A composite conductive material includes at least graphene-like exfoliated from a graphite-based graphite carbon material and a conductive material dispersed in a base material. The graphite-based carbon material has a rhombohedral graphite layer (3R) and a hexagonal graphite layer (2H), wherein a Rate (3R) of the rhombohedral graphite layer (3R) and the hexagonal graphite layer (2H), based on an X-ray diffraction method, which is defined by following Equation 1 is 31% or more:

Rate (3R)=P3/(P3+P4)100(Equation 1)

wherein P3 is a peak intensity of a (101) plane of the rhombohedral graphite layer (3R) based on the X-ray diffraction method, and P4 is a peak intensity of a (101) plane of the hexagonal graphite layer (2H) based on the X-ray diffraction method.

A method for producing a metal detectible ceramic, including mixing a first amount of ceramic material with a second metal oxide to define an admixture, forming the admixture into a green body, sintering the green body to yield a densified body, wherein the densified body has a plurality of metallic particles distributed therethrough, and wherein the densified body is detectible by a metal detector.

A composition having nanoparticles of a refractory-metal carbide or refractory-metal nitride and a carbonaceous matrix. The composition is not in the form of a powder. A composition comprising a metal component and an organic component. The metal component is nanoparticles or particles of a refractory metal or a refractory-metal compound capable of decomposing into refractory metal nanoparticles. The organic component is an organic compound having a char yield of at least 60% by weight or a thermoset made from the organic compound. A method of combining particles of a refractory metal or a refractory-metal compound capable of reacting or decomposing into refractory-metal nanoparticles with an organic compound having a char yield of at least 60% by weight to form a precursor mixture.

A composition having nanoparticles of a refractory-metal carbide or refractory-metal nitride and a carbonaceous matrix. The composition is not in the form of a powder. A composition comprising a metal component and an organic component. The metal component is nanoparticles or particles of a refractory metal or a refractory-metal compound capable of decomposing into refractory metal nanoparticles. The organic component is an organic compound having a char yield of at least 60% by weight or a thermoset made from the organic compound. A method of combining particles of a refractory metal or a refractory-metal compound capable of reacting or decomposing into refractory-metal nanoparticles with an organic compound having a char yield of at least 60% by weight to form a precursor mixture.

A method including applying layers of multiple constituents where the constituents are capable of producing a non-equilibrium condition on the contacting surfaces of a ceramic matrix composite component and a gas turbine engine component where one outer coating includes a first constituent and the other outer coating includes a second constituent; forming a component assembly with the ceramic matrix composite component coupled to the gas turbine engine component with contact between the outer coatings; adding an energy to facilitate an equilibrium reaction between the first constituent of the first outer coating and the second constituent of the second outer coating; and as a result of adding the energy, forming a bond structure in the component assembly with a product of the equilibrium reaction where the bond structure affixes the ceramic matrix composite component to the gas turbine engine component between the first constituent and the second constituent.

The invention relates to a process for the continuous thermal removal of binder from a metallic and/or ceramic shaped body which has been produced by injection molding, extrusion or pressing using a thermoplastic composition and comprises at least one polyoxymethylene homopolymer or copolymer as binder in a binder removal oven, which comprises the steps (a) removal of binder from the shaped body in a binder removal oven at a temperature which is from 5 to 20 C. below, preferably from 10 to 15 C. below, the temperature of a second temperature stage over a period of from 4 to 12 hours in a first temperature stage in an oxygen-comprising atmosphere, (b) removal of binder from the shaped body at a temperature in the range >160 to 200 C. over a period of from 4 to 12 hours in an oxygen-comprising atmosphere in a second temperature stage and (c) removal of binder from the shaped body at a temperature in the range from 200 to 600 C. over a period of from 2 to 8 hours in a third temperature stage in an oxygen-comprising or neutral or reducing atmosphere, with the shaped bodies being transported through the binder removal oven during process steps (a) and (b).

A method of making a sintered ceramic body comprising the steps of disposing a ceramic powder (5) inside an inner volume of a spark plasma sintering tool (1), wherein the tool comprises: a die (2) comprising a sidewall comprising inner and outer walls, wherein the inner wall has a diameter defining the inner volume; upper and lower punches (4,4) operably coupled with the die, wherein each of the punches have an outer wall defining a diameter less than the diameter of the die inner wall, thereby creating a gap (3) between the punches and the inner wall when at least one of the punches are moved within the inner volume, and the gap is from 10 m to 70 m wide; creating vacuum conditions inside the inner volume; moving at least one of the punches to apply pressure to the ceramic powder while heating, and sintering; and lowering the temperature of the sintered body.

The invention presents a near-infrared photothermal coupling curing non-oxide ceramic slurry, along with its preparation method and application. The ceramic slurry consists of various raw materials, with weight fractions as follows: non-oxide ceramic powder (4090 parts), photosensitive resin (0.520 parts), photosensitive monomer (140 parts), photoinitiator (0.254 parts), thermal initiator (0.254 parts), additive (0.755 parts), and up-conversion luminescent material (0.54 parts). The non-oxide ceramic powders can include Si.sub.3N.sub.4, TiN, BN, AlN, SiC, WC, TiC, ZrC, TiB.sub.2, and ZrB.sub.2. By combining the photochemical and photothermal dual curing system using near-infrared up-conversion, this invention addresses the issue of insufficient curing encountered in single photocuring or thermal curing processes. Moreover, by incorporating near-infrared light source-driven additive manufacturing, it enables rapid prototyping of high-solid-content non-oxide ceramic slurry, ultimately allowing for the fabrication of high-fidelity non-oxide ceramic structures.

According to some embodiments, a system includes a three-dimensional (3D) printer, a hydraulic press, and a kiln. The three-dimensional printer includes a print bed, a first printhead, and a second printhead. The first printhead is configured to deposit a layer of a first powder on the print bed. The second printhead is configured to deposit a layer of a second powder on the print bed. The hydraulic press is configured to compress a greenware to form a compressed greenware. The kiln is configured to heat the compressed greenware to a reaction temperature to form an object. The object is surrounded by an excess of the first powder. The kiln is also configured to heat the object surrounded by the excess of the first powder to a melting temperature. The melting temperature is at least the melting point of the first powder and less than the melting point of the object.

A cubic boron nitride sintered body including cubic boron nitride and a binder phase, wherein a content of the cubic boron nitride is 40 volume % or more and 80 volume % or less; a content of the binder phase is 20 volume % or more and 60 volume % or less; an average particle size of the cubic boron nitride is 0.5 m or more and 4.0 m or less; the binder phase contains TiC and TiB.sub.2 and contains substantially no AlN and/or Al.sub.2O.sub.3; a (101) plane of TiB.sub.2 in the binder phase shows a maximum peak position (2) in X-ray diffraction of 44.2 or more; and a (200) plane of TiC in the binder phase shows a maximum peak position (2) in X-ray diffraction of less than 42.1.