WO2001012431A1 - Revetements durs structures multimode realises a partir de materiaux micro-nanocomposites - Google Patents

Revetements durs structures multimode realises a partir de materiaux micro-nanocomposites Download PDF

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Publication number
WO2001012431A1
WO2001012431A1 PCT/US2000/022340 US0022340W WO0112431A1 WO 2001012431 A1 WO2001012431 A1 WO 2001012431A1 US 0022340 W US0022340 W US 0022340W WO 0112431 A1 WO0112431 A1 WO 0112431A1
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Prior art keywords
ceramic
particles
metal
micron
phase material
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PCT/US2000/022340
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English (en)
Inventor
Bernard H. Kear
Ganesh Skandan
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Rutgers, The State University
Nanopowder Enterprises Incorporated
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Publication date
Application filed by Rutgers, The State University, Nanopowder Enterprises Incorporated filed Critical Rutgers, The State University
Priority to US10/049,577 priority Critical patent/US6723387B1/en
Priority to AU70590/00A priority patent/AU7059000A/en
Publication of WO2001012431A1 publication Critical patent/WO2001012431A1/fr

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Classifications

    • 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
    • C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
    • C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
    • C23C4/10—Oxides, borides, carbides, nitrides or silicides; Mixtures thereof
    • 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
    • C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
    • C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
    • C23C4/06—Metallic material
    • 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
    • C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
    • C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
    • C23C4/10—Oxides, borides, carbides, nitrides or silicides; Mixtures thereof
    • C23C4/11—Oxides

