20 research outputs found
Π€ΠΠ ΠΠΠ ΠΠΠΠΠΠ Π ΠΠΠ’ΠΠ§ΠΠ‘ΠΠΠ Π‘ΠΠΠΠ‘Π’ΠΠ ΠΠ‘ΠΠΠΠΠΠΠΠΠ ΠΠΠΠΠ’Π ΠΠ₯ΠΠΠΠ§ΠΠ‘ΠΠΠ ΠΠΠ’ΠΠΠΠ ΠΠΠΠΠ ΠΠΠΠΠΠΠΠ ΠΠΠΠΠΠΠ ΠΠΠ‘ΠΠΠ Π¦ΠΠΠΠ
This paper is targeted at studying the patterns of deposition by electrochemical method of Ni-doped ZnO films, including registering and analyzing their photoluminescence and Raman scattering spectra. We have studied the electrochemical deposition of nickel-doped zinc oxide films on single-crystal silicon substrates from aqueous solutions of zinc and nickel nitrates. The deposition was conducted from aqua solutions of Zn and Ni nitrates in a standard double-electrode electrochemical cell in galvanostatic mode with the current density from 5 to 20 mA/cm2 and deposition time from 5 to 30 min. The Raman scattering on nickel-doped zinc oxide films was examined via laser Raman spectrometer SOL Instruments Confotec NR500. The analysis of Raman spectra showed that an increase of cathodic current density deposition leads to an enhanced concentration of a doping agent in the films. Photoluminescence spectra of the samples were registered on a laser spectral measuring system based on monochromator-spectrograph SOLAR TII MS 7504i where a monochromatic line with the 345-nm wavelength, which was extracted from the spectrum of Xe-lamp by means of double monochromator Solar TII DM160, was used as the excitation source. The research demonstrates that the emmission intensity increases with the thickness of the deposited film, and the position of maximums of the radiation line remains unchanged in a visible wavelength range and on photoluminescence spectra with fixed current density. The change in the density of the cathode current leads to a shift in the position of the photoluminescence spectra maximum, which indicates restructuring of defects and dopant atoms in the doped semiconductor, which in turn changes the position of the corresponding levels in the band gap of the material.Π¦Π΅Π»Ρ ΡΠ°Π±ΠΎΡΡ Π·Π°ΠΊΠ»ΡΡΠ°Π»Π°ΡΡ Π² ΠΈΡΡΠ»Π΅Π΄ΠΎΠ²Π°Π½ΠΈΠΈ Π·Π°ΠΊΠΎΠ½ΠΎΠΌΠ΅ΡΠ½ΠΎΡΡΠ΅ΠΉ ΡΠΎΡΠΌΠΈΡΠΎΠ²Π°Π½ΠΈΡ ΡΠ»Π΅ΠΊΡΡΠΎΡ
ΠΈΠΌΠΈΡΠ΅ΡΠΊΠΈΠΌ ΠΌΠ΅ΡΠΎΠ΄ΠΎΠΌ ΠΏΠ»Π΅Π½ΠΎΠΊ ΠΎΠΊΡΠΈΠ΄Π° ΡΠΈΠ½ΠΊΠ°, Π»Π΅Π³ΠΈΡΠΎΠ²Π°Π½Π½ΡΡ
Π½ΠΈΠΊΠ΅Π»Π΅ΠΌ, Π° ΡΠ°ΠΊΠΆΠ΅ ΡΠ΅Π³ΠΈΡΡΡΠ°ΡΠΈΠΈ ΠΈ ΠΈΡΡΠ»Π΅Π΄ΠΎΠ²Π°Π½ΠΈΠΈ ΡΠΏΠ΅ΠΊΡΡΠΎΠ² ΡΠΎΡΠΎΠ»ΡΠΌΠΈΠ½ΠΈΡΡΠ΅Π½ΡΠΈΠΈ ΠΈ ΡΠ°ΠΌΠ°Π½ΠΎΠ²ΡΠΊΠΎΠ³ΠΎ ΡΠ°ΡΡΠ΅ΡΠ½ΠΈΡ. ΠΡΠ°ΠΆΠ΄Π΅Π½ΠΈΠ΅ ΠΏΠ»Π΅Π½ΠΎΠΊ ΠΎΠΊΡΠΈΠ΄Π° ΡΠΈΠ½ΠΊΠ°, Π»Π΅Π³ΠΈΡΠΎΠ²Π°Π½Π½ΡΡ
Π½ΠΈΠΊΠ΅Π»Π΅ΠΌ, ΠΏΡΠΎΠ²ΠΎΠ΄ΠΈΠ»ΠΎΡΡ ΠΌΠ΅ΡΠΎΠ΄ΠΎΠΌ ΡΠ»Π΅ΠΊΡΡΠΎΡ
ΠΈΠΌΠΈΡΠ΅ΡΠΊΠΎΠ³ΠΎ ΠΎΡΠ°ΠΆΠ΄Π΅Π½ΠΈΡ Π½Π° ΠΏΠΎΠ΄Π»ΠΎΠΆΠΊΠΈ ΠΊΡΠ΅ΠΌΠ½ΠΈΡ ΠΌΠ°ΡΠΊΠΈ ΠΠΠΠ‘-0,01 (111). ΠΡΠ°ΠΆΠ΄Π΅Π½ΠΈΠ΅ ΠΏΡΠΎΠ²ΠΎΠ΄ΠΈΠ»ΠΎΡΡ ΠΈΠ· Π²ΠΎΠ΄Π½ΡΡ
