carbon, boron, silicon, sulfur, and nitrogen. The metallic alloy exhibiting relatively low thermal conductivity and electrical conductivity may be provided as a coating suitable for thermal and/or electrical barrier applications on a variety of substrates.
  • Consistent with the present invention, metallic alloys are provided that exhibit relatively low thermal and electrical conductivity. The alloys according to the present invention may include relatively high fractions of P-group elemental alloying additions in admixture with a metal. The added P-group elements may include, but are not limited to, carbon, nitrogen, phosphorus, silicon, sulfur and boron. The P-group elements may be alloyed with the metal according to such methods as by the addition of the P-group elements to the metal in a melt state.
  • Preferably, an alloy according to the present invention may include P-group alloying constituents. Such constituents are preferably present at a level of at least 4 at % (atomic percent) of the alloy. Desirably, the alloy consistent with the present invention may include more than one alloying component selected from P-group elements, such that the collective content of all of the P-group elements is between about 4 at % to 50 at %.
  • Consistent with the present invention, the alloy may include relatively large fractions of silicon in the alloy composition. For example, an iron/silicon coating alloy can be prepared according to the present invention which coating may be applied, e.g., to any given substrate. For example, it has been found that 5.0 atomic % of silicon, and greater, may be incorporated into the alloy without any measurable loss of toughness when employed in a coating application.
  • As alluded to above, consistent with the present invention, the metal alloy may be applied as coating using a thermal spray process. The resulting coating maybe employed to provide a thermal and/or electrical barrier coating. The coating provides thermal and/or electrical barrier properties exhibited similar to a ceramic material, however without the associated brittleness of conventional ceramic coatings.
  • In addition to the use as a coating, the alloy of the present invention may also be processed by any know means to process a liquid melt including conventional casting (permanent mold, die, injection, sand, continuous casting, etc.) or higher cooling rate, i.e. rapid solidification, processes including melt spinning, atomization (centrifugal, gas,. water, explosive), or splat quenching. One especially preferred method is to utilize atomization to produce powder in the target size range for various thermal spray coating application devices.
  • While not limiting the invention to any particular theory, it is believed at the time of filing that by alloying metals with P-group elements, including but not limited to carbon, nitrogen, phosphorus, and silicon, covalent bonds may be formed between the electrons in the P-group alloying element and the free electrons in the base metal, which base metal, as noted, may include iron. The interaction of the free electrons in the base metal in covalent bonds with the P-group alloying elements apparently act to reduce the free electron density of the base metal, and the outer electron energy band of the base metal is progressively filled. Accordingly, by adding significant quantities of P-group elements, the free electron density of the base metal can be continually reduced and the outer electron energy band can be progressively filled. Because the relatively high thermal conductively and electrical conductivity arise from the free electrons in the unfilled outer energy bands of the metal, as the free electron density is reduced, so are the electrical conductivity and the thermal conductivity. Therefore, the present invention provides a metal alloy that behaves similar to a ceramic with respect to electrical and thermal conductivity.
    • Experimental Observations
  • An exemplary alloy consistent with the present invention was prepared containing a combination of several alloying elements present at a total level of 25.0 atomic % P-group alloying elements in combination with, e.g. iron. The experimental alloy was produced by combining multiple P group elements according to the following distribution: 16.0 atomic % boron, 4.0 atomic % carbon, and 5.0 atomic % silicon with 54.5 atomic % iron, 15.0 atomic % chromium, 2.0 atomic % manganese, 2.0 atomic % molybdenum, and 1.5 atomic % tungsten.