Definitions

  • the present invention relates to hardcoatings primarily for use in wear applications and methods for fabricating same by thermal spraying of powder feeds and more particularly to multimodal coatings which are fabricated by thermal spraying aggregated micro/nano-scale feedstock powders.
  • Nano-scale materials Materials with fine-scale structures have long been recognized to exhibit remarkable and technologically attractive properties. Over the past decade, interest has been growing in a new class of materials known as nano-scale materials, that are composed of ultra- fine grains or particles. A feature of nano-scale materials is the high fraction of atoms that reside at grain boundaries or interfaces in the materials, which can have a beneficial effect on properties. Although much of today's research and development activity is focused on the synthesis and processing of nano-scale bulk materials, there is a growing interest in the fabrication of nano-scale coatings.
  • the SCP production method involves essentially three sequential steps: (1) aqueous solution mixing of ammonium metatungstate (source of tungsten) and cobalt acetate (source of cobalt) to fix the composition of a starting solution, (2) spray drying the starting solution to generate a chemically homogeneous precursor powder, and (3) fluid-bed thermochemical conversion (pyrolysis, reduction and carburization) of the precursor powder to a nano-scale WC/Co powder end-product.
  • a feature of the asynthesized nano-scale powder is its characteristic spherical-shell morphology, which is obtained via the spray drying step of the process.
  • each shell-like or hollow particle is highly porous in nature, and is composed of a completely uniform mixture of WC and Co nano-scale grains, typically with a WC grain size of about 30 nm.
  • powder can be used directly as feedstock material in thermal spraying.
  • the powder can be re-processed into solid agglomerates, as taught in U.S. Patent 6,025,034, which gives some advantages in terms of coating quality, e.g. reduced porosity.
  • Powder re-processing involves mechanically milling the asynthesized nano-scale WC/Co powder in an appropriate fluid medium, which breaks up the shell-like particles (10-30 micron diameter) into much smaller fragments (0.1-1 micron diameter). The slurry formed by milling is spray dried to form solid nano-scale particle agglomerates (5-40 micron diameter).
  • asynthesized nano-scale WC/Co powders are used as feedstock powders in high velocity oxy-fuel (HVOF) spraying of nano-scale WC/Co coatings.
  • HVOF high velocity oxy-fuel
  • asynthesized nano-scale WC/Co powders can not be used as feedstock powders in plasma spraying because plasma spraying causes extensive decarburization of the WC phase, due to the much higher temperatures achieved during spraying.
  • Oxide-ceramic powders with fine and ultra-fine particles sizes have traditionally been produced by solution/precipitation methods, however, recent development work has focused on vapor condensation methods. Pioneering work in this field has resulted in the Inert Gas Condensation (IGC) process.
  • ICG Inert Gas Condensation
  • this process which is conducted in a low pressure (typically 1-30 mbar) inert gas environment, nano-scale particles are produced in a thermalizing zone just above the evaporative source, due to interactions between the hot vapor species and the much colder inert gas atoms in the chamber. The particles are convectively transported to and collected on a water-cooled copper plate.
  • ICG Inert Gas Condensation
  • the ICG process is widely used in the production of metal powders, and some metal-oxide powders.
  • CVC Chemical Vapor Condensation
  • a method for producing an abrasion resistant coating composed of a ceramic/metal material system or a ceramic/ceramic material system comprising the steps of: blending micron-scale particles of a hard phase material with nano-scale particles of a binder phase material to form a uniform powder mixture; aggregating of the powder mixture to bond the nano-scale particles to the micron-scale particles thereby forming a feedstock powder comprised of particle aggregates; and thermal spraying the feedstock powder of particle aggregates onto a substrate thereby forming the abrasion resistant coating thereon.
  • Coatings produced by this method are composed of micron-scale particles of the hard phase material fused together with the binder phase material.
  • FIG. 1 shows a block diagram of a method for fabricating ceramic/metal and ceramic/ceramic multimodal coatings according to the present invention
  • FIGS. 2 A and 2B show two types of coarse and fine-grained mixtures
  • FIG. 3 shows a schematic of a dense coating formed by spraying different combinations of coarse and fine powders
  • FIG. 4 shows a chart that compares the abrasion wear resistance of conventional WC/Co coatings with the abrasion wear resistance of multimodal WC/Co coatings of the present invention
  • FIG. 5 A shows a SEM micrograph that illustrates the morphology of a first multimodal powder structure according to the present invention under low magnification (XI, 000);