ΡΠ°ΡΡΠ²ΠΎΡΠΎΠ² Π½ΠΈΡΡΠ°ΡΠΎΠ² ΡΠΈΠ½ΠΊΠ° ΠΈ Π½ΠΈΠΊΠ΅Π»Ρ Π² Π³Π°Π»ΡΠ²Π°Π½ΠΎΡΡΠ°ΡΠΈΡΠ΅ΡΠΊΠΎΠΌ ΡΠ΅ΠΆΠΈΠΌΠ΅ Π² Π΄ΠΈΠ°ΠΏΠ°Π·ΠΎΠ½Π΅ ΠΏΠ»ΠΎΡΠ½ΠΎΡΡΠ΅ΠΉ ΡΠΎΠΊΠ° ΠΎΡ 5 Π΄ΠΎ 20 ΠΌΠ/ΡΠΌ2 ΠΈ Π²ΡΠ΅ΠΌΠ΅Π½ΠΈ ΠΎΡΠ°ΠΆΠ΄Π΅Π½ΠΈΡ ΠΎΡ 5 Π΄ΠΎ 30 ΠΌΠΈΠ½. ΠΠ° Π»Π°Π·Π΅ΡΠ½ΠΎΠΌ Π Π°ΠΌΠ°Π½ΠΎΠ²ΡΠΊΠΎΠΌ ΡΠΏΠ΅ΠΊΡΡΠΎΠΌΠ΅ΡΡΠ΅ SOL Instruments Confotec NR500 ΠΏΡΠΎΠ²Π΅Π΄Π΅Π½ΠΎ ΠΈΡΡΠ»Π΅Π΄ΠΎΠ²Π°Π½ΠΈΠ΅ ΡΠ°ΠΌΠ°Π½ΠΎΠ²ΡΠΊΠΎΠ³ΠΎ ΡΠ°ΡΡΠ΅ΡΠ½ΠΈΡ Π½Π° ΠΏΠ»Π΅Π½ΠΊΠ°Ρ
Π»Π΅Π³ΠΈΡΠΎΠ²Π°Π½Π½ΠΎΠ³ΠΎ Π½ΠΈΠΊΠ΅Π»Π΅ΠΌ ΠΎΠΊΡΠΈΠ΄Π° ΡΠΈΠ½ΠΊΠ°. ΠΠ½Π°Π»ΠΈΠ· ΡΠ°ΠΌΠ°Π½ΠΎΠ²ΡΠΊΠΈΡ
ΡΠΏΠ΅ΠΊΡΡΠΎΠ² ΠΏΠΎΠΊΠ°Π·Π°Π», ΡΡΠΎ ΡΠ²Π΅Π»ΠΈΡΠ΅Π½ΠΈΠ΅ ΠΊΠ°ΡΠΎΠ΄Π½ΠΎΠΉ ΠΏΠ»ΠΎΡΠ½ΠΎΡΡΠΈ ΡΠΎΠΊΠ° ΠΎΡΠ°ΠΆΠ΄Π΅Π½ΠΈΡ ΠΏΡΠΈΠ²ΠΎΠ΄ΠΈΡ ΠΊ Π²ΠΎΠ·ΡΠ°ΡΡΠ°Π½ΠΈΡ ΠΊΠΎΠ½ΡΠ΅Π½ΡΡΠ°ΡΠΈΠΈ ΠΏΡΠΈΠΌΠ΅ΡΠΈ Π² ΠΏΠ»Π΅Π½ΠΊΠ°Ρ
. Π Π΅Π³ΠΈΡΡΡΠ°ΡΠΈΡ ΡΠΏΠ΅ΠΊΡΡΠΎΠ² ΡΠΎΡΠΎΠ»ΡΠΌΠΈΠ½Π΅ΡΡΠ΅Π½ΡΠΈΠΈ ΠΎΠ±ΡΠ°Π·ΡΠΎΠ² ΠΏΡΠΎΠ²ΠΎΠ΄ΠΈΠ»Π°ΡΡ Π½Π° Π»Π°Π·Π΅ΡΠ½ΠΎΠΌ ΡΠΏΠ΅ΠΊΡΡΠ°Π»ΡΠ½ΠΎΠΌ ΠΈΠ·ΠΌΠ΅ΡΠΈΡΠ΅Π»ΡΠ½ΠΎΠΌ ΠΊΠΎΠΌΠΏΠ»Π΅ΠΊΡΠ΅ Π½Π° ΠΎΡΠ½ΠΎΠ²Π΅ ΠΌΠΎΠ½ΠΎΡ
ΡΠΎΠΌΠ°ΡΠΎΡΠ°-ΡΠΏΠ΅ΠΊΡΡΠΎΠ³ΡΠ°ΡΠ° SOLAR TII MS 7504i, Π³Π΄Π΅ Π² ΠΊΠ°ΡΠ΅ΡΡΠ²Π΅ ΠΈΡΡΠΎΡΠ½ΠΈΠΊΠ° Π²ΠΎΠ·Π±ΡΠΆΠ΄Π°ΡΡΠ΅Π³ΠΎ ΠΈΠ·Π»ΡΡΠ΅Π½ΠΈΡ ΠΈΡΠΏΠΎΠ»ΡΠ·ΠΎΠ²Π°Π»Π°ΡΡ ΠΌΠΎΠ½ΠΎΡ
ΡΠΎΠΌΠ°ΡΠΈΡΠ΅ΡΠΊΠ°Ρ Π»ΠΈΠ½ΠΈΡ Ρ Π΄Π»ΠΈΠ½ΠΎΠΉ Π²ΠΎΠ»Π½Ρ 345 Π½ΠΌ, Π²ΡΠ΄Π΅Π»Π΅Π½Π½Π°Ρ ΠΈΠ· ΡΠΏΠ΅ΠΊΡΡΠ° ΠΊΡΠ΅Π½ΠΎΠ½ΠΎΠ²ΠΎΠΉ Π»Π°ΠΌΠΏΡ ΠΏΡΠΈ ΠΏΠΎΠΌΠΎΡΠΈ Π΄Π²ΠΎΠΉΠ½ΠΎΠ³ΠΎ ΠΌΠΎΠ½ΠΎΡ
ΡΠΎΠΌΠ°ΡΠΎΡΠ° Solar TII DM160. ΠΡΡΠ»Π΅Π΄ΠΎΠ²Π°Π½ΠΈΠ΅ ΠΏΠΎΠΊΠ°Π·Π°Π»ΠΎ, ΡΡΠΎ ΠΈΠ½ΡΠ΅Π½ΡΠΈΠ²Π½ΠΎΡΡΡ ΠΈΠ·Π»ΡΡΠ΅Π½ΠΈΡ ΡΠ°ΡΡΠ΅Ρ Ρ ΡΠ²Π΅Π»ΠΈΡΠ΅Π½ΠΈΠ΅ΠΌ ΡΠΎΠ»ΡΠΈΠ½Ρ ΠΎΡΠ°ΠΆΠ΄Π΅Π½Π½ΠΎΠΉ ΠΏΠ»Π΅Π½ΠΊΠΈ, Π° ΠΏΠΎΠ»ΠΎΠΆΠ΅Π½ΠΈΠ΅ ΠΌΠ°ΠΊΡΠΈΠΌΡΠΌΠΎΠ² ΠΏΠΎΠ»ΠΎΡΡ ΠΈΠ·Π»ΡΡΠ΅Π½ΠΈΡ, Π² Π²ΠΈΠ΄ΠΈΠΌΠΎΠΌ Π΄ΠΈΠ°ΠΏΠ°Π·ΠΎΠ½Π΅ Π΄Π»ΠΈΠ½ Π²ΠΎΠ»Π½, Π½Π° ΡΠΏΠ΅ΠΊΡΡΠ°Ρ
ΡΠΎΡΠΎΠ»ΡΠΌΠΈΠ½Π΅ΡΡΠ΅Π½ΡΠΈΠΈ, ΠΎΡΡΠ°Π΅ΡΡΡ Π½Π΅ΠΈΠ·ΠΌΠ΅Π½Π½ΡΠΌ ΠΏΡΠΈ Π·Π°Π΄Π°Π½Π½ΠΎΠΉ ΠΏΠ»ΠΎΡΠ½ΠΎΡΡΠΈ ΡΠΎΠΊΠ°, Π½Π΅Π·Π°Π²ΠΈΡΠΈΠΌΠΎ ΠΎΡ ΠΏΡΠΎΠ΄ΠΎΠ»ΠΆΠΈΡΠ΅Π»ΡΠ½ΠΎΡΡΠΈ ΠΏΡΠΎΡΠ΅ΡΡΠ° ΠΎΡΠ°ΠΆΠ΄Π΅Π½ΠΈΡ. ΠΠ·ΠΌΠ΅Π½Π΅Π½ΠΈΠ΅ Π²Π΅Π»ΠΈΡΠΈΠ½Ρ ΠΏΠ»ΠΎΡΠ½ΠΎΡΡΠΈ ΠΊΠ°ΡΠΎΠ΄Π½ΠΎΠ³ΠΎ ΡΠΎΠΊΠ° ΠΏΡΠΈΠ²ΠΎΠ΄ΠΈΡ ΠΊ ΡΠ΄Π²ΠΈΠ³Ρ ΠΏΠΎΠ»ΠΎΠΆΠ΅Π½ΠΈΡ ΠΌΠ°ΠΊΡΠΈΠΌΡΠΌΠ° ΡΠΏΠ΅ΠΊΡΡΠ° ΡΠΎΡΠΎΠ»ΡΠΌΠΈΠ½Π΅ΡΡΠ΅Π½ΡΠΈΠΈ, ΡΡΠΎ ΡΠΊΠ°Π·ΡΠ²Π°Π΅Ρ Π½Π° ΠΏΠ΅ΡΠ΅ΡΡΡΠΎΠΉΠΊΡ ΡΡΡΡΠΊΡΡΡΡ Π΄Π΅ΡΠ΅ΠΊΡΠΎΠ² ΠΈ ΠΏΡΠΈΠΌΠ΅ΡΠ΅ΠΉ Π² Π»Π΅Π³ΠΈΡΠΎΠ²Π°Π½Π½ΠΎΠΌ ΠΏΠΎΠ»ΡΠΏΡΠΎΠ²ΠΎΠ΄Π½ΠΈΠΊΠ΅, ΠΏΡΠΈΠ²ΠΎΠ΄ΡΡΡΡ ΠΊ ΠΈΠ·ΠΌΠ΅Π½Π΅Π½ΠΈΡ ΠΏΠΎΠ»ΠΎΠΆΠ΅Π½ΠΈΡ ΡΠΎΠΎΡΠ²Π΅ΡΡΡΠ²ΡΡΡΠΈΡ
ΡΡΠΎΠ²Π½Π΅ΠΉ Π² Π·Π°ΠΏΡΠ΅ΡΠ΅Π½Π½ΠΎΠΉ Π·ΠΎΠ½Π΅ ΠΌΠ°ΡΠ΅ΡΠΈΠ°Π»Π°
Π‘Π’Π Π£ΠΠ’Π£Π ΠΠ«Π Π ΠΠΠΠΠΠ’ΠΠ«Π Π‘ΠΠΠΠ‘Π’ΠΠ Π’ΠΠΠ ΠΠ«Π₯ Π ΠΠ‘Π’ΠΠΠ ΠΠ Π‘ΠΠ‘Π’ΠΠΠ« ΠΠΠ’ΠΠΠΠΠΠ ΠΠΠΠΠΠ¬Π’ΠβΠ’ΠΠΠΠ£Π ΠΠ ΠΠΠΠΠΠ¬Π’Π
By the method of melting special powder amounts of cobalt antimonide and cobalt telluride in vacuum, the solid solutions alloys of the CoSb1βx Tex system were synthesized with the NiAs structure. X-ray analysis results of the alloys confirmed the formation of a continuous series of solid solutions with a nickel-arsenide-type structure in the system. The constants a of the initial CoSb and CoTe compounds are close in values, which determines the course of the dependence a = f(x) that is practically parallel to the concentration axis. The dependence of the constant c on the concentration increases smoothly from 5.181 Γ
