Ferrites are magnetic materials widely distributed and applied in contemporary physics and engineering. In radioelectronics, the most applicable ferrites are spinel ferrite, iron garnet, orthoferrite, and hexaferrite. The main properties and physical parameters of these materials have been measured for the bulk single-crystals. Among the ferrites mentioned the most remarkable by several physical properties is ytrium iron garnet (YIG) with the formula Y3Fe5012. Due to the fact that YIG structure contains trivalent ions of the same sort, which do not possess orbital angular momentum, YIG is characterized by the narrowest possible ferromagnetic linewidth 2AH = 0,2-0, 5 Oe.

Among shortcomings of YIG are very small uniaxial anisotropy field HA = I-40 Oe and relatively small values of saturation magnetization 47CM = 1750 G. These properties are essential in magnetoelectronic devices of extremely high-frequency (EHF) band, since advance to short-wave band requires an increase in internal magnetic field and saturation magnetization, along. with a small value of FMR linewidth. Both spinel ferrite and hexaferrite surpass YIG in HA and 47iM values, but FMR linewidth of these ferrites is 10-100 times more than of YIG.

It is known that to increase HA values, YIG thin films are compressed or stretched mechanically, grown under special conditions, or diluted with other ions. All these treatments increase 2AH values, i. e. degrading resonance properties of the films.. For example, to create materials of higher saturation magnetization values comparing to YIG, Fe ions in octahedral crystallographic sites are partially substituted with diamagnetic ions, for instance Suc3+, Ge4+, Si4+. As a result, YIG saturation magnetization value 47cM ranges up to 2000 G approaching

corresponding values of spinel ferrite and hexaferrite (2000-5000 G), but FMR linewidth increases significantly.

Other solutions apply La ions and Pb ions. As a result of for example Pb introduction, anisotropy field value HA increases, but FMR linewidth value 2AH increases as well. Since the lattice structure of ferrogarnet is highly immune to isomorphic substitutions, yttrium ions of ferrogarnet structure can be substituted with combinations of rare-earth ions, the same as Fe ions can be substituted with various metal ions.

Magnetic properties of the substituted ferrogarnets vary over a wide range being dependent on chemical composition. However, all substitutions diminish microwave and resonance properties of ferrogarnets, i. e. increase FMR linewidth and dissipation ratios.

This review of what is known in the state of the art shows that the relevant problem of YIG for microwave applications is still to fabricate a material empowered by higher values of anisotropy field HA and saturation magnetization 4cM, also preserving narrow FMR linewidth close to 2AH = 0, 2-0 ; 5 Oe. All known techniques based on Fe ion substitution in sublattices of ferrogarnet result in decline of the material's frequency response.

The present invention solves this problem. According to the invention is provided a method for producing iron garnet based ferromagnetic material, having the general formula (I) {Re3-x-yFex3+,Ay}[Fe23+](Fe3+z3+Bz)O12 (I) wherein Re is one or more selected from the group of elements comprising La3+, Pr3+, Nd3+, Sm3+, Eu3+, Gd3+, Tb3+, Dy3+, Ho3+,Er3+, Tm3+, Yb3+, Y3+, Lu3+, wherein A is Bi3+, Sr2+, Ca2+ and wherein B is Ga3+, Al3+, Si4+ Ge4+ V5+ Sc3+ In3+ C 2+ wherein 0< x < 1, 5 wherein y is zero or 1 wherein 0< z < 3 and if Re is two or more elements, than Re3-x-y means that the sum of these elements constituting Re is present in the proportion 3-x-y. comprising the steps of :

i) forming a solution-melt comprising a mixture of polycrystalline ferrogarnets having the general formula (II) {Re3 Y, AY} [Fe2] (Fe3 ZBZ) O12 (II) and orthoferrite having the general formula (III) ReFeO3 (III) wherein Re, A, B, y and z are as described above; ii) homogenization of the mixture at sufficient temperature and period of time; and iii) supercooling of the mixture material to growth temperature such that orthoferrite is implanted in the ferrogarnet.