  • FIG. 5B shows a SEM micrograph that illustrates the morphology of the first multimodal powder structure under high magnification (XI 0,000);
  • FIG. 6A shows an optical micrograph illustrating a polished surface of the multimodal coating of the invention
  • FIG. 6B shows an X-ray diffraction of the coating of FIG. 6 A
  • FIG. 7A shows a SEM micrograph that illustrates the morphology of a second multimodal powder structure according to the present invention under low magnification (XI, 000);
  • FIG. 7B shows a SEM micrograph that illustrates the morphology of the second multimodal powder structure under high magnification (XI 0,000);
  • FIG. 8 A shows an optical micrograph of the surface of a HVOF sprayed coating from mixed powders that were not heat treated.
  • FIG. 8B shows an optical micrograph of the surface of a HVOF sprayed coating from mixed powders that were heat treated.
  • FIG. 1 is a block diagram of a method for fabricating ceramic/metal and ceramic/ceramic multimodal coatings according to the present invention.
  • the coatings are especially useful for wear applications as they exhibit increased abrasion wear resistance while maintaining a reasonable hardness.
  • the first step of the method shown in block 10 involves blending micron-scale (coarse or coarse/fine) particles of a hard phase material with readily fusible nano-scale (ultrafine) particles of a binder phase material to form a powder mixture.
  • the micron-scale particles of hard phase starting material typically comprise a ceramic or a ceramic/metal composite material in aggregate or non- aggregate form. Aggregated particles are clusters of bonded together particles that cannot be easily separated from one another by mechanical means.
  • the nano- scale binder phase starting material typically comprises metal particles, ceramic particles or ceramic/metal composite particles. If the powder mixture employs non-aggregated particles of hard phase starting material, the powder mixture is then agglomerated using any suitable well known particle agglomeration method, such as spray drying, to form particle agglomerates of intimately mixed micron-scale particles of hard phase material and nano-scale particles of binder phase material as shown in FIG. 2A. Agglomerated particles differ from aggregated particles in that they are capable of being mechanically separated from one another.
  • FIG. 2B shows a particle aggregate of hard phase material after blending with the nano-scale particles of binder phase material. As can be seen, the particle aggregate of micron-scale hard ceramic particles is coated with the nano-scale particles of binder phase material.
  • the powder mixture of hard phase/binder phase particle agglomerates (FIG. 2A) or binder phase coated hard phase particles aggregates (FIG. 2B) is heat treated to bond the nano-scale particles to the surfaces of the micron-scale particles.
  • the blended powder is heated in a furnace at an appropriate temperature between 900°C and 1500°C and in a suitable gas atmosphere such as Ar, CH 4 /H 2 .
  • This step produces a feedstock powder comprised of particle aggregates, which are typically about 5-40 microns in size and suitable for thermal spraying.
  • the aggregated feedstock powder is thermally sprayed onto a substrate under controlled conditions.
  • a high velocity oxy-fuel (HVOF) thermal spray gun is used for spraying ceramic/metal coatings. Powders are fed into the gun at a predetermined rate, such rates being well known to ordinary skilled artisans.
  • a plasma torch is used for spraying ceramic/ceramic coatings became of the need to go to a higher temperature. Thermal spraying selectively melts the nano-scale particles of the aggregates, while the micron-scale particles of the aggregates are heated but not necessarily melted.
  • the melted nano-scale particles become a liquid phase binder material that fills the available pore spaces between the heated and softened micron-scale particles hard phase material, hence forming a dense coating on the substrate.
  • the binder phase material provides a strong and tough matrix for the hard phase particles while simultaneously ensuring good bonding between coating and substrate and between the individual splats of in the coating.
  • the thermal spraying step of the method of the invention can be performed using any conventional thermal spraying process that is suitable for the particular aggregated feedstock powder being used.
  • aggregated feedstock powders of ceramic/metal systems such as WC/Co
  • HVOF high velocity oxy-fuel
  • Aggregated feedstock powders of ceramic/ceramic systems such as Al 2 O 3 /TiO 2
  • plasma spray techniques can be thermal sprayed using conventional plasma spray techniques.
  • the choice of operating system for these two different classes of materials is dictated by considerations that are well-known in the thermal spray industry. For example, the lower temperatures and shorter particle residence times characteristic of HVOF spraying enables WC/Co to be spray deposited without causing significant decarburization of the WC phase. Decarburization is recognized to be undesirable because it has an adverse effect on coating properties and performance.