  • The experimental alloy was prepared by mixing the alloying elements at the disclosed ratios and then melting the alloying ingredients using radio frequency induction in a ceramic crucible. The alloy was then process into a powder form by first aspirating molten alloy to initiate flow, and then supplying high pressure argon gas to the melt stream in a close coupled gas atomization nozzle. The power which was produced exhibited a Gaussian size distribution with a mean particle size of 30 microns. The atomized powder was further air classified to yield preferred powder sized either in the range of 10-45 microns or 22-53 microns. These preferred size feed stock powders were then sprayed onto selected metal substrates using high velocity oxy-fuel thermal spray systems to provide a coating on the selected substrates.
  • Reduced thermal behavior was observed for the exemplary alloy in a variety of experiments. Specifically, a small 5 gram ingot of the exemplary alloy was arc-melted on a water cooled copper hearth. It was observed that the alloy ingots took longer time for cooling back to room temperature, relative to other alloys which did not contain the P-group composition noted herein. More specifically, the increased time for cooling was on the order of about 20 times longer.
  • Additionally, while conventional metals and alloys that have been heated to high temperatures cool below their red hot radiance level in a few seconds, it was observed that when the exemplary alloy herein was heated to a temperature above the red hot radiance level of the alloy, the red hot radiance persisted for several minutes after removal of the heat source.
  • Similarly, conventional metals and metallic alloys typically cool rapidly from a melt state on a conventional water cooled copper arc-melter, and can be safely handled in a matter of a few minutes. The experimental alloy prepared as described above required in excess of 30 minutes to cool from a melt state down to a safe handling temperature after being melted on a water cooled copper hearth arc-melter.
  • Finally, when thermally sprayed the experimental alloy powder does not transfer heat sufficiently using conventional operating parameters due to its relatively low conductivity and inability to absorb heat. When using high velocity oxy-fuel thermal spray system, conventional alloys can be sprayed with equivalence ratios (kerosene fuel/oxygen fuel flow rate) equal to 0.8. Because of the low thermal conductivity of the modified experimental alloys, much higher equivalence ratios, in the range of 0.9-1.2, are necessary in order to provide sufficient heating of the power. Additionally, when deposited via the LENS (Laser Engineered Net Shape) process, in which a high powered laser is used to melt metal powder supplied to the focus of the laser by a deposition head, the very thin deposit (225 μm thick weld) took excessive time before another layer can be deposited since it glows red hot for an extended time.
  • In the broad context of the present invention alloy compositions of the following are to be noted, with the numbers reflecting atomic %: SHS717 Powder, with an alloy composition of Fe (52.3), Cr (19.0), Mo (2.5), W (1.7), B (16.0), C (4.0), Si (2.5) and Mn (2.0); SHS717 wire, with an alloy composition of Fe (55.9), Cr (22.0), Mo (0.6), W (0.4), B (15.6), C (3.5), Si (1.2) and Mn (0.9).
  • The thermal conductivity data for the SHS717 coatings was measured by a Laser Flash method and the results are given in Table 1. Note that the wire-arc conductivity is generally lower than the HVOF due to the higher porosity in the wire-arc coating. Note that the conductivity of the coatings is lower than that of titanium which is the lowest thermal conductivity metal and at room temperature are even lower than alumina ceramic (see Table 2).
    TABLE 1
    Thermal Conductivity Data for SHS717 Coatings
    Temperature Conductivity
    Coating Type (° C.) (W/m-K)
    HVOF 25 5.07
    HVOF 200 6.93
    HVOF 400 10.0
    HVOF 600 14.2
    Wire-Arc 25 4.14
    Wire-Arc 200 4.78
    Wire-Arc 400 5.48
    Wire-Arc 600 6.94
  • TABLE 2
    Comparative Thermal Conductivity Data
    600° C.
    25° C. (298 K) 400° C. (673 K) (873 K)
    Alloy W/m-K W/m-K W/m-K
    Al 239 227.5  213.5 
    Au 311 270.5  258*  
    Cu 383 367*   352*  
    Fe 79.1  49.11 39.8
    Ni 74.9 63.0 72* 
    Ti 22.0* 14.0 13.3
    .31 wt % 69.5* 26.5 20.0
    Carbon Steel
    .65 wt % 64.7* 23.8 18.7
    Carbon Steel
    .88 wt % 59.0* 22.6 18.5
    Carbon Steel
    British Steel #7 49.6* 38.1 29.9
    White Cast Iron 12.8* 21.8 19.8
    Grey Cast Iron 29.5* 34.1 23.8
    717HV 5.07  10.00  14.20
    717WA 4.14  5.48  6.94
    302 Stainless Steel 12.3 18.6 22.1
    303 Stainless Steel 14.4* 19.7 23.0
    310 Stainless Steel 13.3* 20.1 25.1
    430 Stainless Steel 22.0* 23.3 24.0
    446 Stainless Steel 17.6* 19.8 21.0
    Alumina Ceramic 24.5*  8.2  6.69

