Disclosed is a method of manufacturing an epitaxy oxide thin film of enhanced crystalline quality, and an epitaxy oxide thin film manufactured thereby according to the present invention. With respect to the manufacturing method of the epitaxy oxide thin film, which epitaxially grows an orientation film with an oxide capable of being oriented to (001), (110), and (111) on a single crystal Si substrate, because time required for raising a temperature of the orientation film up to an annealing temperature at room temperature is extremely minimized, thermal stress arising from the large difference in thermal expansion coefficients between the substrate and the orientation film is controlled, so crystalline quality of the epitaxy oxide thin film can be enhanced. Moreover, various epitaxial functional oxides are integrated into the thin film of enhanced crystalline quality so that a novel electronic device can be embodied.

A method of manufacturing a copper thin film using a single-crystal copper target, and more particularly, a method of manufacturing a copper thin film using a single-crystal copper target, wherein a copper thin film is deposited on a sapphire disk substrate through high-frequency sputtering using a single-crystal copper target grown through a Czochralski process, and may thus exhibit high quality in terms of crystallinity. The method includes depositing a copper thin film on a sapphire disk substrate through a high-frequency sputtering process using a disk-shaped single-crystal copper target obtained by cutting cylindrical single-crystal copper grown through a Czochralski process.

An object of the present invention is to provide a novel technique capable of suppressing the occurrence of cracks in the growth layer.

The present invention is a method for manufacturing a semiconductor substrate, which includes: an embrittlement processing step S10 of reducing strength of an underlying substrate 10; and a crystal growth step S20 of forming the growth layer 20 on the underlying substrate 10. In addition, the present invention is a method for suppressing the occurrence of cracks in the growth layer 20, and this method includes an embrittlement processing step S10 of reducing the strength of the underlying substrate 10 before forming the growth layer 20 on the underlying substrate 10.

Disclosed are a silicon carbide powder and a method of manufacturing a silicon carbide ingot using the same. More particularly, the silicon carbide powder includes carbon and silicon and has a particle circularity of 0.4 to 0.9 measured through 2D image analysis.

Disclosed are a silicon carbide powder and a method of manufacturing a silicon carbide ingot using the same. More particularly, the silicon carbide powder includes carbon and silicon and has a particle circularity of 0.4 to 0.9 measured through 2D image analysis.

Disclosed are a silicon carbide powder, a method of manufacturing a silicon carbide powder, and a silicon carbide wafer. More particularly, the silicon carbide powder includes carbon and silicon and in the silicon carbide powder, O1s/C1s of a surface measured by X-ray photoelectron spectroscopy is 0.28 or less.

Methods and systems of heating a substrate in a vacuum deposition process include a resistive heater having a resistive heating element. Radiative heat emitted from the resistive heating element has a wavelength in a mid-infrared band from 5 μm to 40 μm that corresponds to a phonon absorption band of the substrate. The substrate comprises a wide bandgap semiconducting material and has an uncoated surface and a deposition surface opposite the uncoated surface. The resistive heater and the substrate are positioned in a vacuum deposition chamber. The uncoated surface of the substrate is spaced apart from and faces the resistive heater. The uncoated surface of the substrate is directly heated by absorbing the radiative heat.

Disclosed is a magnetic annealing apparatus including a processing container that performs a magnetic annealing processing on a plurality of substrates accommodated therein in a magnetic field; a substrate holder that holds the plurality of substrates substantially horizontally in the processing container; a division heater including a plurality of sub-division heaters and covering a substantially entire circumferential surface of an outer periphery of a predetermined region of the processing container along a longitudinal direction; a magnet installed to cover an outside of the division heater; and a controller configured to feedback-control a temperature of a predetermined control target heater among the plurality of sub-division heaters, and to control temperatures of the plurality of sub-division heaters other than the predetermined control target heater based on a control output obtained by multiplying a control output of the predetermined control target heater and a predetermined ratio.

The present disclosure provides a film forming method and an aluminum nitride film forming method for a semiconductor device. The film forming method for a semiconductor device includes performing multiple sputtering routes sequentially. Each sputtering routes includes: loading a substrate into a chamber; moving a shielding plate between a target and the substrate; introducing an inert gas into the chamber to perform a surface modification process on the target; performing a pre-sputtering to pre-treat a surface of the target; moving the shielding plate away from the substrate, and performing a main sputtering on the substrate to form a film on the substrate; and moving the substrate out of the chamber.

The present invention relates to a silicon carbide (SiC) substrate with improved mechanical and electrical characteristics. Furthermore, the invention relates to a method for producing a bulk SiC crystal in a physical vapor transport growth system. The silicon carbide substrate comprises an inner region (102) which constitutes at least 30% of a total surface area of said substrate (100), a ring shaped peripheral region (104) radially surrounding the inner region (102), wherein a mean concentration of a dopant in the inner region (102) differs by at least 1.Math.10.sup.18 cm.sup.−3 from the mean concentration of this dopant in the peripheral region (104).