US3773549A - Ceramic coated porous metal structure and process therefor - Google Patents

Ceramic coated porous metal structure and process therefor Download PDF

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Publication number
US3773549A
US3773549A US00203364A US3773549DA US3773549A US 3773549 A US3773549 A US 3773549A US 00203364 A US00203364 A US 00203364A US 3773549D A US3773549D A US 3773549DA US 3773549 A US3773549 A US 3773549A
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porous metal
ceramic
metal structure
containing material
coating
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R Elbert
E Farrier
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Chromalloy Gas Turbine Corp
Union Carbide Corp
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Union Carbide Corp
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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C24/00—Coating starting from inorganic powder
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
    • C23F15/00—Other methods of preventing corrosion or incrustation
    • 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
    • Y10T428/29—Coated or structually defined flake, particle, cell, strand, strand portion, rod, filament, macroscopic fiber or mass thereof

Definitions

  • Porous metal structures such as porous sheets, are admirably suited for use in such applications as filters, abradable seals, sound suppression structures, bearings and bearing retainers, energy absorbing material and the like.
  • One disadvantage of porous structures is that the metal component of the structure, while being relatively oxidation resistant when present in the bulk state in the temperature range of up to lOC, is subject to oxidation when fabricated into a porous state because of its fine structure and extensive surface area.
  • porous metal structures are somewhat limited in their applications to uses wherein they will not be exposed to high temperature oxidizing environments.
  • Abradable seals and bearing materials which are designed for aerospace applications or the like are intended to 'be subjected to oxidation environments thus curtailing their useful and functional life.
  • One of the primary objectives 'of this invention is' to provide an oxidation resistant coating for porous metal structures composed of a ceramic-containing material which will not adversely affect the abradability of porous metal structures when intended for abradable seal applications and will extend the maximum oxidation protection temperature of porous structures intended for bearing applications.
  • the invention relates to an oxidation resistant ceramic-containing coating for porous metal structures that will not substantially affect the abradability of such structures when intended for abradable seal application usage, nor substantially affect the characteristics required of porous structures intended for bearing application or filter usage.
  • the process for applying an oxidation resistant ceramic coating on a porous metal structure would initially entail preparing a colloidal-like suspension of a finely ground ceramic-containing material in a liquid suspending vehicle.
  • the colloidal-like suspension can then be deposited on a porous metal structure to be coated, after which the coated structure is dried to substantially remove the liquid suspending vehicle thereby leaving a dispersed deposition of the ceramiccontaining material on the walls of the accessible pores throughout the structure.
  • the ceramiccontaining material dispersed on the porous metal structure is heated to a temperature below the melting point of the metal components of the porous metal structure, but sufficient to cause the ceramiccontaining material to fuse and wet the wall surfaces of the pores in the structure.
  • the porous metal structure will have a ceramic coating which will act as a barrier so as to minimize attack of foreign gases, such as oxygen, on the metal.
  • a ceramiccontaining coating on porous structures usually between about 0.01 micron and about 10 microns thick and preferably between about 0.01 micron and about 5 microns thick would be admirably suited for abradable seal applications.
  • a ceramic-containing coating on porous structures between about 1 micron and about 30 microns would be suitable.
  • the exact coating thickness on a porous metal structure for a particular application can be determined by any artisan, familiar with porous materials, using the process of this invention.
  • Colloidal-like suspension is intended to mean a suspension of finely ground particles wherein said particles are substantially uniformly dispersed throughout the suspending liquid and are sized to less than 10 micron particle size.
  • a porous metal structure having a nominal pore size of l00 microns or less can be fabricated by known techniques using any metal or metal alloy that is available in powdered, flaked, or fibrous-form and that can be sintered with substantially uniformly controlled pore sizes ranging anywhere from submicronic to 100 microns and higher.