    *Approximated Value

Claims (10)

1. A metal alloy comprising an alloy metal and greater than about 4 atomic % of at least one P-group alloying element.
2. A metal alloy of claim 1 wherein the P-group alloying element is present at a level of 4 atomic % to 50 atomic %.
3. The metal alloy of claim 1 wherein said P-group alloying element is selected from the group consisting of carbon, nitrogen, phosphorous, silicon, boron, and mixtures thereof.
4. A metal alloy according to claim 1, wherein said at least one P-group alloying element comprises 16.0 atomic % B, 4.0 atomic % C, and 5.0 atomic % Si.
5. A metal alloy according to claim 1 wherein the alloy metal is selected from the group consisting of iron, chrome, molybdenum, tungsten, manganese, cobalt, nickel, copper, and mixtures thereof.
6. A method for reducing the thermal and/or electrical conductivity of a metal alloy composition comprising:
(a) supplying a metal alloy composition; and
(b) supplying a P-group alloying element;
(c) mixing said metal alloy composition and said P-group alloying element wherein said P-group alloying element is present at a level to reduce the thermal/and or electrical conductivity of said metal alloy composition.
7. A method of reducing the thermal and/or electrical conductivity of a metal alloy composition comprising:
(a) supplying a base metal with a free electron density
(b) supplying a P-group alloying element
(c) combining said P-group alloying element with said base metal and decreasing the free electron density of the base metal.
8. The method of claim 7 wherein the free electron density of the base metal is reduced from its base metal value, and wherein said free electron density is generally representative of a fully filled outer shell after combination with said P-group alloying element.
9. The method of claim 7 wherein said P-group alloying element is selected from the group consisting of carbon, nitrogen, phosphorous, silicon, boron, and mixtures thereof.
10. The method of claim 7 wherein the base metal is selected from the group consisting of iron, nickel, cobalt, aluminum, copper, zinc. titanium, zirconium, niobium, molybdenum, tantalum, vanadium, hafnium, tungsten, manganese, and combinations thereof.
US10/776,473 2003-02-11 2004-02-11 Formation of metallic thermal barrier alloys Abandoned US20050013723A1 (en)

Priority Applications (2)

Application Number Priority Date Filing Date Title
US10/776,473 US20050013723A1 (en) 2003-02-11 2004-02-11 Formation of metallic thermal barrier alloys
US11/324,576 US7803223B2 (en) 2003-02-11 2006-01-03 Formation of metallic thermal barrier alloys

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
US44661003P 2003-02-11 2003-02-11
PCT/US2004/004026 WO2004072313A2 (en) 2003-02-11 2004-02-11 Formation of metallic thermal barrier alloys
US10/776,473 US20050013723A1 (en) 2003-02-11 2004-02-11 Formation of metallic thermal barrier alloys
WOPCT/US04/04026 2004-02-11

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US11/324,576 Continuation US7803223B2 (en) 2003-02-11 2006-01-03 Formation of metallic thermal barrier alloys

Publications (1)

Publication Number Publication Date
US20050013723A1 true US20050013723A1 (en) 2005-01-20

Family

ID=32869539

Family Applications (2)

Application Number Title Priority Date Filing Date
US10/776,473 Abandoned US20050013723A1 (en) 2003-02-11 2004-02-11 Formation of metallic thermal barrier alloys
US11/324,576 Expired - Lifetime US7803223B2 (en) 2003-02-11 2006-01-03 Formation of metallic thermal barrier alloys

Family Applications After (1)

Application Number Title Priority Date Filing Date
US11/324,576 Expired - Lifetime US7803223B2 (en) 2003-02-11 2006-01-03 Formation of metallic thermal barrier alloys

Country Status (6)

Country Link
US (2) US20050013723A1 (en)
EP (1) EP1594644B1 (en)
JP (1) JP5367944B2 (en)
CN (1) CN1758972A (en)
CA (1) CA2515739C (en)
WO (1) WO2004072313A2 (en)

