MAGNETIC MATERIAL

Abstract: A magnetic material consisting of the following components at the following ratios, in atomic percent: at least one of the rare-earth elements chosen from the group: neodymium, praseodymium 12.0-17.0, at least one of the rare-earth elements chosen from the group: dysprosium, terbium 0.1-5.0, at least one of the elements chosen from the group: aluminium, niobium, chromium 0.5-4.0, at least one of the elements chosen from the group: titanium, hafnium, zirconium, vanadium, tantalum 0.1-1.5, cobalt 2.0-6.0, boron 6.5-8.5, uranium 0.05-1.5, iron remainder. Uranium is used in the form of its isotopes 238 and 235. In addition, the magnetic material may contain gallium and scandium.

Description: FIELD OF TECHNOLOGY THE INVENTION PERTAINS TO. The present invention relates to the special materials having particular physical properties, more specifically, to a magnetic material. DESCRIPTION OF PRIOR ART. The known and wide-spread magnetic materials of Fe-B-R and Fe-B-Co-R systems, having high magnetic energy (BH/2)max, are widely used in electric motors, generators, magnetic clutches, etc. The said materials are used also in various household appliances, namely, in audio- and videorecorders, in computer peripheral devices, in mixers, coffee-grinders, hair-driers, vacuum cleaners, refrigerators, etc, Nevertheless relatively low coercive force iHc values characteristic of the said materials set some limits on the scope of their application. It is known that when the temperature of the material of which a permanent magnet is made raises, the coercive force (iHc) of the said material decreases, and a permanent magnet may become altogether demagnetized if exposed to higher temperatures; but when at room temperature the coercive force (iHc) of a magnet is relatively high, such demagnetizing effect produced by temperature rise is negligible. Besides, higher coercive force (iHc) of the material of which a permanent magnet is made makes it possible to reduce the thickness of the permanent magnet maintaining its designed characteristics.Therefore increasing iHc of the materials used for permanent magnets manufacturing is a high-priority task faced by modern technology. Permanent magnets manufacturing using the known materials of Fe-B-R and Fe-B-Co-R systems requires relatively high specific power inputs. Known is a magnetic material of Fe-B-R system (EP No.0134305). In the said known material R is a sum of R₁ and R₂, wherein R₁ is at least one rare-earth element selected from a group comprising neodymium (Nd) and praseodymium (Pr), and R₂ is at least one rare-earth element selected from a group comprising dysprosium (Dy),terbium (Tb), gadolinium (Gd), holmium (Ho), erbium (Er),thulium (Tu) and ytterbium (Yb).The known material comprises also M additive being at least one element of the group consisting of chromium (Cr), tantalium (Ta), niobium (Nb), aluminium (Al), vanadium (V), wolfram (W), molybdenum (Mo). In the known material the abovementioned elements are contained at the following ratio (at.%): 0.05-5% R₁, 12.5-20%R, 4-20% B and the balance is ferrum (Fe) with additive M being 9% max. Known in the prior art is the fact that the properties of a magnetic material of Fe-B-R system depend on the number of the grains and sizes thereof, on specific magnetization and on coercive force of basic phase (R)₂Fe₁₄B, as well as on the quantity, structure and phases components insulating the grains of basic phase (R)₂Fe₁₄B. To reach maximum values for the parameters characterizing a magnetic material, e.g. (BH)max, operational temperature (Tmo), basic phase (R)₂Fe₁₄B must be present in the material in the quantities approaching, 100%, it must have grains of optimum sizes and maximum specific magnetization and coercive force values; and the phases insulating the grains of basic phase (R)₂Fe₁₄B from each other must be present in minimum quantities on the grains edges, and the said phases must be non-magnetic. The presence of heavy rare-earth elements in the known material, namely,dysprosium (Dy), terbium (Tb), gadolinium (Gd), holmium (Ho), etc.causes some increase in anisotropy field H A of basic phase (NdR)₂Fe₁₄B of the magnetic material, which in turn, causes increase in coercive force iHc. Nevertheless the ion exchange between heavy rare-earth elements and ferrum (Fe) leads to antiferromagnetic orientation of their magnetic moments considerably reducing specific magnetization and, consequently, reducing residual induction Br and (BH)max. In order to increase residual induction Br such elements as Cr,Al,Nb,etc. were additionally introduced into the magnetic material and simultaneously the quantities of dysprosium and terbium contained in the material were reduced, thus making the material cheaper because the last two elements are rather expensive. The main effect which the abovementioned additives produce on coercive force is caused by the formation of neodymium-enriched weak magnetic phases insulating the grains of the basic phase from each other. Some