  • alloy compositions suitable for porous metal abradable'seals include such alics, glass and glass ceramics, in any and all proportions and combinationsjCeramics are basically a class of inorganic, nonmetallic substances as opposed to organic or metallic substances.
  • a suitable ceramic-containing material can be selected as the coating material.
  • a suitable ceramic-containing material could be selected from at least one material selected from the group consisting of silicon dioxide, chromium oxide, titanium oxide, aluminum oxide, boron oxide, sodium oxide, and potassium nitrate.
  • various other ceramic groups can be used such as the oxides, carbides, borides, nitrides, and silicides of such materials as aluminum, magnesium, sodium, lithium, beryllium, cesium, titanium, zirconium, hafnium, tungsten, molybdenum, iron, cobalt, and the like.
  • a preferred method of coating porous metal structures is to first pulverize the ceramic-containing material and then suspend it in a liquid suspending vehicle to form a colloidal-like suspension.
  • the liquid suspending vehicle with the substantially dispersed ceramiccontaining material can then be deposited on the surface of a porous structure by any conventional technique such as painting, spraying, rolling, or dipping the structure into the colloidal-like suspension.
  • the technique for depositing the colloidal-like suspension on and in the porous structure should be adequate so that a layer of the solution is applied to the surface of the porous structure including the internal walls of accessible pores.
  • the coated porous metal structure can be slightly heated, or dried at room temperature, so as to substantially remove the liquid suspending vehicle from the ceramic-containing material so that the latter will be left adhering to the surface of the porous structure. Thereafter, the structure is subjected to a heated environment at a temperature sufficient to cause the ceramic-containing material to assume a molten state whereupon it will fuse and wet the surface of the porous structure providing the substantially uniform layer thereon.
  • the walls of the internal pores will be substantially protected against the penetration of foreign gases, such as oxygen.
  • the ceramic-containing coating which can be deposited as a thin layer on a porous metal structure, it is necessary to initially pulverize the ceramic-containing material to a size smaller than about microns and preferably less than about 1 micron. It is to be understood that the exact size of the pulverized ceramic-containing material is somewhat dependent on the pore size of the porous metal structure to be coated. Thus, when coating a porous metal structure having a nominal pore size of about 100 microns, it will be desirable to pulverize the ceramiccontaining material to less than about 10 microns, while coating a porous metal structure with a nominal pore size of 10 microns will preferably require the ceramic-containing material to be pulverized to less than about 1 micron.
  • the purpose for pulverizing the ceramic-containing material to a fine fraction is to enable the material to be deposited within the walls of accessible pores in the porous metal structure without substantially plugging the pores.
  • the liquid suspending vehicle can be any liquid capable of suspending the selected pulverized ceramic containing material in a substantially uniformly dispersed manner and which is capable of wetting the metal or metal alloy of the porous structure.
  • the liquid suspending vehicle is added in a sufficient amount to form a slurry with the pulverized ceramic-containing material so that when the colloidal-like suspension is deposited on and in the porous metal structures, it will be substantially removed from the porous metal structure thereby leaving the pulverized ceramic-containing material dispersed on the wall surfaces of the accessible pores in the porous metal structure. It is recommended that the viscosity of the colloidal-like suspension be about centipoises or less and preferably about 10 centipoises.
  • Suitable liquid suspending vehicles are alcohol, alcohol containing liquids, methanol, acetone, heptane, and kerosene.
  • a preferred embodiment of this invention would be to select a ceramic-containing material which has a softening range rather than a melting temperature, such softening temperature range being the preferred operating temperature of the coated porous metal structure.
  • glass type ceramics are admirably suited for use in this invention and preferably those materials having a soft or molten state at temperatures between about l600F and 2300F.
  • the ceramiccontaining material having good oxidation resistant properties is selected, it is finely pulverized and suspended in a slurry or colloidal-like suspension which will wet and fill the pores of the porous structure.