In a preferred embodiment the ferromagnetic material according to the invention is produced in a similar manner to that of yttrium iron garnet (YIG), that is in the form of bulk single- crystals as well as epitaxial films, resulting in better EHF properties, and higher adjustable values of anistropy field and saturation magnetization due to Fe3+ ions substitution only. The method according to the invention uses a solution-melt, wherein a mixture is made from polycrystalline ferrogarnets and orthoferite in acceptable proportions between them. Growing the iron garnet based ferromagnetic material from solution-melt leads to the joint crystallization of garnet and ferrous orthoferite complexes. Implantation of orthoferite complexes into garnet structure results in partial substitution of Re for Fe3+, and consequently emergence of additional components of uniaxial anistropy and higher magnetization.

Producing bulk crystals of the ferromagnetic material, as well as epitaxial films is preferably based upon crystallization from one and the same solution-melt using flux PbO-B203 or PbO-Bi203 and a mixture of a special content. Preferably the mixture includes iron oxide Fe203, polycrystalline ferrogarnet, and polycrystalline orthoferrite in a certain proportion. In a preferred embodiment of the general formula is x zero or is y zero, z zero and Re yttrium. In an other preferred embodiment of the invention the mixture for solution-melt comprises 1,4- 1,6 molar percents of polycrystalline ytrium iron garnet (YIG), 14,4-14, 6 molar percents polycrystalline ytrium orthoferite and 83,8-84, 2 molar percents iron oxide. In even another

preferred embodiment a mixture for solution-melt is used comprising (Y, Eu) 3 (FeGa) sol2 and YFeO3. The mixture preparation steps comprises an essential homogenization step, which is generally carried out at the temperature range from 900-1100°C, preferably from 1020- 1040°C, and for 30 to 180 minutes, preferably 60 to 120 minutes and comprises a supercooling step which is generally carried out to growth temperature of 800-1000°C, preferably 920-940°C, more preferably 860-920°C.

In a preferred embodiment of the invention the solution-melt comprises preliminary fabricated polycrystalline compounds, such as polycrystalline ferrogarnets (according to formula II) and orthoferite (according to formula III). It is known that when the temperature of the solution-melt decreases quasi-crystalline clusters are being formed from particles of crystal-forming components such as oxides, salts and metals which remained fully dissociated before decreasing the temperature. These quasi-crystalline structures do not match with the structure of the crystallized compound since they are formed randomly and uncontrolled.

Formation of these quasi-crystalline clusters is considered disadvantageous since they cause degradation of the solution-melt and lead to loss of crystal quality. To overcome this problem preliminary fabricated polycrystalline compounds are used to be grown in the solution-melt instead of the crystal forming components such as oxides, salts and metals. By using these preliminary fabricated polycrystalline compounds quasi-crystalline clusters are formed under incomplete (weak or partial) dissociation of the compounds, preserving the properties of the original structure of the fabricated polycrystalline compounds. Comparing to the clusters described earlier, these clusters are stable and they produce a positive effect on crystallization processes, such as a faster and steadier crystal growth and an improved reproduction of clusters's structure. These quasi-crystalline clusters also transfer heritable information from the fabricated polycrystalline compounds to growing monocrystal. This heritable information includes characteristic properties of original microcrystalline structure of the fabricated polycrystalline compounds, such as the relationships between chemical elements in lattice cell, interatomic distance and exchange interactions angles between metal ions.

An other aspect of the present invention is the ferromagnetic material itself and its use to manufacture bulk-single crystals and/or epitaxial films. Preferably ferromagnetic material is obtained and used that possesses magnetic metastable subsystems. These are anomalies in the regions of temperature curves, where values of basic magnetic properties stay invariable followed by abrupt increase, instead of a gradual increase or decrease (see Figure 1 and 3).