of these elements, .e.g. Al, improve wetting of the grains of basic phase Nd₂Fe₁₄B with a liquid phase,which makes it possible to accelerate sintering in the course of magnetic material manufacturing. The grain sizes of basic phase of the magnetic material very in the range of 0.3-80 m, therefore the material has relatively low coercive force iHc. The abovementioned details show that the magnetic properties of the said material are relatively low, namely coercive force iHc = 5-20 KOe (398-1592 kA/m); energy product (BH)max = 5-38.4 MGOe (39.8-305.7 kJ/m³); residual induction Br = 5-12 KG (0.5-1.2 T). Higher (BH)max values correspond to lower coercive force iHc values and vice versa, lower iHc values correspond to higher (BH)max values. At optimum components ratio in the known material coercive force iHc is 10 KOe (796 kA/m) min., (BH)max is 20 MGOe (159.2 kJ/m³) min., and residual induction Br is 9 KG (0.9 T) min. At temperatures higher than 80-100°C the magnetic properties of the known material drop because this material has low Curie temperature (Tc = 310°C). For these reasons the said material may find only a limited application in electric power motors having high specific power. The known material requires relatively high specific power inputs during the process of magnets manufacturing due to high ingot strength as well as high sintering temperatures. Known in a magnetic material of Fe-B-Co-R system (EP 0106948 B₁) having higher Curie temperature. In the known material R₁ is the sum of R₁ and R₂, wherein R₁ is at least one rare-earth element selected from a group consisting of neodymium (Nd) and praseodymium (Pr), and R₂ is at least one heavy rare-earth element. The known material comprises also additive M being the sum of M₁ and M₂, wherein M₁ is at least one element selected from a group consisting of aluminium (Al), niobium (Nb), chromium (Cr), and others, and M₂ is at least one element selected from a group comprising titanium (Ti), hafnium (Hf), zirconium (Zr), vanadium (V), tantalum (Ta), etc. In the known material the abovementioned components are present in the following ratio (at.%): 8-30% R = R₁ + R₂; 2-28% B, max. 50% Co, and the balance is ferrum (Fe) with additive M = M₁ + M₂, 12.5% max. The presence of cobalt (Co) in the magnetic material increases Curie temperature (Tc) which reaches 750°C, making it possible to use the known material at operational temperatures of 120-160°C without considerable loss in its magnetic properties. But when a material contains high cobalt (Co) quantities, magnetic soft phase appears, which causes decrease in coercive force iHc. To compensate for the decrease in coercive force iHc the metal is alloyed with increased quantities of rare-earth elements and boron (B) which in turn causes decrease in (BH)max. The latter is accounted for by a relative decrease in the quantity of basic phase Nd₂Fe₁₄B. In the known magnetic material average grain sizes of the basic phase are within the range of 1-100 µm which accounts for low coercive force iHc. Besides the known material is characterized by a considerably low manufacturability related to high strength of the ingots made of this material as well as high sintering temperature which results in high specific power inputs required for ingots grinding and sintering. DISCLOSURE OF THE INVENTION. The principal object of the invention is a magnetic material having such a chemical composition and components ratio (at.%) which provide high coercive force iHc values achieved through optimization of the structure of the phases insulating the grains in basic phase Nd₂Fe₁₄B, as well as through optimization of grain sizes in the basic phase. The said magnetic material requires relatively low specific power inputs in the course of its manufacturing. The said magnetic material comprising Fe-B-Co-R, wherein R is the sum of R₁ and R₂, and R₁ is at least one of rare-earth elements selected from a group consisting of neodymium (Nd), and praseodymium (Pr), R₂ is at least one of rare-earth elements selected from a group consisting of dysprosium (Dy), and terbium (Tb), and an additive M which is the sum of M₁ and M₂, wherein M₁ is at least one of the elements selected from a group consisting of aluminium (Al), niobium (Nb), chromium (Cr), and M₂ is at least one of the elements selected from a group consisting of titanium (Ti), hafnium (Hf), zirconium (Zr), vanadium (V), tantalum (Ta), according to the invention additionally comprises uranium (U), the components ratio being as follows (at.