  • ceramic-containing materials can be pulverized to a submicron particle size in a liquid suspending vehicle using nickel base alloy balls in a nickel based alloy container so as to minimize contamination.
  • the mixture can be ball milled for a time sufficient to cause the resulting mixture to approach a colloidal suspension, that being evidenced by no visible separation of the ceramic-containing material in the liquid.
  • the colloidal-like suspension can then be diluted with a liquid suspending vehicle, preferably the same used in the mill operation, to obtain a viscosity of between about 100 centipoises and about 1 centipoise and preferably about 10 centipoises.
  • the viscosity of the colloidal-like suspension can be varied depending on the porous metal structure to be coated.
  • the colloid coated porous structure is then exposed to ambient so as to evaporate substantially all of the liquid suspending vehicle thereby leaving the ceramic-containing material substantially uniformly disposed on the wall surface of the pores in the structure.
  • the ceramic-containing coated porous structure is then heated to the molten state temperature of the ceramic-containing material whereupon the ceramic-containing material substantially fuses and wets the wall surfaces of the accessible pores in the porous structure thus forming a thin protective coating on and within the structure.
  • Ceramiccontainin'g materials having a softening range between about l600F and 2300F should be heated to between about 1800F and 2400F. As stated above, this temperature should be below the melting temperature of the metal components in the porous metal structure.
  • the coated porous structure is thereafter cooled and ready for its intended application.
  • a ceramic-containing material having good oxidation resistant properties at between about 1200F and about 2000F and being soft or molten at temperatures between 1600F and 2000F is ideally suited. It is to be understood that the ceramiccontaining material selected has to be compatible with the metal components of the porous metal structure so that detrimental reactions do not occur. Ceramic mixtures containing SiO Cr O A1 and TiO are admirably suited for this purpose.
  • the above process can be repeated so in effect we have a multiple layer build-up which upon being heated in the final stage will form a substantially homogeneous coating.
  • EXAMPLE 1 A porous metal abradable seal, commercially available as Type AB-l measuring 2 inches by 6 inches and being 0.06 inch thick on an lnconel 600 backing sheet (0.06 inch thick) was obtained from Union Carbide Corporation.
  • This commercial abradable seal fabricated by a diffusion-sintered bonding ofNi alloy (nominal 80% Ni-20% Cr) as disclosed in U. S. copending application Ser. No. 128,182, had a void fraction of 0.65 nominal, a bulk density of 3 grams per cubic centimeter, a tensile strength of 500 pounds per square inch nominal, and a hardness of 91 nominal based on a Rockwell B scale of inch diameter ball at a 15 kilogram load.
  • the abradable seal material was coated with a ceramic mix (cermet) of the following composition:
  • frit 100 grams of frit (commercially available as No. 6210 from the Ferro Composition, Cleveland, Ohio).
  • the abradable seal material was then impregnated with the solution which was applied by a roller technique.
  • the coated abradable seal material was allowed to dry at room temperature for about 8 hours after which it was furnaced in a continuous belt furnace at 1 150C for a period of 30 minutes in a hydrogen atmosphere.
  • the coating material which was applied to the abradable seal material amounted to 0.8 percent of the weight of the coated material.
  • the coated abradable seal material was then subjected to an oxidation environment within a furnace at a temperature of 1600F.
  • the percent weight gained after various exposure times is indicated as Curve 1' on the graph of the drawing.
  • a similar abradable seal material, except lacking the coating of this invention, was also subjected to the same oxidation environment and showed a substantial weight increase over that of the coated abradable seal for similar time periods.
  • Curve 1 on the graph represents the uncoated abradable seal material.
  • a comparison of Curves 1 and l demonstratively reveals the increase in the oxidation resistant characteristics of a porous metal structure coated in accordance with this invention.
  • the coated and uncoated abradable seal materials specified above were subjected to an abradability test utilizing a tester composed of a 7% inch diameter rotating knife edge having a peripheral speed of revolutions per second and designed to plunge at a depth of 0.001 inch per second until a scar ofa 0.030 inch depth was imparted in the material being tested.