The magnetic metastable subsystem occurs in the claimed material as a result of an

implantation of an excess of iron into the ferrite structure. The magnetic metastable subsystem in the present invention differs from the metastable phase in other substances in that it coexists with a main stable magnetic phase and exhibits properties typical of liquids.

The ferromagnetic material according to the invention can for example be used in seismology, geophysics, microwave devices, computing devices, optoelectronics, data storage, magnetostatic waves devices, communications, mobile communications, magnetic storage and or recording devices, generators and detectors of gravity waves and any other radio-electronic or magneto-electronic device.

Mentioned and further features and advantages of the present invention will be appreciated on the basis of the following drawings and examples. These examples are given for illustration purposes and are not intended to limit the scope of the invention.

Example 1 Polycrystalline YIG 1 g of weight, 2,5 g of polycrystalline yttrium orthoferrite YFeO3, and 11, 96 g of iron oxide were dissolved in 200 g of solvent PbO-B203. The solution-melt was homogenized at 1020-1040 C for 1-2 hours along with intensive agitation simultaneously.

Then solution-melt was shifted to supercooled state. After that, with the aim to produce thin films by LPE method, on gadolinium gallium garnet substrates (GGG), oriented in the (111) plane.

Epitaxially grown at temperature range 940 C-920 C, with rotating substrate in solution- melt, were single-crystal ferrogarnet films of various thickness (4-1001lm). Out of the solution-melt at ultimate low temperature of 920 C by spontaneous crystallization were also grown bulk single crystals of ferrogarnet structure having a formula of Y3 xFes+xOs2 X-ray diffraction analysis, as well as chemical analysis and other methods indicated that all fabricated ferrites were single-phased, had garnet structure and its iron content was higher than in YIG.

Table 1. displays chemical composition of the ferrite grown out of solution-melt at temperature range 940 C-920 C. As a standard was used YIG film grown by conventional technology from a custom solution-melt, which chemical compound appeared to be close to theoretical one having the formula of Y3+-36% ; Fie3+-3 8% ; 02--24%.

Table 1. Growth Chemical composition of the claimed ferrite temperature Degrees Y3+ Y3+ Fe3+ Fe3+ Celsius, By Formula By Formula by Formula ~ 1 C weight % Units weight % Units weight % Units 2% 1, 5% 940 34 2, 9 39 5, 1 26 12 935 31 2, 6 42 5, 4 27 12 925 26 2, 0 47 6, 0 27 12 920 20 1,5 52 6,5 28 12

X-ray analysis also indicated that a lattice parameter of the claimed ferrite as compared to YIG (a = 12,376 A) tend towards scaling-down when increasing iron content. Thus, if x = 0,5 then a = 12, 373 A, and if x = 1,5 then a = 12, 371 A.

Table 2. compares magnetic properties of standard YIG and the claimed ferrite.

Table 2. Material Magnetic properties 47tu, G HA, Oe 2#H, Oe γ 10-7, s/Oe T°N, C Y3Fe5Ol2 1750 0-60 0, 2-0, 5 1, 76 286 Y3-xFe5+xO12 1750-60-1500 0,2-0, 5 1, 76 286-270 2000 An increase of x value leads to increase of an uniaxial anisotropy field HA and saturation magnetization 4rtM reaching HA=1500 Oe and zum = 2000 G at x = 1,5. At that, slight increase in gyromagnetic ratio is also registered. The most important factor is conservation of

ferromagnetic resonance (FMR) linewidth 2AH, whereof the Newel temperature TN falls inconsiderably.

Results of a magneto-optic analysis with use of a polarizing microscope has shown that single-crystal layers of the claimed ferrite have a stable strip domain structure characterized by a very small coercive field Hc less then 0,1 Oc and a high contrast in a polarized light. The lattice constant of the domain structure is weakly dependent on the film thickness varying from 1,5 to 10 um at variations of the film thickness from 4 to 20 µm. If film thickness is more than 20 urn then the domain structure type changes. The structure of custom domain walls changes into the structure of spiroid walls.