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20040140017A1 (en) * 2000-11-09 2004-07-22 Branagan Daniel J. Hard metallic materials
US20050104867A1 (en) * 1998-01-26 2005-05-19 University Of Delaware Method and apparatus for integrating manual input
US20070107809A1 (en) * 2005-11-14 2007-05-17 The Regents Of The Univerisity Of California Process for making corrosion-resistant amorphous-metal coatings from gas-atomized amorphous-metal powders having relatively high critical cooling rates through particle-size optimization (PSO) and variations thereof
US20070107810A1 (en) * 2005-11-14 2007-05-17 The Regents Of The University Of California Amorphous metal formulations and structured coatings for corrosion and wear resistance
US20070243335A1 (en) * 2004-09-16 2007-10-18 Belashchenko Vladimir E Deposition System, Method And Materials For Composite Coatings
US20070281102A1 (en) * 2006-06-05 2007-12-06 The Regents Of The University Of California Magnetic separation of devitrified particles from corrosion-resistant iron-based amorphous metal powders
US7618500B2 (en) 2005-11-14 2009-11-17 Lawrence Livermore National Security, Llc Corrosion resistant amorphous metals and methods of forming corrosion resistant amorphous metals
US20100019817A1 (en) * 2005-09-06 2010-01-28 Broadcom Corporation Current-controlled CMOS (C3MOS) fully differential integrated delay cell with variable delay and high bandwidth
US20100084052A1 (en) * 2005-11-14 2010-04-08 The Regents Of The University Of California Compositions of corrosion-resistant Fe-based amorphous metals suitable for producing thermal spray coatings
US20110014353A1 (en) * 2005-11-14 2011-01-20 Jor-Shan Choi Corrosion resistant neutron absorbing coatings
CN103898434A (en) * 2014-04-01 2014-07-02 北京工业大学 Heat-insulating coating material for preventing hot-end component of automobile engine, and preparation method thereof
US20220028589A1 (en) * 2018-10-16 2022-01-27 Magneto B.V. Magnetocaloric effect of Mn-Fe-P-Si-B-V alloy and use thereof

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101357855B (en) * 2008-09-12 2012-01-11 西安交通大学 Postprocessing method for improving heat insulating property of ceramic heat barrier coating
JP5626947B2 (en) * 2008-09-22 2014-11-19 独立行政法人物質・材料研究機構 Alloy particles and wires used for atmospheric plasma spraying and hot wire arc spraying
JP5251715B2 (en) * 2009-05-08 2013-07-31 トヨタ自動車株式会社 Internal combustion engine
CN105525199A (en) * 2016-01-20 2016-04-27 广西丛欣实业有限公司 Zinc-plated iron alloy
CN107012411A (en) * 2017-03-08 2017-08-04 宁波高新区远创科技有限公司 A kind of preparation method of soil grounded screen alloy material

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3986867A (en) * 1974-01-12 1976-10-19 The Research Institute For Iron, Steel And Other Metals Of The Tohoku University Iron-chromium series amorphous alloys
US4067732A (en) * 1975-06-26 1978-01-10 Allied Chemical Corporation Amorphous alloys which include iron group elements and boron
US4290808A (en) * 1979-03-23 1981-09-22 Allied Chemical Corporation Metallic glass powders from glassy alloys
US4381943A (en) * 1981-07-20 1983-05-03 Allied Corporation Chemically homogeneous microcrystalline metal powder for coating substrates
US4515870A (en) * 1981-07-22 1985-05-07 Allied Corporation Homogeneous, ductile iron based hardfacing foils
US4523621A (en) * 1982-02-18 1985-06-18 Allied Corporation Method for making metallic glass powder

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5827338B2 (en) * 1974-01-12 1983-06-08 東北大学金属材料研究所長 Fe-Cr amorphous alloy
JPS5841343B2 (en) * 1974-07-01 1983-09-12 トウホクダイガク キンゾクザイリヨウケンキユウシヨチヨウ High strength Fe-Cr amorphous alloy
US4067932A (en) * 1976-06-02 1978-01-10 Stauffer Chemical Company Derivatives of phosphorus-containing aldehydes and ketones
JPS58213857A (en) * 1982-06-04 1983-12-12 Takeshi Masumoto Amorphous iron alloy having superior fatigue characteristic
US4822415A (en) * 1985-11-22 1989-04-18 Perkin-Elmer Corporation Thermal spray iron alloy powder containing molybdenum, copper and boron
SE459863B (en) * 1986-07-04 1989-08-14 Hoeganaes Ab HEAT-INSULATING SINTERED COMPONENT OF YEAR-BASED POWDER AND SET TO MANUFACTURE THIS
DE3876529T2 (en) * 1987-07-31 1993-06-24 Tdk Corp MAGNETIC SOFT IRON POWDER FOR SHAPING MAGNETIC SHIELDING, CONNECTION AND METHOD FOR PRODUCING IT.
SU1615222A1 (en) * 1988-10-31 1990-12-23 Московский станкоинструментальный институт Method of working surface subject to friction
US4965139A (en) * 1990-03-01 1990-10-23 The United States Of America As Represented By The Secretary Of The Navy Corrosion resistant metallic glass coatings
JP3075331B2 (en) * 1993-12-28 2000-08-14 ボルボ コンストラクション イクイップメントコリア カンパニー リミテッド Wear-resistant, corrosion-resistant, heat-resistant mechanical seal
RO111513B1 (en) * 1995-12-27 1999-12-30 Institutul Naţional De Cercetare - Dezvoltare Pentru Fizică Tehnică-Ift Iaşi Amorphous and nano-crystalline magnetic yarns which are covered with glass and preparation process therefor
EP0818549B1 (en) * 1996-06-25 2004-02-04 Castolin S.A. Nickel-based material in powder- or wireform for coating as well as the processes thereof
US6258185B1 (en) * 1999-05-25 2001-07-10 Bechtel Bwxt Idaho, Llc Methods of forming steel