  • the horsepower required to produce this 0.030 inch scar in both the coated and uncoated materials was compared and found to be essentially the same, that being about 0.1 of a horsepower.
  • This abradability test was conducted on the materials both before and after the materials were subjected to the oxidation environment. Thus, the ceramic oxidation coating on the abradable seal material produced no detrimental effects to the abradability characteristics of the material.
  • EXAMPLE 2 Abradable seal material similar to that as in Example 1 except that it had a hardness of 85 nominal as measured by a Rockwell B scale with a 54 inch diameter ball under a 15 kilogram load. This material was also fabri cated as disclosed in U. S. copending application Serial No. 128,182 and was commercially obtained from Union Carbide Corporation as Type AB-2 abradable seal material. The abradable seal material measured 2 inches by 6 inches and was 0.06 inch thick on an lnconel 600 backing sheet (0.06 inch thick).
  • Example 2 A ceramic mix identical to that specified in Example 1 was applied to the abradable seal material as also disclosed in Example 1.
  • the coated abradable seal material was then allowed to dry at room temperature for about 8 hours after which it was subjected to a hydrogen atmosphere in a heated environment of a continuous belt furnace at a temperature of 1 C for a period of 30 minutes.
  • the coating material which was added to the abradable seal material amounted to 0.8 percent of the weight of the coated material.
  • the coated abradable seal material was then subjected to an oxidation environment within a furnace at a temperature of 1600F.
  • the percent weight gained after various exposure times is indicated as Curve 11' on the graph of the drawing.
  • a similar abradable seal material, except lacking the coating of this invention, was also subjected to the same oxidation environment and showed a substantial weight increase over that of the coated abradable seal for similar time periods.
  • Curve 1 1 on the graph of the drawing represents the uncoated abradable seal material.
  • a comparison of Curves 11 and 11 demonstratively reveals the increase in the oxidation resistant characteristics of a porous metal structure coated in accordance with this invention.
  • the coated and uncoated abradable seal materials specified above were subjected to an abradability test utilizing a tester composed of a 7% inch diameter rotating knife edge having a peripheral speed of 100 revolutions per second and designed to plunge at a depth of 0.00] inch per second until a scar ofa 0.030 inch depth was imparted in the material being tested.
  • the horsepower required to produce this 0.030 inch scar in both the coated and uncoated materials was compared and found to be essentially the same, that being below 0.1 of a horsepower.
  • This abradability test was conducted on the materials both before and after the materials were subjected to the oxidation environment. Thus, the ceramic oxidation coating on the abradable seal material produced no detrimental effects to the abradability characteristics of the material.
  • the oxidation resistant coating of this invention is also admirably suited for use on porous metal structures having a bimodal pore distribution, that is, a porous structure having two nominal pore sizes.
  • the colloidal-like suspension of ceramic-containing material could be deposited on the structure in a state that would permit the smaller pores to be filled with the coating by capillary action. After drying, the bimodal porous structure would be heated so that the ceramiccontaining material would substantially fuse and wet the walls of the larger pores while substantially filling the cavities of the smaller pores. This would provide the porous structure with a good oxidation resistant coating while not substantially affecting the mechanical properties of the structure.
  • a process for coating porous metal structures having a nominal pore size no greater than 100 microns with an oxidation resistant ceramic-containing material comprising the steps:
  • step (a) depositing a layer of the colloidal-like suspension of step (a) on the surface of the porous metal structure;
  • step (c) said liquid suspending vehicle is substantially removed at room temperature.
  • step (a) said ceramic-containing material is selected from at least one of the groups consisting of oxides, carbides, borides, nitrides, and silicides of aluminum, magnesium, sodium, lithium, beryllium, cesium, titanium, zirconium, hafnium, tungsten, molybdenum, iron and cobalt.