  • the materials systems that are applicable to the method of the invention include a wide variety of ceramic/metal composite materials, such as WC/Co, Cr 3 C /NiCr and TiC/Fe, and ceramic/ceramic composite materials, such as Al 2 O 3 , YSZ (yttria-stabilized zirconia), Al 2 O 3 /TiO 2 , ZrO 2 /Y 2 O 3 , ZrO 2 /Y 2 O 3 -Al 2 O 3 , Cr 2 O 3 , Cr O 3 /SiO .
  • the nano-scale binder phase materials used in the aggregated feedstock powder of the invention can be from virtually any source as purity of the material is not critical.
  • applicable feedstock powders can include any mixture of micron-scale hard phase material and nano-scale binder phase material. Some examples are shown below in Table I.
  • the aggregated feedstock powder can be composed of one, two or more hard phase material particles of different sizes and/or compositions, with a particle size distribution that will provide a high packing density of hard phase material particles in the binder phase material.
  • the aggregated feedstock powder can comprise a bimodal composite structure which includes, for example, a 70:30 mixture of coarse particles of hard phase material (5-30 microns) and ultra- fine nano-scale particles or grains of binder phase material (less than 0.1 micron).
  • the aggregated feedstock powder can comprise a trimodal composite structure which includes, for example, a mixture of coarse particles of hard phase material (5-30 micron), fine particles of hard phase material (0.1-5 micron), and ultra- fine nano-scale particles or grains of binder phase material (less than 0.1 micron).
  • the composite structure can be made up of materials of different compositions. More complex multimodal structures can be envisioned, particularly when the hard phase material constituents in the aggregate particle mass are of different compositions. Table I
  • Aggregate composite systems are well-known in the materials engineering field.
  • An example is concrete, which consists of a mixture of a coarse aggregate such as gravel, a fine aggregate such as sand, and a binder phase such as cement.
  • cement calcium alumino-silicate
  • Typical total aggregate (fine plus coarse) volume fractions in concrete are 0.60 - 0.75. The aggregated particles markedly increase the compressive strength of the concrete and reduce its cost.
  • the aggregated feedstock powders of the present invention are designed for use in combustion-flame or arc-plasma spray guns, where particle residence times in the hot zones of the high velocity gas streams are very short, measured in milliseconds.
  • conventional aggregate composites do not employ the present invention's readily fusible nano-scale binder phase material which serves to bond the aggregated material into a dense coating.
  • FIGS. 3 A and 3B schematically show the dense coatings formed by spraying the aggregated feedstock powders of the invention.
  • Optimal wear properties are achieved when the volume fraction of hard phase particles in the aggregate is high, typically in the range 0.5-0.9.
  • a HVOF gun was used for thermal spraying of ceramic/metal systems
  • a plasma gun was used for thermal spraying of ceramic/ceramic systems. All tests were conducted using WC/Co aggregated feedstock powders in an ambient air environment. Argon shrouding was used when spraying WC/Co aggregated feedstock powder in order to preclude oxidation of the coating material.
  • the materials were characterized by standard metallographic, SEM and X- ray diffraction methods. Hardness measurements were performed on polished sections of powder particles and coatings. In the case of the latter, both transverse and in-plane sections were examined, since it is known that crack propagation around the hardness indentation is more extensive in in-plane sections, because of the relatively weak interfaces between the splat-quenched layers in the coating.
  • FIG. 4 compares the abrasion wear resistance of conventional WC/Co coatings with the abrasion wear resistance of multimodal WC/Co coatings of the present invention.
  • the abrasion wear resistance of the conventional WC/Co coatings falls in band 18 and the abrasion wear resistance of multimodal WC/Co coatings of the present invention falls in band 16.
  • the abrasion wear resistance of the conventional WC/Co coatings like most other materials, scales with hardness, i.e. the higher the hardness, the greater the abrasion wear resistance.
  • the abrasion wear resistance of the multimodal coatings of the present invention advantageously exhibit increased abrasion wear resistance while maintaining a reasonable hardness. This is accomplished in the present invention by manipulating the structure of the starting feedstock powder in the manner described above which provides a strong and tough matrix that holds the coarse particles together.
  • WC particles with a particle size of 2-3 microns were mixed with cobalt powder to achieve a composition of WC/12Co. 70 wt. % of this powder was mixed with 30 wt. % of ball milled nano-scale particles of the same composition, WC/12Co.
  • the particular nano-scale material used in this example is marketed by Nanodyne (now Union Miniere) under the Tradename Nanocarb®.
  • the individual ball milled particles of Nanocarb® were in the size range of 0.1 to 5
