The present disclosure relates to the field of ceramics, and discloses a metal-based aluminum nitride composite material. The composite material includes an aluminum nitride ceramic skeleton and a metal filling at least part of pores of the aluminum nitride ceramic skeleton. The aluminum nitride ceramic skeleton contains aluminum nitride and CuAlO.sub.2, and the aluminum nitride ceramic skeleton has a porosity of 20 to 40 percent. The present disclosure further discloses a method for preparing the metal-based aluminum nitride composite material and the metal-based aluminum nitride composite material obtained by the method. A CuAlO.sub.2 substance is formed in the aluminum nitride ceramic skeleton obtained in the present disclosure.

A cubic boron nitride sintered material comprises cubic boron nitride particles and a bonding material, wherein the bonding material comprises at least one first metallic element selected from the group consisting of titanium, zirconium, vanadium, niobium, hafnium, tantalum, chromium, rhenium, molybdenum, and tungsten; cobalt; and aluminum; the cubic boron nitride sintered material has a first interface region sandwiched between an interface between the cubic boron nitride particles and the bonding material, and a first virtual line passing through a point 10 nm apart from the interface to the bonding material side; and when an element that is present at the highest concentration among the first metallic elements in the first interface region is defined as a first element, an atomic concentration of the first element in the first interface region is higher than an atomic concentration of the first element in the bonding material excluding the first interface region.

A cubic boron nitride sintered material comprises cubic boron nitride particles and a bonding material, wherein the bonding material comprises at least one first metallic element selected from the group consisting of titanium, zirconium, vanadium, niobium, hafnium, tantalum, chromium, rhenium, molybdenum, and tungsten; cobalt; and aluminum; the cubic boron nitride sintered material has a first interface region sandwiched between an interface between the cubic boron nitride particles and the bonding material, and a first virtual line passing through a point 10 nm apart from the interface to the bonding material side; and when an element that is present at the highest concentration among the first metallic elements in the first interface region is defined as a first element, an atomic concentration of the first element in the first interface region is higher than an atomic concentration of the first element in the bonding material excluding the first interface region.

An insert includes a cBN sintered compact including cBN particles and a binder phase binding the cBN particles. The cBN particles occupy 60% or more of the cross-sectional area of the cBN sintered compact. The binder phase contains Al compound particles containing at least one of AlN or Al.sub.2O.sub.3. A particle distribution of the Al compound particles in a cumulative distribution based on the number of the Al compound particles in a cross section of the cBN sintered compact is as follows. The proportion of the Al compound particles with the particle diameter of 0.3 ?m or larger is 5% or more, and the proportion of the Al compound particles with the particle diameter of 0.5 ?m or larger is less than 5%.

An insert includes a cBN sintered compact including cBN particles and a binder phase binding the cBN particles. The cBN particles occupy 60% or more of the cross-sectional area of the cBN sintered compact. The binder phase contains Al compound particles containing at least one of AlN or Al.sub.2O.sub.3. A particle distribution of the Al compound particles in a cumulative distribution based on the number of the Al compound particles in a cross section of the cBN sintered compact is as follows. The proportion of the Al compound particles with the particle diameter of 0.3 ?m or larger is 5% or more, and the proportion of the Al compound particles with the particle diameter of 0.5 ?m or larger is less than 5%.

A method for fabricating tungsten carbide cermet components or parts employs powder bed fusion of powder mixture of ceramic particles and metal binder. Some embodiments also include a step of hot isostatic pressing to increase the density of the part.

A coated bearing component comprising a metallic part and a coating deposited on the metallic part. The coating is a multi-layer coating having a sensor active layer made of a material having electrostrictive properties. The sensor active layer is directly coated on the metallic part. The bearing component can be integrated into a bearing.

The present invention relates to tungsten-rhenium coated compounds, materials formed from tungsten-rhenium coated compounds, and to methods of forming the same. In embodiments, tungsten and rhenium are coated on ultra hard material particles to form coated ultra hard material particles, and the coated ultra hard material particles are sintered at high temperature and high pressure.

The present invention relates to tungsten-rhenium coated compounds, materials formed from tungsten-rhenium coated compounds, and to methods of forming the same. In embodiments, tungsten and rhenium are coated on ultra hard material particles to form coated ultra hard material particles, and the coated ultra hard material particles are sintered at high temperature and high pressure.

A sintered polycrystalline body and a method of forming the sintered polycrystalline body are disclosed. The sintered polycrystalline body comprises a plurality of particles cubic boron nitride dispersed in a matrix. The matrix includes materials selected from compounds of any of titanium and aluminium. The polycrystalline body further comprises 0.1 to 5.0 volume % of lubricating chalcogenide particles dispersed in the matrix. The chalcogenide particles have a coefficient of friction of less than 0.1 with respect to a workpiece material. Preferably sulfide particles are used as lubricant. Preferably 30-70 vol.-% cBN is contained. Sintering takes place at 1100-1600 C. and 4-8 GPa.