  • step (a) said ceramic-containing material is selected from at least one of the groups consisting of silicon dioxide, chromium oxide, titanium oxide, aluminum oxide, boron oxide, sodium oxide, and potassium nitrate.
  • step (a) said ceramic-containing material has a softening range at a temperature between about 1600F and about 2300F; and wherein in step (d) said porous metal material is heated to a temperature between about 1800F and about 2400F.
  • step (a) said finely ground ceramic-containing material is sized be tween about 0.01 micron and about 10 microns.
  • step (a) said liquid suspending vehicle is selected from at least one of the groups consisting of alcohol, an alcoholcontaining liquid, methanol, acetone, heptane, and kerosene.
  • step (a) has a viscosity of between about centipoises and about 1 centipoise.
  • step (d) said layer of ceramic coating material is between about 0.01 micron and about 10 microns.
  • step (d) said ceramic-containing material is between about 1 micron and about 30 microns thick.
  • a porous metal structure having a nominal pore size no greater than 100 microns and having an oxidation resistant coating of a ceramic-containing material, said coating being deposited substantially on the wall surfaces of the pores in said porous metal structure thereby providing a barrier which substantially minimizes the attack of gases on the metal.
  • porous metal structure of claim 13 intended for abradable seal applications wherein said oxidation resistant coating is between about 0.01 micron and about 10 microns thick.
  • porous metal structure of claim 13 intended for bearing application wherein said oxidation resistant coating is between about 1 micron and about 30 microns thick.

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  • Metallurgy (AREA)
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  • Chemical Kinetics & Catalysis (AREA)
  • Other Surface Treatments For Metallic Materials (AREA)
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US00203364A 1971-11-30 1971-11-30 Ceramic coated porous metal structure and process therefor Expired - Lifetime US3773549A (en)

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JP (1) JPS4864107A (enrdf_load_stackoverflow)
BE (1) BE792075A (enrdf_load_stackoverflow)
CA (1) CA981992A (enrdf_load_stackoverflow)
FR (1) FR2162082B1 (enrdf_load_stackoverflow)
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Cited By (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3922458A (en) * 1972-11-24 1975-11-25 Curran Oils Ltd Vitreous enamelling
US3963502A (en) * 1973-02-02 1976-06-15 P. R. Mallory & Co., Inc. Composition for application to die cavity surface
US4059712A (en) * 1976-01-26 1977-11-22 Bothwell Bruce E Metal-ceramic composite and method for making same
US4059707A (en) * 1975-08-29 1977-11-22 Rca Corporation Method of filling apertures with crystalline material
US4251272A (en) * 1978-12-26 1981-02-17 Union Carbide Corporation Oxidation resistant porous abradable seal member for high temperature service
US4276331A (en) * 1976-01-26 1981-06-30 Repwell Associates, Inc. Metal-ceramic composite and method for making same
US4425411A (en) 1981-05-21 1984-01-10 Swiss Aluminium Ltd. Mold with thermally insulating, protective coating
US4427721A (en) 1977-11-01 1984-01-24 United Kingdom Atomic Energy Authority Method of coating steel substrates to reduce carbonaceous deposition thereon
US4713300A (en) * 1985-12-13 1987-12-15 Minnesota Mining And Manufacturing Company Graded refractory cermet article
US4738874A (en) * 1984-12-28 1988-04-19 Commissariat A L'energie Atomique Process for the production of porous, permeable mineral membranes