%): at least one rare-earth element selected from a group consisting of neodymium and praseodymium : 12.0-17.0; at least one rare-earth element selected from a group consisting of dysprosium and terbium : 0.1-5.0; at least one element selected from a group consisting of aluminium, niobium, chromium : 0.5-4.0; at least one element selected from a group consisting of titanium, hafnium, zirconium, vanadium, tantalum ; 0.1-1.5; cobalt : 2.0-6.0 boron : 6.5-8.5 uranium : 0.05-1.5 ferrum : the balance It is necessary that uranium (U) should contain the following isotopes: 238 U : 99.7-99.9999 235 U : 0.0001-0.3 The magnetic material according to the invention shows high magnetic properties, namely, it has increased coercive force iHc value of 25 KOe (1990 kA/m) at (BH)max = 29-36 MGOe (230.8-286.6) and specific power inputs of 0.71-0.9. These properties are accounted for by the fact that the introduction of uranium (U) into the magnetic material improves insulating properties of inter-grain phases like U-Fe-Co-R and increases anisotropy field of basic phase (U + R)₂Fe₁₄B. Radiographic analysis of the magnetic material according to the invention has shown that uranium ions partially substitue for neodymium ions in the lattice of basic phase Nd₂Fe₁₄B, but generally uranium ions are present in neodymium-enriched inter-grain phases insulating the grains of the basic phase. Magnetic properties of uranium (U) compounds depend on the level of localization of 5f electrons in uranium ions. In a compound containing uranium (U) and ferrum (Fe), valence uranium electrons pass into "d" zone of ferrum (Fe) until they occupy it completely causing a decrease in magnetic moment of a ferrum (Fe) atom. With uranium (U) in the magnetic material being 0.05 at.% max., the said atom experts practically no influence on the magnetic moment of ferrum (Fe) atoms and that of anisotropy field H A of the basic phase. When the uranium (U) content is within the abovementioned range of 0.05-1.5 at.%, the uranium ions substituting for neodymium ions in the lattice of the basic phase increase anisotropy field H A of the basic phase due to the partial localization of valence electrones (5f electrons) consequently increasing coercive force iHc. Further, when uranium (U) comes into the lattice of inter-grain phases U-Fe-Co-R, it reduces their Curie temperature to the values considerably lower than room temperature; therefore at operational temperatures in permanent magnets made of the claimed material inter-grain phases U-Fe-Co-R become paramagnetic providing a reliable magnetic insulation for the grains of the basic phase, thus increasing coercive force. Besides, the enrichment of inter-grain phases with uranium reduces wetting of the grains of the basic phase which results in higher brittleness of casted alloy. The magnetic material according to the invention is characterized by lower specific power inputs required for the magnetic powder preparation and sintering, owing to higher brittleness and improved sintering quality of casted material which allows to carry out sintering at lower temperatures of 1000-1100°C. When uranium concentrations in the magnetic material exceed 1.5 at.%, its concentration in basic phase Nd₂Fe₁₄B reaches such a level at which magnetic moments of ferrum (Fe) atoms as well as anisotropy field of the basic phase decrease abruptly (as a result of 5f electrons delocalization) causing decrease in coercive force iHc. Alloying with uranium improves the properties of a magnetic material increasing its coercive force iHc by reducing grain sizes in basic phase Nd₂Fe₁₄B to 4-6 m. The average grain sizes vary inversely as the uranium concentrations in the material, i.e. the higher concentrations present, the smaller grain sizes are observed. Natural uranium is characterized by α activity which depends mainly on ²³⁵U isotope. When uranium isotope content is within the above specified boundary ranges, exposure rate of α irradiation does not exceed natural background levels caused by space irradiation and irradiation from isotopes naturally distributed in the environment. The introduction of scandium (Sc) into a magnetic material increases its coercive force iHc, causing modification of fine structures of inter-grain phases which insulate the grains of basic phase Nd₂Fe₁₄ because scandium is known to form hard solutions with rare-earth elements. Besides scandium ions partially substituted with neodymium ions in phase (U+R)₂Fe₁₄B contribute to the localization of 5f uranium electrons thus increasing anisotropy field H A and coercive force iHc. The introduction of gallium (Ga) into a magnetic material increases its coercive force iHc for the following reasons. Gallium substitutes for ferrum in basic phase Nd₂Fe₁₄B occupying the positions 8j₁ and 4c in lattice points which are bounded by antiferromagnetic interactions, which results in some increase in Curie temperature. But the main positive effect produced by gallium is related to the fact that gallium improves wetting of the grains of basic phase Nd₂Fe₁₄B with the liquid phase thus improving their insulation which causes an increase in coercive force iHc. With gallium (Ga) content in the material exceeding 4 at.