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3986867A (en) * 1974-01-12 1976-10-19 The Research Institute For Iron, Steel And Other Metals Of The Tohoku University Iron-chromium series amorphous alloys
US4067732A (en) * 1975-06-26 1978-01-10 Allied Chemical Corporation Amorphous alloys which include iron group elements and boron
US4290808A (en) * 1979-03-23 1981-09-22 Allied Chemical Corporation Metallic glass powders from glassy alloys
US4381943A (en) * 1981-07-20 1983-05-03 Allied Corporation Chemically homogeneous microcrystalline metal powder for coating substrates
US4515870A (en) * 1981-07-22 1985-05-07 Allied Corporation Homogeneous, ductile iron based hardfacing foils
US4523621A (en) * 1982-02-18 1985-06-18 Allied Corporation Method for making metallic glass powder

Cited By (27)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20050104867A1 (en) * 1998-01-26 2005-05-19 University Of Delaware Method and apparatus for integrating manual input
US8097095B2 (en) 2000-11-09 2012-01-17 Battelle Energy Alliance, Llc Hardfacing material
US7785428B2 (en) 2000-11-09 2010-08-31 Battelle Energy Alliance, Llc Method of forming a hardened surface on a substrate
US20040140017A1 (en) * 2000-11-09 2004-07-22 Branagan Daniel J. Hard metallic materials
US20100015348A1 (en) * 2000-11-09 2010-01-21 Branagan Daniel J Method of forming a hardened surface on a substrate
US20070243335A1 (en) * 2004-09-16 2007-10-18 Belashchenko Vladimir E Deposition System, Method And Materials For Composite Coatings
US7670406B2 (en) 2004-09-16 2010-03-02 Belashchenko Vladimir E Deposition system, method and materials for composite coatings
US20100019817A1 (en) * 2005-09-06 2010-01-28 Broadcom Corporation Current-controlled CMOS (C3MOS) fully differential integrated delay cell with variable delay and high bandwidth
US7618500B2 (en) 2005-11-14 2009-11-17 Lawrence Livermore National Security, Llc Corrosion resistant amorphous metals and methods of forming corrosion resistant amorphous metals
US8187720B2 (en) 2005-11-14 2012-05-29 Lawrence Livermore National Security, Llc Corrosion resistant neutron absorbing coatings
US8778459B2 (en) 2005-11-14 2014-07-15 Lawrence Livermore National Security, Llc. Corrosion resistant amorphous metals and methods of forming corrosion resistant amorphous metals
US20100084052A1 (en) * 2005-11-14 2010-04-08 The Regents Of The University Of California Compositions of corrosion-resistant Fe-based amorphous metals suitable for producing thermal spray coatings
US20070107810A1 (en) * 2005-11-14 2007-05-17 The Regents Of The University Of California Amorphous metal formulations and structured coatings for corrosion and wear resistance
US20110014353A1 (en) * 2005-11-14 2011-01-20 Jor-Shan Choi Corrosion resistant neutron absorbing coatings
US20110165348A1 (en) * 2005-11-14 2011-07-07 Lawrence Livermore National Security, Llc Compositions of Corrosion-resistant Fe-Based Amorphous Metals Suitable for Producing Thermal Spray Coatings
US8075712B2 (en) 2005-11-14 2011-12-13 Lawrence Livermore National Security, Llc Amorphous metal formulations and structured coatings for corrosion and wear resistance
US20070107809A1 (en) * 2005-11-14 2007-05-17 The Regents Of The Univerisity Of California Process for making corrosion-resistant amorphous-metal coatings from gas-atomized amorphous-metal powders having relatively high critical cooling rates through particle-size optimization (PSO) and variations thereof
US20100021750A1 (en) * 2005-11-14 2010-01-28 Farmer Joseph C Corrosion resistant amorphous metals and methods of forming corrosion resistant amorphous metals
US8778460B2 (en) 2005-11-14 2014-07-15 Lawrence Livermore National Security, Llc. Amorphous metal formulations and structured coatings for corrosion and wear resistance
US8480864B2 (en) 2005-11-14 2013-07-09 Joseph C. Farmer Compositions of corrosion-resistant Fe-based amorphous metals suitable for producing thermal spray coatings
US8524053B2 (en) 2005-11-14 2013-09-03 Joseph C. Farmer Compositions of corrosion-resistant Fe-based amorphous metals suitable for producing thermal spray coatings
US8580350B2 (en) 2005-11-14 2013-11-12 Lawrence Livermore National Security, Llc Corrosion resistant neutron absorbing coatings
US8245661B2 (en) 2006-06-05 2012-08-21 Lawrence Livermore National Security, Llc Magnetic separation of devitrified particles from corrosion-resistant iron-based amorphous metal powders
US20070281102A1 (en) * 2006-06-05 2007-12-06 The Regents Of The University Of California Magnetic separation of devitrified particles from corrosion-resistant iron-based amorphous metal powders
CN103898434A (en) * 2014-04-01 2014-07-02 北京工业大学 Heat-insulating coating material for preventing hot-end component of automobile engine, and preparation method thereof
US20220028589A1 (en) * 2018-10-16 2022-01-27 Magneto B.V. Magnetocaloric effect of Mn-Fe-P-Si-B-V alloy and use thereof
US11972883B2 (en) * 2018-10-16 2024-04-30 Magneto B.V. Magnetocaloric effect of Mn—Fe—P—Si—B—V alloy and use thereof