WO1989011342A1 (en) * 1988-05-24 1989-11-30 Ceramem Corporation Porous inorganic membrane with reactive inorganic binder, and method of forming same
US5364586A (en) * 1993-08-17 1994-11-15 Ultram International L.L.C. Process for the production of porous membranes
US5996497A (en) * 1998-06-12 1999-12-07 Eastman Kodak Company Method of making a durable hydrophilic layer
WO2000073530A1 (en) * 1999-05-27 2000-12-07 Sandvik Ab; (Publ) Surface modification of high temperature alloys
AU775455B2 (en) * 1999-05-27 2004-08-05 Sandvik Intellectual Property Ab Surface modification of high temperature alloys
US20040253371A1 (en) * 2003-06-10 2004-12-16 Janney Mark A. Filter and method of fabricating
US20060057295A1 (en) * 1999-07-31 2006-03-16 The Regents Of The University Of California Structures and fabrication techniques for solid state electrochemical devices
WO2008046785A2 (de) 2006-10-17 2008-04-24 Robert Bosch Gmbh Verfahren zur stabilisierung und funktionalisierung von porösen metallischen schichten
US20100126133A1 (en) * 2008-11-26 2010-05-27 Curtis Robert Fekety Coated Particulate Filter And Method
US20110104586A1 (en) * 2008-04-18 2011-05-05 The Regents Of The University Of California Integrated seal for high-temperature electrochemical device
US8343686B2 (en) 2006-07-28 2013-01-01 The Regents Of The University Of California Joined concentric tubes
US8445159B2 (en) 2004-11-30 2013-05-21 The Regents Of The University Of California Sealed joint structure for electrochemical device
CN115522145A (zh) * 2021-09-26 2022-12-27 哈尔滨工业大学（威海） 多孔结构的强化工艺及其制品
CN117448657A (zh) * 2023-11-23 2024-01-26 中国核动力研究设计院 一种碳化硼不锈钢复合材料及其制备方法

Families Citing this family (3)

* Cited by examiner, † Cited by third party
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IT1077238B (it) * 1977-06-09 1985-05-04 Montedison Spa Procedimento protettivo per mezzo di vernici inorganiche di superfici metalliche ferrose e non ferrose contro la corrosione da carburazione in alta temperatura eventualmente congiunta a quella di ossidazione
JPS6362802A (ja) * 1986-09-03 1988-03-19 Nippon Tungsten Co Ltd 多孔質金属焼結体
JPH0499184A (ja) * 1990-08-02 1992-03-31 Hino Motors Ltd セラミックコーティング発泡金属体及びその製造方法

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Publication number Priority date Publication date Assignee Title
BE629895A (enrdf_load_stackoverflow) * 1961-09-29 1900-01-01
FR1464965A (fr) * 1965-03-15 1967-01-06 Hexcel Products Inc Procédé de fabrication d'une structure en nid d'abeilles soudée par explosion

Cited By (35)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3922458A (en) * 1972-11-24 1975-11-25 Curran Oils Ltd Vitreous enamelling
US3963502A (en) * 1973-02-02 1976-06-15 P. R. Mallory & Co., Inc. Composition for application to die cavity surface
US4059707A (en) * 1975-08-29 1977-11-22 Rca Corporation Method of filling apertures with crystalline material
US4059712A (en) * 1976-01-26 1977-11-22 Bothwell Bruce E Metal-ceramic composite and method for making same
US4276331A (en) * 1976-01-26 1981-06-30 Repwell Associates, Inc. Metal-ceramic composite and method for making same
US4427721A (en) 1977-11-01 1984-01-24 United Kingdom Atomic Energy Authority Method of coating steel substrates to reduce carbonaceous deposition thereon
US4251272A (en) * 1978-12-26 1981-02-17 Union Carbide Corporation Oxidation resistant porous abradable seal member for high temperature service
US4425411A (en) 1981-05-21 1984-01-10 Swiss Aluminium Ltd. Mold with thermally insulating, protective coating