% anisotropy field H A in basic phase Nd₂Fe₁₄B decreases and consequently a decrease in coercive force iHc occurs. BRIEF DESCRIPTION OF THE DROWINGS. Further objects of the invention as well as advantages thereof are disclosed in the examples of specific embodiments of the invention provided below, and in the drawings where Fig.1 is a graph of coercive force iHc versus uranium (U) content; Fig.2 is a graph of coercive force iHc versus average grain sizes; Fig.3 is a graph of coercive force iHc versus scandium (Sc) content; Fig.4 is a graph of coercive force iHc versus gallium (Ga) content. VARIANTS OF SPECIFIC EMBODIMENTS OF THE INVENTION. Magnetic material according to the invention comprises Fe-B-Co-U-R-M. R is the sum of R₁ and R₂, wherein R₁ is at least one rare-earth element selected from a group consisting of neodymium (Nd) and praseodymium (Pr), and R₂ is at least one rare-earth element selected from a group consisting of dysprosium (Dy) and terbium (Tb). Additive M is the sum of M₁ and M₂, wherein M₁ is at least one element selected from a group consisting of aluminium (Al), niobium (Nb), chromium (Cr), gallium (Ga), and M₂ is at least one element selected from a group consisting of titanium (Ti), hafnium (Hf),zirconium (Zr), vanadium (V), tantalum (Ta), scandium (Sc). The above-mentioned components are present in the said magnetic material in the following ratio (at.%): neodymium and/or prasedymium 12.0-17.0 dysprosium and/or terbium 9.1-5.0 aluminium and/or niobium, and/or gallium, and/or chromium 0.5-4.0 titanium and/or hafnium, and/or zirconium, and/or vanadium, and/or tantalum, and/or scandium 0.1-1.5 cobalt 2.0-6.0 boron 6.5-8.5 uranium 0.05-1.5 ferrum the balance Uranium contained in the magnetic material accroding to the invention has the following isotope content (at.%): 238 U 99.7-99.9999 235 U 0.0001-0.3 The intensity of exposure does of α irradiation does not exceed background levels caused by space irradiation and irradiation from isotopes naturally distributed in the environment. The total content of neodymium and/or proseodymium, dysprosium and/or terbium and uranium in the magnetic material is within the range of 15-17.6 at.%. The total content in the magnetic material of at least one element selected from a group consisting of aluminium (Al), niobium (Nb), chromium (Cr), gallium (Ga), and at least one element selected from a group consisting of titanium (Ti), hafnium (Hf), zirconium (Zr), vanadium (V), tantalum (Ta), scandium (Sc),is within the range of 0.6-4.5 at.%. The magnetic material according to the invention is produced using the method described below. First in vacuum induction furnace under argon atmosphere and under the pressure of 300 mm Hg a melt is produced which comprises the same components as the magnetic materials described in Table 1. Boron is introduced into the melt in the form of Fe - 10 wt.% B alloying composition. Then the melt thus produced is casted into a copper water-cooled mould to make an ingot. The latter is subjected to rough grinding up to particle sizes of less than 500 m; then a finer grinding is performed in a vibratory ball mill up to particle sizes of 1-5 µm. To create magnetic texture the powder thus produced is placed into a magnetic field having the intenity of 10 kOe and after that the powder is compacted applying the force of 0.1-5 t/cm². Then the compacted billet is sintered at 1000-1200°C during 2 hours and after that a thermal treatment of the sintered billet is performed at temperatures within the range of 400-1000°C. Examples illustrating the production of the magnetic material according to the invention are provided below. EXAMPLE 1. Magnetic material Fe-5Co-7B-13.5Hd-1.5Dy-1Al-0.5Ti-0.1Sc-xU is produced using the following method. In vacuum induction furnace under argon atmosphere and under the pressure of 300 mm Hg a melt is produced which comprises the same components as the magnetic material described in Table 1 (3,27,28,29,31,32,39). An ingot is produced out of the melt as described above; then the ingot is grinded up to particle sizes of 3-4 µm. Then the grinded particles are placed into the magnetic field having the intensity of 10 kOe (796 kA/m) and after that the powder is compacted applying the force of 9.4 t/cm². Then the compacted billet is sintered at 1030-1130°C during 2 hours and after that a thermal treatment of the sintered billet is performed at temperatures within the range of 560-910°C. The values for the magnetic properties of the said material and those for specific power inputs are provided in Table 1. The dependency between uranium (U) content and the magnitude of coercive force iHc is illustrated by a graph in Fig.1. The study of the abovementioned curve shows that when the values of uranium content in the magnetic material are within the range of x = 0.05-0.2at.% coercive force iHc sharply increases up to the value of 23 kOe (1830.8 kA/m), which is caused by two factors. The first factor is the decrease in average grain sizes in basic phase Nd₂Fe₁₄B (Fig.2 shows that grain sizes monotonically decrease when U content increases); and the second factor is related to the partial substitution of neodymium ions with uranium ions when the localization of 5f electrons is preserved and anisotropy field H A of the basic phase Nd₂Fe₁₄B increases. At x=0.2-1.5 at.