  • FIGS. 5A and 5B are SEM micrographs of the multimodal powder morphology.
  • FIG. 5 A shows the multimodal powder mo ⁇ hology under low magnification (XI, 000) and
  • FIG. 5B shows the multimodal powder mo ⁇ hology under high magnification (XI 0,000). The coarse and fine particles are clearly visible.
  • FIG. 6A is an optical micrograph of a polished surface of the resulting multimodal coating
  • FIG. 6B is a corresponding X-ray diffraction of the coating showing that a small amount of decarburization has occurred.
  • the abrasion wear resistance of this coating measured 2.0 x 10 2 Nm mm 3 .
  • a similar test on a conventional coarse grained material gave a wear resistance of only 1.4 x 10 2 Nm mm 3 .
  • the significant enhancement in wear properties is attributed to the presence of a strong and tough matrix that holds the coarse WC particles together.
  • micron-scale component can have a composition ranging from WC/lCo to WC/12Co
  • nano-scale component can have a composition ranging from WC/5Co to WC/15Co.
  • the average Co content can be as low as 4.1%. This gives the added benefit that the volume fraction of the hard phase is greater than usual, which is likely to lead to higher wear resistance.
  • a composition having a micron: nano ratio of 70:30 was selected because it exceeds the percolation threshold of the minor phase, i.e. the nano-grained material maintains its continuity.
  • modifications to the ratio over a wider range can also lead to enhancement in the wear properties.
  • Powders of WC/12 Co were obtained from a commercial source, which have a typical agglomerate size of 15-40 microns. Each agglomerate was composed of WC/Co particles with a carbide grain size of 2-5 microns. (WC/8C0 can be used as well.) Nano-scale particles of binder phase material (Nanocarb®) with a composition of WC/5Co was milled in a conventional ball mill into particles in the range 0.1-5 microns. Each particle is composed of several nanocrystals of WC, ⁇ 50 nm in diameter. The two powders were homogeneously mixed in the ratio 70:30, the larger weight fraction being that of the micron-grain material (WC/12Co). The average Co content in the material was 9.9%. Subsequently, the mixed powders were heat treated at a temperature of 850 °C for 1 hour in an atmosphere of H 2 and CH .
  • FIGS. 7 A and 7B are low and high magnification SEM images of the mixed and heat treated powders. These images clearly illustrate the coarse and fine particles. Heat treatment allows the nano-scale particles of binder phase material to sinter to the surface of the larger agglomerates of hard phase material. It should be noted that any combination of micron (WC/0 Co - WC/12 Co) and nano grain (WC/5 Co - WC/15 Co) compositions can be used to form HVOF thermal sprayed coatings.
  • a non-heat treated powder sample (sample #1) and a heat treated powder sample (sample #2) were sprayed using standard DJ HVOF thermal spray gun. Coatings with thickness in the range 500 - 600 microns (-0.2 inches) were sprayed for both samples.
  • the average hardness of Sample #1 was 750 VHN and that of Sample #2 was 800 VHN.
  • the slight increase in hardness for the sintered powders is probably due to the increased density of the coating, as corroborated by the optical micrographs of the surface of the coatings, shown in FIGS. 8 A and 8B.
  • the optical micrograph of FIG. 8 A is the non-heat treated sample #1 and the optical micrograph of FIG. 8B is the heat treated sample #2. Both samples were greater than 90% dense (i.e. 90% of the theoretical value).
  • Sample #1 had an abrasive wear resistance of 1.6 x 10 2 Nm/mm 3 and Sample #2 had an abrasive wear resistance of 2.5 x 10 2 Nm/mm 3 . These numbers represent a 75% improvement over state-of-the-art thermal sprayed coatings of conventional WC/12Co materials.
  • Table II shown below is a summary of characterization and wear data of the samples described in Examples 1 and 2. For pu ⁇ oses of comparison, three other WC/Co materials are also described.
  • Multimodal feedstock powders of ceramic/ceramic composites were obtained.
  • the blended powder was spray dried and agglomerated into dense structures and plasma sprayed.
  • the performance of the coating in terms of ductility and toughness was enhanced compared to a conventional coatings, resulting in enhanced wear resistance.
  • Multimodal feedstock powders of alumina ceramics were produced by
  • blended powder was spray dried and agglomerated into a dense structure and plasma sprayed.
  • the performance of the coating in terms of ductility and toughness was enhanced compared to conventional coatings.
  • coatings for wear applications having additional properties and performance advantages can be gained by blending predetermined volume fractions of micro-scale and nano-scale powders in the feedstock powder used for thermal spraying.
  • the use of such feedstock powders makes it possible to produce coatings with superior properties and performance for specific applications. For example, higher hardness and wear resistance for protective coatings in combustion and gas turbine engines, high optical transparency and toughness for aircraft canopies and radome structures, and enhanced ballistic impact strength for armor plates.