US4738874A (en) * 1984-12-28 1988-04-19 Commissariat A L'energie Atomique Process for the production of porous, permeable mineral membranes
US4713300A (en) * 1985-12-13 1987-12-15 Minnesota Mining And Manufacturing Company Graded refractory cermet article
US4743511A (en) * 1985-12-13 1988-05-10 Minnesota Mining And Manufacturing Company Graded refractory cermet article
WO1989011342A1 (en) * 1988-05-24 1989-11-30 Ceramem Corporation Porous inorganic membrane with reactive inorganic binder, and method of forming same
US5364586A (en) * 1993-08-17 1994-11-15 Ultram International L.L.C. Process for the production of porous membranes
WO1995005256A1 (en) * 1993-08-17 1995-02-23 Ultram International, L.L.C. Process for the production of porous membranes
US5996497A (en) * 1998-06-12 1999-12-07 Eastman Kodak Company Method of making a durable hydrophilic layer
US6416871B1 (en) 1999-05-27 2002-07-09 Sandvik Ab Surface modification of high temperature alloys
AU775455B2 (en) * 1999-05-27 2004-08-05 Sandvik Intellectual Property Ab Surface modification of high temperature alloys
AU775455C (en) * 1999-05-27 2005-04-21 Sandvik Intellectual Property Ab Surface modification of high temperature alloys
WO2000073530A1 (en) * 1999-05-27 2000-12-07 Sandvik Ab; (Publ) Surface modification of high temperature alloys
KR100706936B1 (ko) * 1999-05-27 2007-04-11 산드빅 인터렉츄얼 프로퍼티 에이비 고온 합금의 표면 개질
US7351488B2 (en) 1999-07-31 2008-04-01 The Regents Of The University Of California Structures and fabrication techniques for solid state electrochemical devices
US8283077B1 (en) 1999-07-31 2012-10-09 The Regents Of The University Of California Structures and fabrication techniques for solid state electrochemical devices
US20060057295A1 (en) * 1999-07-31 2006-03-16 The Regents Of The University Of California Structures and fabrication techniques for solid state electrochemical devices
US7118777B2 (en) 1999-07-31 2006-10-10 The Regents Of The University Of California Structures and fabrication techniques for solid state electrochemical devices
US6998009B2 (en) 2003-06-10 2006-02-14 Ut-Battelle, Llc Filter and method of fabricating
US20040253371A1 (en) * 2003-06-10 2004-12-16 Janney Mark A. Filter and method of fabricating
US8445159B2 (en) 2004-11-30 2013-05-21 The Regents Of The University Of California Sealed joint structure for electrochemical device
US8343686B2 (en) 2006-07-28 2013-01-01 The Regents Of The University Of California Joined concentric tubes
WO2008046785A2 (de) 2006-10-17 2008-04-24 Robert Bosch Gmbh Verfahren zur stabilisierung und funktionalisierung von porösen metallischen schichten
WO2008046785A3 (de) * 2006-10-17 2009-05-07 Bosch Gmbh Robert Verfahren zur stabilisierung und funktionalisierung von porösen metallischen schichten
US20110104586A1 (en) * 2008-04-18 2011-05-05 The Regents Of The University Of California Integrated seal for high-temperature electrochemical device
US8486580B2 (en) 2008-04-18 2013-07-16 The Regents Of The University Of California Integrated seal for high-temperature electrochemical device
US20100126133A1 (en) * 2008-11-26 2010-05-27 Curtis Robert Fekety Coated Particulate Filter And Method
CN115522145A (zh) * 2021-09-26 2022-12-27 哈尔滨工业大学（威海） 多孔结构的强化工艺及其制品
CN117448657A (zh) * 2023-11-23 2024-01-26 中国核动力研究设计院 一种碳化硼不锈钢复合材料及其制备方法

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FR2162082B1 (enrdf_load_stackoverflow) 1975-03-28
FR2162082A1 (enrdf_load_stackoverflow) 1973-07-13
CA981992A (en) 1976-01-20
JPS4864107A (enrdf_load_stackoverflow) 1973-09-05
BE792075A (fr) 1973-05-29
GB1414519A (en) 1975-11-19
DE2258282A1 (de) 1973-06-14
DE2258282B2 (de) 1977-07-07

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