Described ferromagnetic material exibits metastable magnetic phase observed within 400- 430K temperature range. Figure 1 compares temperature dependency of saturation magnetisation of films having the formula of Y3-xFe5+xO12 and standard YIG film in different magnetic fields H which are parallel to film plane. As seen on Figure 3, stepwise anomalies of temperature dependency of saturation magnetisation are observed only in film having the formula Y3_xFes+X Oi2. These anomalies are the action of magnetic metastable subsystem which is present in film having the formula Yg-xFes+xOn.

Example 2 Polycrystalline garnet 1 g of weight having the formula Y2. 6Euo. 4Fe3. 9Ga1.1O12, 2,5 g of poycrystalline yttrium orthoferrite YFeO3, and 11, 96 g of iron oxide were dissolved in 200 g of solvent PbO-B203. Epitaxial films were grown on GGG (11 l) substrates by LPE method, as well as single crystals by spontaneous crystallization.

X-ray diffraction analysis and chemical analysis proved that obtained films and crystals have the structure of a garnet of formula {Y3+, Eu3-x3+Fex3+}[Fe23+](Fe3-x3+Gaz3+)O12, where 0<xl.

Table 3. displays magnetic properties of obtained films comparing to properties of ordinary ferrogarnet films having the similar composition.

Table 3. Magnetic properties Material 47CM HA, Hc, 2#H αRDB αFMR γ 10- , G Oe Oe, Oe 7 m (SOe) OeS-1 {Y3+,Eu3- 320 800 0,1 50 0,02 0,008 1,58 160 x3+Fex3+}[Fe23+](Fe3- z3+Gaz3+)O12 (Y, Eu) 3 (Fe, Ga) 5O12 180 1800 10 300 0, 4 0, 02 1,27 12 Where aRDB-dissipation ratio, determined by domain walls resonance method.

αFMR- dissipation ratio, determined by FMR method.

He-coercive field of domain walls

p-mobility of domain walls Table 3. displays that FMR linewidth 2AH of the substituted ferrite is six times less, coercive field and dissipation ratios 100 times less, and mobility of domain walls is 10 times higher than those observed in films of ordinary ferrogarnet.

Figure 2 represents relationship between imaginary part of magnetic susceptibility'Y'and its frequency"v"for new ferrite and ordinary one.

1. Invention 2. Pnor art As seen on Figure 2 the resonance curve of the new ferrite is located in high frequency region having higher peak value and smaller width as compared with the ordinary ferrogarnet. Thus experimental findings prove that microwave and resonance properties of new ferrite exceed significantly those of common ferrogarnets.

Figure 3 Temperature dependency of saturation magnetisation of crystals of new ferromagnetic material having the formula of {Y3+, Eu3-x3+Fex3+}[Fe23+](Fe3-z3+Gaz3+)O12.

Such stepwise magnetisation anomalies within 20 - 100K temperature range are indicative of the fact that the crystals contain magnetic metastable subsystem.

Example 3 Polycrystalline garnet 1 g of weight having the formula Eu3Fe5012, 2,5 g of europium orthoferrite EuFeO3, and 11,96 g of iron oxide Fe203 were dissolved in 200 g of solvent PbO-

B203. Films were grown from the solution-melt on GGG and NdGG (l 1 l) substrates. Single crystals were produced by spontaneous crystallization. X-ray diffraction analysis and chemical analysis displayed that obtained films and crystals have the structure of garnet having the formula {Eu3-x3+Fex3+}[Fe23+](Fe33+)O12, where 0<x<1.

Saturation magnetization 47iM of the ferrite having the formula {Eu3 <BR> <BR> <BR> x3+Fex3+}[Fe23+](Fe33+)O12 equals to 1350G, which is 200G more than saturation<BR> magnetization value of the ordinary ferrogarnet having the formula Eu3Fe5Ol2. One of the unique properties of new ferrite is anisotropy of coercive field Hc < 0,01 Oe. At present time none of the known ferrites possess so small Hc value.