in CoSb to 5.371 Γ
in CoTe with a slight deflection to the concentration axis. The alloy density, determined by the hydrostatic weighing in carbon tetrachloride, has a linear dependence on the concentration. The concentration dependence of the micro hardness of the CoSb1βx Tex alloys passes through a weakly expressed maximum in the range of average compositions. Specific magnetization and magnetic susceptibility of the alloys are measured by the ponderomotive method in a magnetic field of 6.8 Β· 105 A/m in the temperature range 80β1200 K. At the temperature of liquid nitrogen, the value of specific magnetization is maximum (~6,0β6,5 ΠΡ Β· ΡΠΌ3 Β· Π³β1) in CoTe and solid solutions based on it. Solid solutions of compositions x = 0.4β0.9 have a magnetic transition temperature exceeding 1200 K.Β ΠΠ΅ΡΠΎΠ΄ΠΎΠΌ ΠΏΠ»Π°Π²Π»Π΅Π½ΠΈΡ ΡΠΎΠΎΡΠ²Π΅ΡΡΡΠ²ΡΡΡΠΈΡ
ΠΊΠΎΠ»ΠΈΡΠ΅ΡΡΠ² ΠΏΠΎΡΠΎΡΠΊΠΎΠ² ΡΠΎΠ΅Π΄ΠΈΠ½Π΅Π½ΠΈΠΉ Π°Π½ΡΠΈΠΌΠΎΠ½ΠΈΠ΄Π° ΠΊΠΎΠ±Π°Π»ΡΡΠ° ΠΈ ΡΠ΅Π»Π»ΡΡΠΈΠ΄Π° ΠΊΠΎΠ±Π°Π»ΡΡΠ° Π² Π²Π°ΠΊΡΡΠΌΠ΅ ΡΠΈΠ½ΡΠ΅Π·ΠΈΡΠΎΠ²Π°Π½Ρ ΡΠΏΠ»Π°Π²Ρ ΡΠ²Π΅ΡΠ΄ΡΡ
ΡΠ°ΡΡΠ²ΠΎΡΠΎΠ² ΡΠΈΡΡΠ΅ΠΌΡ CoSb1βx Tex . Π Π΅Π·ΡΠ»ΡΡΠ°ΡΡ ΡΠ΅Π½ΡΠ³Π΅Π½ΠΎΡΡΡΡΠΊΡΡΡΠ½ΠΎΠ³ΠΎ Π°Π½Π°Π»ΠΈΠ·Π° ΡΠΏΠ»Π°Π²ΠΎΠ² ΠΏΠΎΠ΄ΡΠ²Π΅ΡΠ΄ΠΈΠ»ΠΈ ΠΎΠ±ΡΠ°Π·ΠΎΠ²Π°Π½ΠΈΠ΅ Π² ΡΠΈΡΡΠ΅ΠΌΠ΅ Π½Π΅ΠΏΡΠ΅ΡΡΠ²Π½ΠΎΠ³ΠΎ ΡΡΠ΄Π° ΡΠ²Π΅ΡΠ΄ΡΡ
ΡΠ°ΡΡΠ²ΠΎΡΠΎΠ² ΡΠΎ ΡΡΡΡΠΊΡΡΡΠΎΠΉ Π½ΠΈΠΊΠ΅Π»Ρ- Π°ΡΡΠ΅Π½ΠΈΠ΄Π½ΠΎΠ³ΠΎ ΡΠΈΠΏΠ°. ΠΠΎΡΡΠΎΡΠ½Π½ΡΠ΅ Π° ΠΈΡΡ
ΠΎΠ΄Π½ΡΡ
ΡΠΎΠ΅Π΄ΠΈΠ½Π΅Π½ΠΈΠΉ CoSb ΠΈ CoTe Π±Π»ΠΈΠ·ΠΊΠΈ ΠΏΠΎ Π²Π΅Π»ΠΈΡΠΈΠ½Π°ΠΌ, ΡΡΠΎ ΠΎΠΏΡΠ΅Π΄Π΅Π»ΡΠ΅Ρ ΠΏΡΠ°ΠΊΡΠΈΡΠ΅ΡΠΊΠΈ ΠΏΠ°ΡΠ°Π»Π»Π΅Π»ΡΠ½ΡΠΉ ΠΎΡΠΈ ΠΊΠΎΠ½ΡΠ΅Π½ΡΡΠ°ΡΠΈΠΈ Ρ
ΠΎΠ΄ Π·Π°Π²ΠΈΡΠΈΠΌΠΎΡΡΠΈ a = f(x). ΠΠ°Π²ΠΈΡΠΈΠΌΠΎΡΡΡ ΠΏΠΎΡΡΠΎΡΠ½Π½ΠΎΠΉ Ρ ΠΎΡ ΠΊΠΎΠ½ΡΠ΅Π½ΡΡΠ°ΡΠΈΠΈ ΠΏΠ»Π°Π²Π½ΠΎ Π²ΠΎΠ·ΡΠ°ΡΡΠ°Π΅Ρ ΠΎΡ 5,181 Γ
Ρ CoSb Π΄ΠΎ 5,371 Γ
Ρ CoTe Ρ Π½Π΅Π±ΠΎΠ»ΡΡΠΈΠΌ ΠΏΡΠΎΠ³ΠΈΠ±ΠΎΠΌ ΠΊ ΠΎΡΠΈ ΠΊΠΎΠ½ΡΠ΅Π½ΡΡΠ°ΡΠΈΠΉ. ΠΠ»ΠΎΡΠ½ΠΎΡΡΡ ΡΠΏΠ»Π°Π²ΠΎΠ², ΠΎΠΏΡΠ΅Π΄Π΅Π»Π΅Π½Π½Π°Ρ ΠΌΠ΅ΡΠΎΠ΄ΠΎΠΌ Π³ΠΈΠ΄ΡΠΎΡΡΠ°ΡΠΈΡΠ΅ΡΠΊΠΎΠ³ΠΎ Π²Π·Π²Π΅ΡΠΈΠ²Π°Π½ΠΈΡ Π² ΡΠ΅ΡΡΠ°Ρ
Π»ΠΎΡΠΈΠ΄Π΅ ΡΠ³Π»Π΅ΡΠΎΠ΄Π°, ΠΈΠΌΠ΅Π΅Ρ Π»ΠΈΠ½Π΅ΠΉΠ½ΡΠΉ Ρ
Π°ΡΠ°ΠΊΡΠ΅Ρ Π·Π°Π²ΠΈΡΠΈΠΌΠΎΡΡΠΈ ΠΎΡ ΠΊΠΎΠ½ΡΠ΅Π½ΡΡΠ°ΡΠΈΠΈ. ΠΠΎΠ½ΡΠ΅Π½ΡΡΠ°ΡΠΈΠΎΠ½Π½Π°Ρ Π·Π°Π²ΠΈΡΠΈΠΌΠΎΡΡΡ ΠΌΠΈΠΊΡΠΎΡΠ²Π΅ΡΠ΄ΠΎΡΡΠΈ ΡΠΏΠ»Π°Π²ΠΎΠ² ΡΠΈΡΡΠ΅ΠΌΡ CoSb1βx Tex ΠΏΡΠΎΡ
ΠΎΠ΄ΠΈΡ ΡΠ΅ΡΠ΅Π· ΡΠ»Π°Π±ΠΎ Π²ΡΡΠ°ΠΆΠ΅Π½Π½ΡΠΉ ΠΌΠ°ΠΊΡΠΈΠΌΡΠΌ Π² ΠΎΠ±Π»Π°ΡΡΠΈ ΡΡΠ΅Π΄Π½ΠΈΡ
ΡΠΎΡΡΠ°Π²ΠΎΠ². ΠΠΎΠ½Π΄Π΅ΡΠΎΠΌΠΎΡΠΎΡΠ½ΡΠΌ ΠΌΠ΅ΡΠΎΠ΄ΠΎΠΌ Π² ΠΌΠ°Π³Π½ΠΈΡΠ½ΠΎΠΌ ΠΏΠΎΠ»Π΅ 6,8 Β· 105 Π/ΠΌ Π² ΠΈΠ½ΡΠ΅ΡΠ²Π°Π»Π΅ ΡΠ΅ΠΌΠΏΠ΅ΡΠ°ΡΡΡ 80β1200 Π ΠΈΠ·ΠΌΠ΅ΡΠ΅Π½Ρ ΡΠ΄Π΅Π»ΡΠ½Π°Ρ Π½Π°ΠΌΠ°Π³Π½ΠΈΡΠ΅Π½Π½ΠΎΡΡΡ ΠΈ ΠΌΠ°Π³Π½ΠΈΡΠ½Π°Ρ Π²ΠΎΡΠΏΡΠΈΠΈΠΌΡΠΈΠ²ΠΎΡΡΡ ΡΠΏΠ»Π°Π²ΠΎΠ² ΡΠΈΡΡΠ΅ΠΌΡ. ΠΡΠΈ ΡΠ΅ΠΌΠΏΠ΅ΡΠ°ΡΡΡΠ΅ ΠΆΠΈΠ΄ΠΊΠΎΠ³ΠΎ Π°Π·ΠΎΡΠ° Π²Π΅Π»ΠΈΡΠΈΠ½Π° ΡΠ΄Π΅Π»ΡΠ½ΠΎΠΉ Π½Π°ΠΌΠ°Π³Π½ΠΈΡΠ΅Π½Π½ΠΎΡΡΠΈ ΠΌΠ°ΠΊΡΠΈΠΌΠ°Π»ΡΠ½Π° (~6,0β6,5 ΠΡ Β· ΡΠΌ3 Β· Π³β1) Ρ ΡΠΎΡΡΠ°Π²ΠΎΠ² CoTe ΠΈ CoSb0,1Te0,9 ΠΈ ΠΏΡΠ°ΠΊΡΠΈΡΠ΅ΡΠΊΠΈ ΡΠ°Π²Π½Π° Π½ΡΠ»Ρ Ρ CoSb ΠΈ ΡΠ²Π΅ΡΠ΄ΡΡ
ΡΠ°ΡΡΠ²ΠΎΡΠΎΠ² Π½Π° Π΅Π³ΠΎ ΠΎΡΠ½ΠΎΠ²Π΅. Π’Π²Π΅ΡΠ΄ΡΠ΅ ΡΠ°ΡΡΠ²ΠΎΡΡ ΡΠΎΡΡΠ°Π²ΠΎΠ² Ρ
= 0,4β0,9 ΠΎΠ±Π»Π°Π΄Π°ΡΡ ΡΠ΅ΠΌΠΏΠ΅ΡΠ°ΡΡΡΠΎΠΉ ΠΌΠ°Π³Π½ΠΈΡΠ½ΠΎΠ³ΠΎ ΠΏΠ΅ΡΠ΅Ρ
ΠΎΠ΄Π°, ΠΏΡΠ΅Π²ΡΡΠ°ΡΡΠ΅ΠΉ 1200 Π
Π€ΠΎΡΠΌΠΈΡΠΎΠ²Π°Π½ΠΈΠ΅ ΠΈ ΡΠ»Π΅ΠΊΡΡΠΎΡ ΠΈΠΌΠΈΡΠ΅ΡΠΊΠΈΠ΅ ΡΠ²ΠΎΠΉΡΡΠ²Π° ΠΏΠ»Π΅Π½ΠΎΠΊ ΠΎΠΊΡΠΈΠ΄ΠΎΠ² Π½ΠΈΠΊΠ΅Π»Ρ ΠΈ ΠΊΠΎΠ±Π°Π»ΡΡΠ°
Films of cobalt oxide and nickel oxide on monocrystalline silicon substrates were obtained by electrochemical deposition from aqueous electrolyte solutions. Their structure and composition were studied by Raman microscopy and scanning electron microscopy. The results of the study by Raman spectroscopy showed that the obtained films are polycrystalline structures of cobalt (II, III) oxide and nickel (II) oxide, the crystalline perfection of which increases with an increase in the electrolyte temperature. It was found by scanning electron microscopy that nickel oxide films have a smoother surface, while cobalt oxide has a more developed structure consisting of lamellar crystals. The specific electrochemical capacity of cobalt oxide and nickel oxide films obtained under optimal conditions, measured by voltammetry, was 14.67 and 1634.08 F/g, respectively. The high specific electrochemical capacity of a nickel oxide film can be used to create efficient electrochemical devices and energy storage devices.ΠΠ΅ΡΠΎΠ΄ΠΎΠΌ ΡΠ»Π΅ΠΊΡΡΠΎΡ
ΠΈΠΌΠΈΡΠ΅ΡΠΊΠΎΠ³ΠΎ ΠΎΡΠ°ΠΆΠ΄Π΅Π½ΠΈΡ ΠΏΠΎΠ»ΡΡΠ΅Π½Ρ ΠΏΠ»Π΅Π½ΠΊΠΈ ΠΎΠΊΡΠΈΠ΄Π° ΠΊΠΎΠ±Π°Π»ΡΡΠ° ΠΈ ΠΎΠΊΡΠΈΠ΄Π° Π½ΠΈΠΊΠ΅Π»Ρ Π½Π° ΠΏΠΎΠ΄Π»ΠΎΠΆΠΊΠ°Ρ
ΠΌΠΎΠ½ΠΎΠΊΡΠΈΡΡΠ°Π»Π»ΠΈΡΠ΅ΡΠΊΠΎΠ³ΠΎ ΠΊΡΠ΅ΠΌΠ½ΠΈΡ. ΠΡΠΎΠ²Π΅Π΄Π΅Π½Ρ ΠΈΡΡΠ»Π΅Π΄ΠΎΠ²Π°Π½ΠΈΡ ΠΈΡ
ΡΡΡΡΠΊΡΡΡΡ ΠΈ ΡΠΎΡΡΠ°Π²Π° ΠΌΠ΅ΡΠΎΠ΄Π°ΠΌΠΈ ΡΠ°ΠΌΠ°Π½ΠΎΠ²ΡΠΊΠΎΠΉ ΠΌΠΈΠΊΡΠΎΡΠΊΠΎΠΏΠΈΠΈ ΠΈ ΡΠΊΠ°Π½ΠΈΡΡΡΡΠ΅ΠΉ ΡΠ»Π΅ΠΊΡΡΠΎΠ½Π½ΠΎΠΉ ΠΌΠΈΠΊΡΠΎΡΠΊΠΎΠΏΠΈΠΈ. Π Π΅Π·ΡΠ»ΡΡΠ°ΡΡ ΠΈΡΡΠ»Π΅Π΄ΠΎΠ²Π°Π½ΠΈΡ ΠΌΠ΅ΡΠΎΠ΄ΠΎΠΌ ΡΠ°ΠΌΠ°Π½ΠΎΠ²ΡΠΊΠΎΠΉ ΡΠΏΠ΅ΠΊΡΡΠΎΡΠΊΠΎΠΏΠΈΠΈ ΠΏΠΎΠΊΠ°Π·Π°Π»ΠΈ, ΡΡΠΎ ΠΏΠΎΠ»ΡΡΠ΅Π½Π½ΡΠ΅ ΠΏΠ»Π΅Π½ΠΊΠΈ ΠΏΡΠ΅Π΄ΡΡΠ°Π²Π»ΡΡΡ ΡΠΎΠ±ΠΎΠΉ ΠΏΠΎΠ»ΠΈΠΊΡΠΈΡΡΠ°Π»Π»ΠΈΡΠ΅ΡΠΊΠΈΠ΅ ΡΡΡΡΠΊΡΡΡΡ ΠΎΠΊΡΠΈΠ΄Π° ΠΊΠΎΠ±Π°Π»ΡΡΠ° (II, III) ΠΈ ΠΎΠΊΡΠΈΠ΄Π° Π½ΠΈΠΊΠ΅Π»Ρ (II), ΠΊΡΠΈΡΡΠ°Π»Π»ΠΈΡΠ΅ΡΠΊΠΎΠ΅ ΡΠΎΠ²Π΅ΡΡΠ΅Π½ΡΡΠ²ΠΎ ΠΊΠΎΡΠΎΡΡΡ
Π²ΠΎΠ·ΡΠ°ΡΡΠ°Π΅Ρ Ρ ΡΠ²Π΅Π»ΠΈΡΠ΅Π½ΠΈΠ΅ΠΌ ΡΠ΅ΠΌΠΏΠ΅ΡΠ°ΡΡΡΡ ΡΠ»Π΅ΠΊΡΡΠΎΠ»ΠΈΡΠ°. ΠΠ΅ΡΠΎΠ΄ΠΎΠΌ ΡΠΊΠ°Π½ΠΈΡΡΡΡΠ΅ΠΉ ΡΠ»Π΅ΠΊΡΡΠΎΠ½Π½ΠΎΠΉ ΠΌΠΈΠΊΡΠΎΡΠΊΠΎΠΏΠΈΠΈ Π±ΡΠ»ΠΎ ΡΡΡΠ°Π½ΠΎΠ²Π»Π΅Π½ΠΎ, ΡΡΠΎ ΠΏΠ»Π΅Π½ΠΊΠΈ ΠΎΠΊΡΠΈΠ΄Π° Π½ΠΈΠΊΠ΅Π»Ρ ΠΎΡΠ»ΠΈΡΠ°ΡΡΡΡ Π³Π»Π°Π΄ΠΊΠΎΠΉ ΠΏΠΎΠ²Π΅ΡΡ
Π½ΠΎΡΡΡΡ, Π² ΡΠΎ Π²ΡΠ΅ΠΌΡ ΠΊΠ°ΠΊ ΠΎΠΊΡΠΈΠ΄ ΠΊΠΎΠ±Π°Π»ΡΡΠ° ΠΎΠ±Π»Π°Π΄Π°Π΅Ρ Π±ΠΎΠ»Π΅Π΅ ΡΠ°Π·Π²ΠΈΡΠΎΠΉ ΡΡΡΡΠΊΡΡΡΠΎΠΉ ΠΈ ΡΠΎΡΡΠΎΠΈΡ ΠΈΠ· ΠΊΡΠΈΡΡΠ°Π»Π»ΠΎΠ² ΠΏΠ»Π°ΡΡΠΈΠ½ΡΠ°ΡΠΎΠΉ ΡΠΎΡΠΌΡ. ΠΠ·ΠΌΠ΅ΡΠ΅Π½Π½Π°Ρ ΠΌΠ΅ΡΠΎΠ΄ΠΎΠΌ Π²ΠΎΠ»ΡΡΠ°ΠΌΠΏΠ΅ΡΠΎΠΌΠ΅ΡΡΠΈΠΈ ΡΠ΄Π΅Π»ΡΠ½Π°Ρ ΡΠ»Π΅ΠΊΡΡΠΎΡ
ΠΈΠΌΠΈΡΠ΅ΡΠΊΠ°Ρ Π΅ΠΌΠΊΠΎΡΡΡ ΠΏΠ»Π΅Π½ΠΎΠΊ ΠΎΠΊΡΠΈΠ΄Π° ΠΊΠΎΠ±Π°Π»ΡΡΠ° ΠΈ ΠΎΠΊΡΠΈΠ΄Π° Π½ΠΈΠΊΠ΅Π»Ρ, ΠΏΠΎΠ»ΡΡΠ΅Π½Π½ΡΡ
Π² ΠΎΠΏΡΠΈΠΌΠ°Π»ΡΠ½ΡΡ
ΡΡΠ»ΠΎΠ²ΠΈΡΡ
, ΡΠΎΡΡΠ°Π²ΠΈΠ»Π° ΡΠΎΠΎΡΠ²Π΅ΡΡΡΠ²Π΅Π½Π½ΠΎ 14,67 ΠΈ 1634,08 Π€/Π³. ΠΡΡΠΎΠΊΠ°Ρ ΡΠ΄Π΅Π»ΡΠ½Π°Ρ ΡΠ»Π΅ΠΊΡΡΠΎΡ
ΠΈΠΌΠΈΡΠ΅ΡΠΊΠ°Ρ Π΅ΠΌΠΊΠΎΡΡΡ ΠΏΠ»Π΅Π½ΠΊΠΈ ΠΎΠΊΡΠΈΠ΄Π° Π½ΠΈΠΊΠ΅Π»Ρ ΠΌΠΎΠΆΠ΅Ρ Π±ΡΡΡ ΠΈΡΠΏΠΎΠ»ΡΠ·ΠΎΠ²Π°Π½Π° Π΄Π»Ρ ΡΠΎΠ·Π΄Π°Π½ΠΈΡ ΡΡΡΠ΅ΠΊΡΠΈΠ²Π½ΡΡ
ΡΠ»Π΅ΠΊΡΡΠΎΡ
ΠΈΠΌΠΈΡΠ΅ΡΠΊΠΈΡ
ΠΏΡΠΈΠ±ΠΎΡΠΎΠ² ΠΈ ΡΡΡΡΠΎΠΉΡΡΠ² Π½Π°ΠΊΠΎΠΏΠ»Π΅Π½ΠΈΡ ΡΠ½Π΅ΡΠ³ΠΈΠΈ
Π£ΡΠ»ΠΎΠ²ΠΈΡ ΡΠΈΠ½ΡΠ΅Π·Π°, ΠΊΡΠΈΡΡΠ°Π»Π»ΠΈΡΠ΅ΡΠΊΠ°Ρ ΡΡΡΡΠΊΡΡΡΠ° ΠΈ ΠΌΠ°Π³Π½ΠΈΡΠ½ΡΠ΅ ΡΠ²ΠΎΠΉΡΡΠ²Π° ΡΠ΅Π»Π΅Π½ΠΈΠ΄ΠΎΠ² MnβTmβSe
Single-phase compositions in the MnSeβTmSe quasi-binary section have been synthesized by the method of reactions in the solid phase. The crystal structure of polycrystalline powders has been studied in CuKΞ±-radiation. It was found that the samples in the concentration range 0 x 0.7 have a cubic structure of the space group Fm m3 . An increase in the concentration of Tm cations in the Mn1βxTmxSe compositions leads to an increase in the unit cell parameter a from 0.547 nm for the Mn0.975Tm0.025Se compound to 0.566 nm for the Mn0.3Tm0.7Se composition. Thin layers of Mn1βxTmxSe solid solutions were synthesized by the flash method on optically transparent glass substrates. The film thicknesses are in the range of values from 0.8 to 3.2 Β΅m. It has been established that Mn1βxTmxSe films also have the system NaCl, S.G.: Fm m3 . The composition of the Mn1βxTmxSe films corresponds to the chemical composition of the MnSeβTmSe charge powders. In the temperature range ~ 80β900 K, the va lues of the specific magnetization and magnetic susceptibility of the studied selenides were measured. The results obtained make it possible to determine the temperature regimes for the synthesis of new magnetic semiconductor substances, including those in the film state. The synthesized substances can be used in multifunctional microelectronic devices, as well as in the development of new materials capable of operating in wide temperature ranges and under the influence of external magnetic fields.ΠΠ΅ΡΠΎΠ΄ΠΎΠΌ ΡΠ΅Π°ΠΊΡΠΈΠΉ Π² ΡΠ²Π΅ΡΠ΄ΠΎΠΉ ΡΠ°Π·Π΅ ΡΠΈΠ½ΡΠ΅Π·ΠΈΡΠΎΠ²Π°Π½Ρ ΠΎΠ΄Π½ΠΎΡΠ°Π·Π½ΡΠ΅ ΡΠΎΡΡΠ°Π²Ρ Π² ΠΊΠ²Π°Π·ΠΈΠ±ΠΈΠ½Π°ΡΠ½ΠΎΠΌ ΡΠ°Π·ΡΠ΅Π·Π΅ MnSeβTmSe. ΠΡΠΈΡΡΠ°Π»Π»ΠΈΡΠ΅ΡΠΊΠ°Ρ ΡΡΡΡΠΊΡΡΡΠ° ΠΏΠΎΠ»ΠΈΠΊΡΠΈΡΡΠ°Π»Π»ΠΈΡΠ΅ΡΠΊΠΈΡ
ΠΏΠΎΡΠΎΡΠΊΠΎΠ² ΠΈΠ·ΡΡΠ΅Π½Π° Π² CuKΞ±-ΠΈΠ·Π»ΡΡΠ΅Π½ΠΈΠΈ. Π£ΡΡΠ°Π½ΠΎΠ²Π»Π΅Π½ΠΎ,ΡΡΠΎ ΠΎΠ±ΡΠ°Π·ΡΡ Π² ΠΈΠ½ΡΠ΅ΡΠ²Π°Π»Π΅ ΠΊΠΎΠ½ΡΠ΅Π½ΡΡΠ°ΡΠΈΠΉ 0 x 0,7 ΠΈΠΌΠ΅ΡΡ ΠΊΡΠ±ΠΈΡΠ΅ΡΠΊΡΡ ΡΡΡΡΠΊΡΡΡΡ ΠΏΡΠΎΡΡΡΠ°Π½ΡΡΠ²Π΅Π½Π½ΠΎΠΉ Π³ΡΡΠΏΠΏΡ Fm m3 . ΠΠ·ΠΌΠ΅Π½Π΅Π½ΠΈΠ΅ ΠΊΠΎΠ½ΡΠ΅Π½ΡΡΠ°ΡΠΈΠΈ ΠΊΠ°ΡΠΈΠΎΠ½ΠΎΠ² Tm Π² ΡΠΎΡΡΠ°Π²Π°Ρ
Mn1βxTmxSe ΠΏΡΠΈΠ²ΠΎΠ΄ΠΈΡ ΠΊ ΡΠ²Π΅Π»ΠΈΡΠ΅Π½ΠΈΡ ΠΏΠ°ΡΠ°ΠΌΠ΅ΡΡΠ° a ΡΠ»Π΅ΠΌΠ΅Π½ΡΠ°ΡΠ½ΠΎΠΉ ΠΊΡΠΈΡΡΠ°Π»Π»ΠΈΡΠ΅ΡΠΊΠΎΠΉ ΡΡΠ΅ΠΉΠΊΠΈ ΠΎΡ 0,547 Π½ΠΌ Π΄Π»Ρ ΡΠΎΡΡΠ°Π²Π° Mn0,975Tm0,025Se Π΄ΠΎ 0,566 Π½ΠΌ Ρ ΡΠΎΡΡΠ°Π²Π° Mn0,3Tm0,7Se. ΠΠ΅ΡΠΎΠ΄ΠΎΠΌ Β«flashΒ» Π½Π° ΠΏΠΎΠ΄Π»ΠΎΠΆΠΊΠ°Ρ
ΠΎΠΏΡΠΈΡΠ΅ΡΠΊΠΈ ΠΏΡΠΎΠ·ΡΠ°ΡΠ½ΠΎΠ³ΠΎ ΡΡΠ΅ΠΊΠ»Π° ΡΠΈΠ½ΡΠ΅Π·ΠΈΡΠΎΠ²Π°Π½Ρ ΡΠΎΠ½ΠΊΠΈΠ΅ ΡΠ»ΠΎΠΈ ΡΠ²Π΅ΡΠ΄ΡΡ
ΡΠ°ΡΡΠ²ΠΎΡΠΎΠ² Mn1βxTmxSe. Π’ΠΎΠ»ΡΠΈΠ½Ρ ΠΏΠ»Π΅Π½ΠΎΠΊ Π·Π°ΠΊΠ»ΡΡΠ΅Π½Ρ Π² ΠΈΠ½ΡΠ΅ΡΠ²Π°Π»Π΅ Π·Π½Π°ΡΠ΅Π½ΠΈΠΉ ΠΎΡ 0,8 Π΄ΠΎ 3,2 ΠΌΠΊΠΌ. Π£ΡΡΠ°Π½ΠΎΠ²Π»Π΅Π½ΠΎ, ΡΡΠΎ ΠΏΠ»Π΅Π½ΠΊΠΈ Mn1βxTmxSe ΡΠ°ΠΊΠΆΠ΅ ΠΎΠ±Π»Π°Π΄Π°ΡΡ ΡΠΈΠ½Π³ΠΎ-Π½ΠΈΠ΅ΠΉ NaCl, S.G.: Fm m3 . Π‘ΠΎΡΡΠ°Π² ΠΏΠ»Π΅Π½ΠΎΠΊ Mn1βxTmxSe ΡΠΎΠΎΡΠ²Π΅ΡΡΡΠ²ΡΠ΅Ρ Ρ
ΠΈΠΌΠΈΡΠ΅ΡΠΊΠΎΠΌΡ ΡΠΎΡΡΠ°Π²Ρ ΠΏΠΎΡΠΎΡΠΊΠΎΠ² ΡΠΈΡ
ΡΡ MnSeβTmSe. Π ΠΈΠ½ΡΠ΅ΡΠ²Π°Π»Π΅ ΡΠ΅ΠΌΠΏΠ΅ΡΠ°ΡΡΡ ~ 80β900 Π ΠΈΠ·ΠΌΠ΅ΡΠ΅Π½Ρ Π²Π΅Π»ΠΈΡΠΈΠ½Ρ ΡΠ΄Π΅Π»ΡΠ½ΠΎΠΉ Π½Π°ΠΌΠ°Π³Π½ΠΈΡΠ΅Π½Π½ΠΎΡΡΠΈ ΠΈ ΠΌΠ°Π³Π½ΠΈΡΠ½ΠΎΠΉ Π²ΠΎΡΠΏΡΠΈΠΈΠΌΡΠΈΠ²ΠΎΡΡΠΈ ΠΈΡΡΠ»Π΅Π΄ΡΠ΅ΠΌΡΡ
ΡΠ΅Π»Π΅Π½ΠΈΠ΄ΠΎΠ². ΠΠΎΠ»ΡΡΠ΅Π½Π½ΡΠ΅ ΡΠ΅Π·ΡΠ»ΡΡΠ°ΡΡ ΠΏΠΎΠ·Π²ΠΎΠ»ΡΡΡ ΠΎΠΏΡΠ΅Π΄Π΅Π»ΠΈΡΡ ΡΠ΅ΠΌΠΏΠ΅ΡΠ°ΡΡΡΠ½ΡΠ΅ ΡΠ΅ΠΆΠΈΠΌΡ ΡΠΈΠ½ΡΠ΅Π·Π° Π½ΠΎΠ²ΡΡ
ΠΌΠ°Π³Π½ΠΈΡΠ½ΡΡ
ΠΏΠΎΠ»ΡΠΏΡΠΎΠ²ΠΎΠ΄Π½ΠΈΠΊΠΎΠ²ΡΡ
Π²Π΅ΡΠ΅ΡΡΠ², Π² ΡΠΎΠΌ ΡΠΈΡΠ»Π΅ Π² ΠΏΠ»Π΅Π½ΠΎΡΠ½ΠΎΠΌ ΡΠΎΡΡΠΎΡΠ½ΠΈΠΈ. Π‘ΠΈΠ½ΡΠ΅Π·ΠΈΡΠΎΠ²Π°Π½Π½ΡΠ΅ Π²Π΅ΡΠ΅ΡΡΠ²Π° ΠΌΠΎΠ³ΡΡ Π±ΡΡΡ ΠΈΡΠΏΠΎΠ»ΡΠ·ΠΎΠ²Π°Π½Ρ Π² ΡΡΡΡΠΎΠΉΡΡΠ²Π°Ρ
ΠΌΠΈΠΊΡΠΎΡΠ»Π΅ΠΊΡΡΠΎΠ½ΠΈΠΊΠΈ ΠΌΠ½ΠΎΠ³ΠΎΡΡΠ½ΠΊΡΠΈΠΎΠ½Π°Π»ΡΠ½ΠΎΠ³ΠΎ Π½Π°Π·Π½Π°ΡΠ΅Π½ΠΈΡ, Π° ΡΠ°ΠΊΠΆΠ΅ ΠΏΡΠΈ ΡΠ°Π·ΡΠ°Π±ΠΎΡΠΊΠ΅ Π½ΠΎΠ²ΡΡ
ΠΌΠ°ΡΠ΅ΡΠΈΠ°Π»ΠΎΠ², ΡΠΏΠΎΡΠΎΠ±Π½ΡΡ
ΡΠ°Π±ΠΎΡΠ°ΡΡ Π² ΡΠΈΡΠΎΠΊΠΈΡ
ΠΈΠ½ΡΠ΅ΡΠ²Π°Π»Π°Ρ
ΡΠ΅ΠΌΠΏΠ΅ΡΠ°ΡΡΡ ΠΈ ΠΏΡΠΈ Π²ΠΎΠ·Π΄Π΅ΠΉΡΡΠ²ΠΈΠΈ Π²Π½Π΅ΡΠ½ΠΈΡ
ΠΌΠ°Π³Π½ΠΈΡΠ½ΡΡ
ΠΏΠΎΠ»Π΅ΠΉ
ΠΠΠΠΠΠ’ΠΠ‘ΠΠΠ ΠΠ’ΠΠΠΠΠΠΠ Π ΠΠ€Π€ΠΠΠ’ Π₯ΠΠΠΠ Π Π’ΠΠΠ ΠΠΠ Π ΠΠ‘Π’ΠΠΠ Π Mn0,55V0,45S
In the 80-300 K temperature range and magnetic fields with induction of up to 2.1 T are studied the characteristics of magnetoresistive properties and Hall effect of Mn0,55V0,45S solid solution. It was found that the Mn0,55V0,45S composition is a semiconductor with high p-type carrier concentration and low values of their mobility; a magnetoresistive effect is observed; solid solution has a noncollinear antiferromagnetic structure at temperatures ranges T < TN = 130 K; in the vicinity of the temperature T ~ 180 K in Mn0,55V0,45S there is a phase transition of semiconductor-semimetal type due to delocalization of charge carriers and the formation of micro areas with ferromagnetic ordering in an antiferromagnetic matrix. Magnetoresistive effect in this case, most likely is due to the magnetic inhomogeneity and can be interpreted in the framework of the electronic and magnetic phase separation consistent with the theory of current flow in heavily doped semiconductors.Π ΠΈΠ½ΡΠ΅ΡΠ²Π°Π»Π΅ ΡΠ΅ΠΌΠΏΠ΅ΡΠ°ΡΡΡ 80-300 Π ΠΈ ΠΌΠ°Π³Π½ΠΈΡΠ½ΡΡ
ΠΏΠΎΠ»ΡΡ
Ρ ΠΈΠ½Π΄ΡΠΊΡΠΈΠ΅ΠΉ Π΄ΠΎ 2,1 Π’Π» ΠΈΠ·ΡΡΠ΅Π½Ρ ΠΎΡΠΎΠ±Π΅Π½Π½ΠΎΡΡΠΈ ΠΌΠ°Π³Π½ΠΈΡΠΎΒ¬ΡΠ΅Π·ΠΈΡΡΠΈΠ²Π½ΡΡ
ΡΠ²ΠΎΠΉΡΡΠ² ΠΈ ΡΡΡΠ΅ΠΊΡΠ° Π₯ΠΎΠ»Π»Π° ΡΠ²Π΅ΡΠ΄ΠΎΠ³ΠΎ ΡΠ°ΡΡΠ²ΠΎΡΠ° Mn0,55V0,45S. Π£ΡΡΠ°Π½ΠΎΠ²Π»Π΅Π½ΠΎ, ΡΡΠΎ ΡΠΎΡΡΠ°Π² Mn0,55V0,45S ΡΠ²Π»ΡΠ΅ΡΡΡ ΠΏΠΎΠ»ΡΠΏΡΠΎΠ²ΠΎΠ΄Π½ΠΈΠΊΠΎΠΌ Ρ Π²ΡΡΠΎΠΊΠΈΠΌΠΈ Π·Π½Π°ΡΠ΅Π½ΠΈΡΠΌΠΈ ΠΊΠΎΠ½ΡΠ΅Π½ΡΡΠ°ΡΠΈΠΈ Π½ΠΎΡΠΈΡΠ΅Π»Π΅ΠΉ Π·Π°ΡΡΠ΄Π° Ρ-ΡΠΈΠΏΠ° ΠΈ Π½ΠΈΠ·ΠΊΠΈΠΌΠΈ Π²Π΅Π»ΠΈΡΠΈΠ½Π°ΠΌΠΈ ΠΈΡ
ΠΏΠΎΠ΄Π²ΠΈΠΆΠ½ΠΎΡΡΠΈ; ΠΎΠ±Π»Π°Π΄Π°Π΅Ρ ΠΌΠ°Π³Π½ΠΈΡΠΎΡΠ΅Π·ΠΈΡΡΠΈΠ²Π½ΡΠΌ ΡΡΡΠ΅ΠΊΡΠΎΠΌ; ΠΈΠΌΠ΅Π΅Ρ Π½Π΅ΠΊΠΎΠ»Π»ΠΈΠ½Π΅Π°ΡΠ½ΡΡ Π°Π½ΡΠΈΡΠ΅ΡΡΠΎΠΌΠ°Π³Π½ΠΈΡΠ½ΡΡ ΡΡΡΡΠΊΡΡΡΡ Π² ΠΎΠ±Π»Π°ΡΡΠΈ ΡΠ΅ΠΌΠΏΠ΅ΡΠ°ΡΡΡ Π’ < Π’N = 130 Π; Π² ΠΎΠΊΡΠ΅ΡΡΠ½ΠΎΡΡΠΈ ΡΠ΅ΠΌΠΏΠ΅ΡΠ°ΡΡΡΡ Π’ ~ 180 Π Π² Mn0 55V0 45S ΠΈΠΌΠ΅Π΅Ρ ΠΌΠ΅ΡΡΠΎ ΡΠ°Π·ΠΎΠ²ΠΎΠ΅ ΠΏΡΠ΅Π²ΡΠ°ΡΠ΅Π½ΠΈΠ΅ ΡΠΈΠΏΠ° ΠΏΠΎΠ»ΡΠΏΡΠΎΠ²ΠΎΠ΄Π½ΠΈΠΊ-ΠΏΠΎΠ»ΡΠΌΠ΅ΡΠ°Π»Π», ΠΎΠ±ΡΡΠ»ΠΎΠ²Π»Π΅Π½Π½ΠΎΠ΅ Π΄Π΅Π»ΠΎΠΊΠ°Π»ΠΈΠ·Π°ΡΠΈΠ΅ΠΉ Π½ΠΎΡΠΈΡΠ΅Π»Π΅ΠΉ Π·Π°ΡΡΠ΄Π° ΠΈ ΠΎΠ±ΡΠ°Π·ΠΎΠ²Π°Π½ΠΈΠ΅ΠΌ ΠΌΠΈΠΊΡΠΎΠΎΠ±Π»Π°ΡΡΠ΅ΠΉ Ρ ΡΠ΅ΡΡΠΎΠΌΠ°Π³Π½ΠΈΡΠ½ΡΠΌ ΡΠΏΠΎΡΡΠ΄ΠΎΡΠ΅Π½ΠΈΠ΅ΠΌ Π² Π°Π½ΡΠΈΡΠ΅ΡΡΠΎΠΌΠ°Π³Π½ΠΈΡΠ½ΠΎΠΉ ΠΌΠ°ΡΡΠΈΡΠ΅. ΠΠ°Π³Π½ΠΈΡΠΎΡΠ΅Π·ΠΈΡΡΠΈΠ²Π½ΡΠΉ ΡΡΡΠ΅ΠΊΡ Π² ΡΡΠΎΠΌ ΡΠ»ΡΡΠ°Π΅, Π²Π΅ΡΠΎΡΡΠ½Π΅Π΅ Π²ΡΠ΅Π³ΠΎ, ΠΎΠ±ΡΡΠ»ΠΎΠ²Π»Π΅Π½ ΠΌΠ°Π³Π½ΠΈΡΠ½ΠΎΠΉ Π½Π΅ΠΎΠ΄Π½ΠΎΡΠΎΠ΄Π½ΠΎΡΡΡΡ ΠΈ ΠΌΠΎΠΆΠ΅Ρ Π±ΡΡΡ ΠΏΡΠΎΠΈΠ½ΡΠ΅ΡΠΏΡΠ΅ΡΠΈΡΠΎΠ²Π°Π½ Π² ΡΠ°ΠΌΠΊΠ°Ρ
ΠΌΠΎΠ΄Π΅Π»ΠΈ ΡΠ»Π΅ΠΊΡΡΠΎΠ½Π½ΠΎΠ³ΠΎ ΠΈ ΠΌΠ°Π³Π½ΠΈΡΠ½ΠΎΠ³ΠΎ ΡΠ°Π·Π΄Π΅Π»Π΅Π½ΠΈΡ ΡΠ°Π·, ΡΠΎΠ³Π»Π°ΡΡΡΡΠ΅ΠΉΡΡ Ρ ΡΠ΅ΠΎΡΠΈΠ΅ΠΉ ΠΏΡΠΎΡΠ΅ΠΊΠ°Π½ΠΈΡ ΡΠΎΠΊΠ° Π² ΡΠΈΠ»ΡΠ½ΠΎ Π»Π΅Π³ΠΈΡΠΎΠ²Π°Π½Π½ΡΡ
ΠΏΠΎΠ»ΡΠΏΡΠΎΠ²ΠΎΠ΄Π½ΠΈΠΊΠ°Ρ
SYNTHESIS AND OPTICAL PROPERTIES OF Ni-DOPED ZnO GROWN BY ELECTROCHEMICAL DEPOSITION
This paper is targeted at studying the patterns of deposition by electrochemical method of Ni-doped ZnO films, including registering and analyzing their photoluminescence and Raman scattering spectra. We have studied the electrochemical deposition of nickel-doped zinc oxide films on single-crystal silicon substrates from aqueous solutions of zinc and nickel nitrates. The deposition was conducted from aqua solutions of Zn and Ni nitrates in a standard double-electrode electrochemical cell in galvanostatic mode with the current density from 5 to 20 mA/cm2 and deposition time from 5 to 30 min. The Raman scattering on nickel-doped zinc oxide films was examined via laser Raman spectrometer SOL Instruments Confotec NR500. The analysis of Raman spectra showed that an increase of cathodic current density deposition leads to an enhanced concentration of a doping agent in the films. Photoluminescence spectra of the samples were registered on a laser spectral measuring system based on monochromator-spectrograph SOLAR TII MS 7504i where a monochromatic line with the 345-nm wavelength, which was extracted from the spectrum of Xe-lamp by means of double monochromator Solar TII DM160, was used as the excitation source. The research demonstrates that the emmission intensity increases with the thickness of the deposited film, and the position of maximums of the radiation line remains unchanged in a visible wavelength range and on photoluminescence spectra with fixed current density. The change in the density of the cathode current leads to a shift in the position of the photoluminescence spectra maximum, which indicates restructuring of defects and dopant atoms in the doped semiconductor, which in turn changes the position of the corresponding levels in the band gap of the material
Magnetic Properties of Bulk and Thin NdβFeββB Films after Corrosion Action
The corrosion action for bulk and thin NdβFeββB films magnets in different corrosion media was studied. The thin Nd-Fe-B films of 100 nm β€ d β€ 1000 nm were deposited on glass substrate by "flash" evaporation method. The structure and microstructure of the samples were studied by X-ray diffraction analysis, scanning electron microscopy. The temperature dependence of the magnetization before and after corrosion action was carried out by ponderomotive method in the temperature range 80 β€ T β€ 800 K. It is shown that the specific magnetizations of the thin Nd-Fe-B films with d β₯ 1000 nm are comparable to those measured for the powder samples. The values of the coercive and saturation fields were determined from the hysteresis loops measurements
Crystal Structure and Magnetic Properties of Solid Solutions
The synthesis of polycrystalline solid solutions is carried out by solid state reaction method followed by quenching from the temperature of 1370 K. The X-ray diffraction studies realized at 300 K revealed that the structure of the single phase samples in the 0 < x < 0.15 concentration range is identified on base a face centered cubic crystal cell of Fm3m space group. The heating of the solid solutions to 900 K does not affect on the magnetic susceptibility as the dependences is identical to the measurements in the "heating-cooling" regime. Comparing the research results of magnetic properties of the solid solutions with those of solid solutions, we can conclude that substitution of manganese ions by gadolinium in manganese selenide lead to more changes in the basic magnetic characteristics than in manganese sulfide
Eο¬ect of Co-Doping on Magnetic Properties of Bismuth Ferrite
The eο¬ect of co-doping on structure and magnetic properties of the BiFeO3-based multiferroics with a partial
isovalent substitution of bismuth for La3+, Gd3+, Dy3+, and Er3+ ions have been experimentally investigated by
X-ray diο¬raction and magnetic methods. The ceramic R1xR20.2βxBi0.8FeO3 type (x = 0, 0.05, 0.10, 0.15, 0.20;
R1, R2 = La, Gd, Dy, Er) samples have been prepared by a solid-state reaction method under cold pressing at
high pressure P = 4 GPa. Temperature dependences of magnetization for the co-doped BiFeO3 demonstrate
magnetic βweak ferromagneticβantiferromagneticβ phase transitions in a high temperature range T = 550β650 K.
The presence of a weak ferromagnetism in all compositions is conο¬rmed by open loops of magnetic ο¬eld dependences.
It has been found out that the magnetic characteristics strongly depend on the degree of substitution, temperature,
and magnitude of magnetic ο¬eld