Abstract

Cette invention concerne un procédé de métallisation à chaud pour la fabrication de revêtements durs en céramique/métal et céramique/céramique pour applications soumises à usure. Le procédé consiste à utiliser une charge en poudre, composée d'agrégats de particules de matériau en phase dure de la taille du micron qui soit sont mélangés à un nanomatériau (12) à phase liante facilement fusible, soit en sont enduits. Ainsi, pendant l'opération (14) de métallisation à chaud, le matériau à nanostructure subit une fusion rapide, cependant que le matériau composé d'agrégats est chauffé, mais sans forcément fondre. Une couche dense se forme lorsque le nanomatériau fondu remplit les espaces poreux entre les agrégats chauffés et attendris, ce qui donne une matrice robuste et tenace. On obtient des caractéristiques d'usure optimale lorsque la proportion en volume de particules agrégées est élevée, de l'ordre généralement de 0,5-0,9. Le matériau agrégé peut être composé d'une, de deux ou de plusieurs particules de taille et/ou de composition différentes, avec une répartition par taille des particules qui donne une forte densité de tassement pour la phase dure.
PCT/US2000/022340 1999-08-16 2000-08-16 Revetements durs structures multimode realises a partir de materiaux micro-nanocomposites WO2001012431A1 (fr)

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US10/049,577 US6723387B1 (en) 1999-08-16 2000-08-16 Multimodal structured hardcoatings made from micro-nanocomposite materials
AU70590/00A AU7059000A (en) 1999-08-16 2000-08-16 Multimodal structured hardcoatings made from micro-nanocomposite materials

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US14912899P 1999-08-16 1999-08-16
US60/149,128 1999-08-16

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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1227213A3 (fr) * 2001-01-04 2002-08-07 Camco International (UK) Limited Trépan de forage résistant à l'usure
GB2393452A (en) * 2002-08-28 2004-03-31 C A Technology Ltd Superfine powder and spraying
US7799111B2 (en) * 2005-03-28 2010-09-21 Sulzer Metco Venture Llc Thermal spray feedstock composition
US7914856B2 (en) 2007-06-29 2011-03-29 General Electric Company Method of preparing wetting-resistant surfaces and articles incorporating the same
WO2011035965A1 (fr) * 2009-09-23 2011-03-31 Voith Patent Gmbh Poudre à pulvériser pour appliquer un revêtement de cermet à des lames de racles
RU2506346C2 (ru) * 2011-11-29 2014-02-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Воронежский государственный технический университет" Наноструктурное покрытие из гранулированного композита
RU2506347C2 (ru) * 2011-11-29 2014-02-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Воронежский государственный технический университет" Способ повышения износостойкости наноструктурного покрытия из гранулированного композита

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103484811B (zh) * 2013-10-09 2015-09-02 河北工业大学 金属氧化物基无机复合材料涂层的制备方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5120693A (en) * 1991-03-25 1992-06-09 Uop Bonded adsorbent agglomerates
WO1997018341A1 (fr) * 1995-11-13 1997-05-22 The University Of Connecticut Produits nanostructures pour pulverisation a chaud
US5880382A (en) * 1996-08-01 1999-03-09 Smith International, Inc. Double cemented carbide composites

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5120693A (en) * 1991-03-25 1992-06-09 Uop Bonded adsorbent agglomerates
WO1997018341A1 (fr) * 1995-11-13 1997-05-22 The University Of Connecticut Produits nanostructures pour pulverisation a chaud
US5880382A (en) * 1996-08-01 1999-03-09 Smith International, Inc. Double cemented carbide composites

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1227213A3 (fr) * 2001-01-04 2002-08-07 Camco International (UK) Limited Trépan de forage résistant à l'usure
GB2393452A (en) * 2002-08-28 2004-03-31 C A Technology Ltd Superfine powder and spraying
GB2393452B (en) * 2002-08-28 2005-12-28 C A Technology Ltd Improvements to powder production and spraying
US7799111B2 (en) * 2005-03-28 2010-09-21 Sulzer Metco Venture Llc Thermal spray feedstock composition
US7914856B2 (en) 2007-06-29 2011-03-29 General Electric Company Method of preparing wetting-resistant surfaces and articles incorporating the same
WO2011035965A1 (fr) * 2009-09-23 2011-03-31 Voith Patent Gmbh Poudre à pulvériser pour appliquer un revêtement de cermet à des lames de racles
RU2506346C2 (ru) * 2011-11-29 2014-02-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Воронежский государственный технический университет" Наноструктурное покрытие из гранулированного композита
RU2506347C2 (ru) * 2011-11-29 2014-02-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Воронежский государственный технический университет" Способ повышения износостойкости наноструктурного покрытия из гранулированного композита

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