% (Fig.1) coercive force iHc valuer do not vary being 23.1 kOe (1838.8 kA/m) and do not depend on uranium content values. It is accounted for by two opposite processes. On the one hand, uranium quantity in the basic phase increases which leads to partial delocalization of its 5f electrons and consequently to decrease in anisotropy field of basic phase Nd₂Fe₁₄B. On the other hand, grinding of the grains contributes to the increase in iHc, which occurs mainly due to the reduction in the number of centers producing domains of opposite magnetization. At the concentrations of x>1.5 at.% U the process of delocalization of uranium 5f electrons in the basic phase leads to a sharp lowering of anisotropy field and consequently to a decrease in coercive force iHc. EXAMPLE 2. Magnetic material Fe-5Co-7B-13.5Nd-0.5U-1.5Dy-1Al-0.5Ti-xSc is produced using the following method. In vacuum induction furnace under argon atmosphere and under the pressure of 300 mm Hg a melt is produced which comprises the same components as the magnetic material described in Table 1 (3,16,63,64,65). An ingot is produced out of the melt as described above; then the ingot is grinded up to particle sizes of 3 µm. Then the grinded particles are placed into the magnetic field having the intensity of 10 kOe (796 kA/m) and after that the powder is compacted applying the force of 0.8 t/cm². Then the compacted billet is sintered at 1070°C during 2 hours and after that a thermal treatment of the sintered billet is performed at temperatures within the ranges of 560-910°C. The values for the magnetic properties of the said materials and those for specific power inputs are provided in Table 1. The influence of Sc content on coercive force iHc values is illustrated by a graph in Fig.3. The study of the abovementioned curve shows that with Sc content in the magnetic material being within the range of x=0.03-0.1 at.% a sharp increase in coercive force iHc values up to those of 23 kOe (1830.8 kA/m) occurs. This is accounted for by the fact that Sc ions in basic phase Nd₂Fe₁₄B contribute to the localization of 5f electrons or uranium ions. Besides, Sc forms hard solutions with all rare-earth elements modifying the structures of inter-grain phases, as a result of which the number of centers producing domains of opposite magnetizing is reduced. The increase in scandium content to more than 1.5 at.% leads to a decrease in iHc values due to lowering of anisotropy field of basic phase Nd₂Fe₁₄B. Scandium causes increase in coercive force only when it is combined with such elements as U and Dy. EXAMPLE 3. Magnetic material Fe-5Co-7B-13.5Nd-0.5U-1.5Dy-0.5Ti-0.1Sc-xGa is produced using the following method. In vacuum induction furnace under argon atmosphere and under the pressure of 300 mm Hg a melt is produced which comprises the same components as the magnetic material described in Table 1 (49,66-71). An ingot is produced out of the melt as described above; then the ingot is grinded up to particle sizes of 3 µm. Then the grinded particles are placed into the magnetic field having the intensity of 10 kOe (796 kA/m) and after that the powder is compacted applying the force of 0.8 t/cm². Then the compacted billet is sintered at 1000-1100°C during 2 hours and after that a thermal treatment of the sintered billet is performed at temperatures ranges of 490-920°C. The values for the magnetic properties of the said material and those for specific power inputs are provided in Table 1. The dependency between Ga content and coercive force iHc values is illustrated by Fig.4. The dependency pattern between iHc values and Ga content is the same as the dependency pattern between coercive force and U and Ga contents variations. The sharp increase in coercive force iHc values up to the value of 23.2 kOe (1846.7 kA/m) at x=0.03-1.0 at.% Ga is related to the intensification of anisotropy field of the basic phase when partial substitution of ferrum with gallium occurs. Besides gallium contributes to better magnetic insulation of the grains of the basic phase while sintering because it improves wetting of the grains of basic phase Nd₂Fe₁₄B with the liquid phase. The sharp drop in coercive force iHc at x>4 at.% Ga is attributed to a number of reasons. First, as a result of ferrum substitution with gallium (Ga) Curie temperature (Tc) in the basic phase begins to decrease sharply and that means that anisotropy constant decreases, too. Second, due to the fact that gallium is a non-magnetic material, the exchange interaction between ferrum sub-lattices and rare-earth elements decreases. INDUSTRIAL APPLICABILITY. The present invention may be successfully used in electrical engineering and in electronics. The magnetic material according to the invention requires specific power inputs of about 0.71-0.9, it has residual inductions of Br = 10.5-12.5 kG (1.05-1.25 T), coercive force iHc = 14-25.1 kOe (114.4-1997.96 kA/m), energy product (BH)max = 29.5-36.0 MGOe (234.8-286.6 kJ/m³) The material retains its operational properties at temperatures of up to 180-250°C.

Claims: A magnetic material comprising Fe-B-Co-R wherein R is the sum of R₁ and R₂ in which R₁ is at least one rare-earth elements selected from a group consisting of neodymium (Nd) and praseodymium (Pr), and R₂ is at least one rare-earth element selected from a group consisting of dysprosium (Dy) and terbium (Tb), and additive M being the sum of M₁ and M₂ in which M₁ is at least one element selected from a group consisting of aluminium (Al), niobium (Nb), chromium (Cr), and M₂ is at least one element selected from a group consisting of titanium (Ti), hafnium (Hf), zirconium (Zr), vanadium (V), tantalum (Ta), characterized in that the said material additionally comprises uranium (U), with the following components ratio (at.%): at least one rare-earth element selected from a group consisting of neodymium and proseodynium 12.0-17.0 at least one rare-earth element selected from a group consisting of dysprosium and terbium 0.1-5.0 at least one element selected from a group consisting of aluminium, niobium, chromium 0.5-4.0 at least one element selected from a group consisting of titanium, hafnium, zirconium, vanadium, tantalum 0.1-1.5 cobalt 2.0-6.0 boron 6.5-8.5 uranium 0.05-1.5 ferrum the balance Magnetic material according to claim 1 characterized in that uranium has the following isotope content (at.%): 238 U 99.7-99.9999 235 U 0.0001-0.3 Magnetic material for permanent magnets according to claim 1 characterized in that additive M₁ additionally comprises gallium (Ga). Magnetic material according to claim 1 or claim 3 characterized in that additive M₂ additionally comprises scandium (Sc).

Inventors: BUINOVSKY ALEXANDR SERGEEVICH, IVANOV SERGEI IGOREVICH, KACHANOV EVGENY BORISOVICH, KHASKIN JURY VIKTOROVICH, KONDAKOV VLADIMIR MIKHAILOVICH, ORLOV VLADISLAV KONSTANTINOVIC, PETRAKOV ALEXANDR FEDOROVICH, PISKORSKY VADIM PETROVIH, SAVICH ALEXANDR NIKOLAEVICH, SHALIN RADY EVGENIEVICH, SHINGAREV EDUARD NIKOLAEVICH, VEVJURKO ALEXANDR ILIICH, BUINOVSKY, ALEXANDR SERGEEVICH, IVANOV, SERGEI IGOREVICH, KACHANOV, EVGENY BORISOVICH, KHASKIN, JURY VIKTOROVICH, KONDAKOV, VLADIMIR MIKHAILOVICH, ORLOV, VLADISLAV KONSTANTINOVICH, PETRAKOV, ALEXANDR FEDOROVICH, PISKORSKY, VADIM PETROVIH, SAVICH, ALEXANDR NIKOLAEVICH, SHALIN, RADY EVGENIEVICH, SHINGAREV, EDUARD NIKOLAEVICH, VEVJURKO, ALEXANDR ILIICH
Applicants: AURA SYSTEMS INC, AURA SYSTEMS, INC.
Application year: 1991
Main classification: H01F1
IPC codes: H01F1, C22C38