Also Published As

Publication number Publication date
JP5367944B2 (en) 2013-12-11
US7803223B2 (en) 2010-09-28
CN1758972A (en) 2006-04-12
CA2515739A1 (en) 2004-08-26
WO2004072313A3 (en) 2005-06-23
EP1594644A2 (en) 2005-11-16
EP1594644B1 (en) 2013-05-15
EP1594644A4 (en) 2008-03-26
WO2004072313A2 (en) 2004-08-26
US20060110278A1 (en) 2006-05-25
CA2515739C (en) 2012-08-14
JP2006517616A (en) 2006-07-27

Similar Documents

Publication Publication Date Title
US7803223B2 (en) Formation of metallic thermal barrier alloys
US4297135A (en) High strength iron, nickel and cobalt base crystalline alloys with ultrafine dispersion of borides and carbides
EP0511318B1 (en) Plasma spraying of rapidly solidified aluminum base alloys
JPH0474423B2 (en)
TW201418001A (en) Consumer electronically processed housing using a coating that exhibits metamorphic conversion
CN114829655A (en) Method for additive manufacturing of maraging steel
CN110629218A (en) A method for in-situ additive manufacturing of fine-grained high-entropy alloys
CN111742072A (en) Use of aluminum alloys for additive manufacturing
KR20200031132A (en) Copper-based alloys for the production of bulk metallic glass
CN106133185B (en) Sputtering target comprising Ni-P alloy or Ni-Pt-P alloy and manufacturing method thereof
CN108796297B (en) High-strength high-toughness copper-nickel-tin alloy raw material directly used for 3D printing and preparation method and application thereof
CN114787404A (en) Metal Powders for Additive Manufacturing
JPS5942070B2 (en) What is the best way to do this?
CN110396625A (en) A kind of preparation method of antiwear heat resisting aluminium alloy
US11932921B2 (en) Alloy composition, method for producing alloy composition, and die
JP2023130647A (en) Ni-based self-fluxing alloy
WO2021214958A1 (en) Molding powder and molding wire comprising stainless steel
CN110760714A (en) 3D printing copper alloy powder
CN120112376A (en) Metal powders for additive manufacturing
CN113195763B (en) Low thermal expansion alloy excellent in low temperature stability and method for producing the same
JP2023031420A (en) Ni-based self-fluxing alloy
JP7574557B2 (en) Method for producing ferritic stainless steel powder and ferritic stainless steel powder
KR20250093357A (en) Metal Powders for Additive Manufacturing
EP4506478A1 (en) Alloy, alloy powder, alloy member, and composite member
JP7512077B2 (en) Sputtering target material

Legal Events

Date Code Title Description
STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION