JP6070454B2 - Ferrite compound - Google Patents

Description

  The present invention relates to a ferrite compound used for a ferrite sintered magnet or the like.

Ferrite sintered magnets are used in various applications such as various motors, generators, and speakers. As typical ferrite sintered magnets, Sr ferrite (SrFe ₁₂ O ₁₉ ) and Ba ferrite (BaFe ₁₂ O ₁₉ ) having a hexagonal M-type magnetoplumbite structure are known. These sintered ferrite magnets are manufactured at a relatively low cost by powder metallurgy using iron oxide and strontium (Sr) or barium (Ba) carbonate as raw materials.

In recent years, due to environmental considerations and the like, there has been a demand for higher performance of sintered ferrite magnets for the purpose of reducing the size, weight, and efficiency of automotive electrical parts, electrical equipment parts, and the like. In particular, motors used in automotive electrical components maintain high residual magnetic flux density B _r (hereinafter simply referred to as “B _r ”), and do not demagnetize due to strong demagnetizing fields when thinned. There is a demand for a ferrite sintered magnet having a magnetic force H _cJ (hereinafter simply referred to as “H _cJ ”) and a high squareness ratio H _k / H _cJ (hereinafter simply referred to as “H _k / H _cJ ”). Here, H _k is a position where J becomes a constant ratio with respect to the value of J _r (residual magnetization) in the second quadrant of the J (magnetization magnitude) −H (magnetic field strength) curve. Is the value of H (hereinafter the same). The 0.90 J _r to 0.95J _r is used as the value of a certain percentage.

Order to improve the magnetic properties of the sintered ferrite magnet was replaced with the rare earth element La, etc. Some of the Sr in the above Sr ferrite, by substituting a part of Fe with Co, the H _cJ and B _r JP-A-10-149910 (Patent Document 1) and JP-A-11-154604 (Patent Document 2) have been proposed as methods for improvement.

  Sr ferrite (hereinafter referred to as “SrLaCo ferrite”) in which a part of Sr described in Patent Document 1 and Patent Document 2 is substituted with a rare earth element such as La and a part of Fe is replaced with Co or the like Because of its superiority, it has been widely used in various applications in place of conventional Sr ferrite and Ba ferrite, but further improvement in magnet properties is also desired.

Japanese Patent Laid-Open No. 2001-223104 (Patent Document 3) describes a _method of increasing the heating rate in the temperature range from 900 ° C. to the maximum temperature in the heating process of the firing process in order to improve the _HcJ of the SrLaCo ferrite. Proposed to be 5 ° C / min. In Examples of Patent Document 3, in the composition of Sr _1-x La _x (Fe _12-y Co _y ) _z O ₁₉ , H _cJ is improved by increasing the temperature rising rate to 1 to 5 ° C./min. Have been described. In Patent Document 3, the temperature lowering rate is not particularly limited, and is usually described as 1 to 20 ° C./min. In the examples, the temperature lowering rate is 5 ° C./min.

On the other hand, Ca ferrite is also known as a ferrite sintered magnet together with the Sr ferrite and Ba ferrite. It is known that Ca ferrite has a stable structure represented by a composition formula of CaO—Fe ₂ O ₃ or CaO—2Fe ₂ O ₃ and forms hexagonal ferrite by adding La. However, the obtained magnet characteristics are similar to those of the conventional Ba ferrite and are not sufficiently high.

Patent No. 3181559 (Patent Document 4), increase of B _r and H _cJ of the Ca ferrite, and for improving the temperature characteristics of the H _cJ, by replacing part of Ca with rare earth elements such as La, the Fe partially substituted with Co, etc., 20 kOe or more anisotropic magnetic field H _a (hereinafter, simply referred to as "H _a") discloses a Ca ferrite having (hereinafter referred to as "CaLaCo ferrite"), the H _a is The value is 10% or more higher than that of Sr ferrite.

However, CaLaCo ferrite of Patent Document 4, although having a H _A above the SrLaCo ferrite, B _r and H _cJ are comparable to SrLaCo ferrite, while the H _k / H _cJ is very poor, and high H _cJ The high H _k / H _cJ cannot be satisfied, and it has not yet been applied to various uses such as motors.

  Various proposals have been made to improve the magnetic properties of CaLaCo ferrite. For example, Japanese Patent Laid-Open No. 2006-104050 (Patent Document 5) proposes a CaLaCo ferrite in which the atomic ratio and molar ratio n of each constituent element are optimized and La and Co are contained at a specific ratio. International Publication No. 2007/060757 (Patent Document 6) proposes CaLaCo ferrite in which a part of Ca is replaced with La and Ba. International Publication No. 2007/077811 (Patent Document 7) We have proposed CaLaCo ferrite partially substituted with La and Sr.

  However, although the CaLaCo ferrites described in Patent Documents 5 to 7 have improved magnetic properties compared to the CaLaCo ferrite proposed in Patent Document 4, they are sufficient for the demand for higher performance that has become stronger in recent years. However, there is a demand for further improvement in magnet characteristics.

International Publication No. 2011/001831 (Patent Document 8) is a CaLaCo ferrite proposed in Patent Documents 5 to 7, and more than 1% by mass and less than 1.8% by mass of SiO ₂ and CaO as a sintering aid in by adding CaCO ₃ 1-2% by weight calcined body, while preventing a decrease in B _r and H _k / H _cJ as much as possible, to propose a CaLaCo ferrite specifically improves H _cJ Yes.

CaLaCo ferrite containing a relatively large amount of sintering aid proposed in Patent Document 8 improves H _cJ specifically, but most of them _exceed H _kJ of 360 kA / m (about 4.5 kOe) H _k / H _cJ has been reduced to less than 85%, and it cannot be said that the ferrite sintered magnets, which have been requested in recent years, are sufficiently thin.

Japanese Patent Laid-Open No. 10-149910 Japanese Patent Laid-Open No. 11-154604 JP 2001-223104 A Japanese Patent No. 3181559 JP 2006-104050 A International Publication No. 2007/060757 International Publication No. 2007/077811 International Publication No. 2011/001831

Accordingly, an object of the present invention, in the CaLaCo ferrite, high and B _r and a high H _k / H _cJ while H _cJ was maintained with improved useful ferrite compound as a compound of the ferrite sintered magnet that can respond to thinning Is to provide.

As a result of diligent research in view of the above object, the inventors have found that in the M-type magnetoplumbite structure, which is the crystal structure of CaLaCo ferrite, the amount of Co present at the 4f ₁ and 4f ₂ sites, which are the down spin sites, is increased. We found a ferrite compound that is larger than the amount of Co present at the 2a, 4e and 12k sites. Then, it found that ferrite sintered magnet that the crystal phase (ferrite phase) the main phase composed of the ferrite compound, has a high H _cJ with a high B _r and a high H _k / H _cJ, completed the present invention did.

That is, the ferrite compound of the present invention is a ferrite compound having a hexagonal M-type magnetoplumbite structure and containing Ca, La, Fe and Co as essential components,
The total amount of Co present at the 4f ₁ and 4f ₂ sites that are the down spin sites in the unit cell of the M-type magnetoplumbite structure is the total amount of Co present at the 2a, 4e, and 12k sites that are the up spin sites. It is characterized by more.

The ferrite compound is an element of Ca, La, Ba, and / or Sr, Fe, and Co that exists at 2a, 4e, and 12k sites that are upspin sites in the unit cell of the M-type magnetoplumbite structure of hexagonal crystal. The composition formula showing the atomic ratio of the metal element of Co ^UP which is Co ^UP and Co ^DOWN which is Co present in the 4f ₁ and 4f ₂ sites which are down spin sites: Ca _1-xy La _x A _y Fe _2n-vw Co ^UP _{In v} Co ^DOWN _w , 1-xy, x, y, v, w, and n indicating a molar ratio are
0.23 ≦ 1-xy ≦ 0.75,
0.2 ≦ x ≦ 0.65,
0 ≦ y ≦ 0.4,
0.2 ≦ v + w <0.65,
w> v,
3 <n <6 and
0 ≦ y / (1-x) <0.56
Is preferably satisfied.

  The ferrite compound is obtained by pulverizing a calcined body obtained by calcining raw material powder, a temperature rising rate in a temperature range of 1100 ° C. to firing temperature is 1 to 4 ° C./min, and a temperature range of firing temperature to 1100 ° C. It is produced by firing under the condition that the temperature lowering rate at 6 ° C./min or more.

Since the ferrite compound according to the present invention has high saturation magnetization and high _HA , it can exhibit high performance when used in a sintered magnet, a bonded magnet, a magnetic recording medium or the like. Especially when used as the main compound constituting the ferrite sintered magnet, with improved H _cJ while maintaining high B _r and a high H _k / H _cJ, sintered ferrite magnets to accommodate thinning are obtained, which By using a ferrite sintered magnet, it is possible to provide various electric motor parts such as various motors, generators, and speakers, electric equipment parts, and the like that are reduced in size, weight, and efficiency.

It is a graph showing the relationship between the heating rate and B _r in the firing step of the sintered ferrite magnet of the sample No.1~8 of Example 1 (closed circles) and H _cJ (black triangles). 6 is a graph showing the relationship between the temperature increase rate and H _k / H _cJ in the firing step of the ferrite sintered magnets of Sample Nos. 1 to 8 in Example 1. FIG. It is a graph showing the relationship between the cooling rate and the B _r and H _cJ in the firing step of the sintered ferrite magnet of the sample No.9~13 of Example 1 (closed circles) and sample Nanba14～18 (black triangles). 4 is a graph showing the relationship between the temperature drop rate and H _k / H _cJ in the firing process of ferrite sintered magnets of Sample Nos. 9 to 13 (black circles) and Sample Nos. 14 to 18 (black triangles) of Example 1. FIG. It is a graph showing the relationship between the heating rate and B _r in the firing step of the sintered ferrite magnet of the sample No.19~26 of Example 1 (closed circles) and H _cJ (black triangles). 4 is a graph showing the relationship between the temperature increase rate and H _k / H _cJ in the firing step of the ferrite sintered magnets of Sample Nos. 19 to 26 in Example 1. FIG.

[1] Ferrite compound The ferrite compound of the present invention is a ferrite compound having a hexagonal M-type magnetoplumbite structure and containing Ca, La, Fe and Co as essential components, the M-type magnetoplumbite The total amount of Co present in the 4f ₁ and 4f ₂ sites that are the down spin sites in the unit cell of the structure is larger than the total amount of Co present in the 2a, 4e, and 12k sites that are the up spin sites. And

  The ferrite compound of the present invention has a hexagonal M-type magnetoplumbite structure. “Having hexagonal M-type magnetoplumbite structure” means that a ferrite sintered magnet or ferrite powder containing a crystal phase (ferrite phase) composed of the ferrite compound of the present invention is used in a general X-ray diffraction method. It means that an X-ray diffraction pattern of a hexagonal M-type magnetoplumbite structure is mainly observed when measured under conditions.

M-type magnetoplumbite structure hexagonal is a complex crystal structure, when the Sr ferrite, 2d that Sr occupies, 2a that Fe occupies, 4e, 4f _1, 4f ₂ and 12k, and O (oxygen) It has 11 different sites, 4e, 4f, 6h, 12k ₁ and 12k _{2 to} occupy. The number of chemical formula units per unit cell is 2, that is, it contains two chemical formula atoms per unit cell. For example, in the case of Sr ferrite (chemical formula is SrFe ₁₂ O ₁₉ ), 2 Sr, 24 Fe, and 38 O are contained per unit cell.

Sr ferrite is ferrimagnetic, and the magnetic moment of the magnetic element occupying the 2a, 4e and 12k sites and the direction of the magnetic moment of the magnetic element occupying the 4f ₁ and 4f ₂ sites are antiparallel, and the difference between the magnetic moments Becomes the magnetic moment of the entire Sr ferrite crystal. The total number of 2a, 4e and 12k sites (up spin sites) per unit cell is 16, and the total of 4f ₁ and 4f ₂ sites (down spin sites) is 8, so the magnetic moment that occupies each site is large. If the lengths are the same, the magnetic moment of 8 upspins becomes the magnetic moment per unit cell. For example magnetic element if the Sr ferrite is a trivalent Fe ions having a magnetic moment of 5 [mu] _B, the magnetic moment per unit cell becomes _{5μ B × (16-8) = 40μ} B.

In the SrLaCo ferrite described above, La is present in part of the 2d site (Sr site), Co is present in part of the 2a, 4e, 4f ₁ , 4f ₂ and 12k sites (Fe site), and upspin. It is known that the amount of Co occupying a site (present at an upspin site) is greater than the amount of Co occupying a downspin site (present at a downspin site) (eg, J. Ceram. Soc. Jpn, 119, 285-290 (2011)). Also, in the CaLaCo ferrite described above, like SrLaCo ferrite, Ca and La are present in part of the 2d site, and Co is present in part of the 2a, 4e, 4f ₁ , 4f ₂ and 12k sites. The composition of the conventional ferrite sintered magnet is designed based on such a concept. These are apparent from the composition formulas described in Patent Documents 5 to 7 described above.

In CaLaCo ferrite, Sr (ion radius of Sr ²⁺ in 144 coordination: 144 pm) and Ba (ion radius of Ba ²⁺ in 161 coordination: 161 pm) are occupied by conventional Sr ferrite and Ba ferrite. In some sites, Ca (12-coordinate Ca ²⁺ ion radius: 134 pm, 6-coordinate ion radius: 100 pm) and La (12-coordinate La ³⁺ ion radius: 136 pm) is replaced, Fe (the Fe ³⁺ in the six-coordinate ion radius: 64.5 pm) of Co ²⁺ in Co (6 coordinated to some sites occupied ionic radius: 74.5 pm) is substituted Therefore, it is considered that a large strain is generated in the crystal structure of the M-type magnetoplumbite compared to the unsubstituted Sr ferrite and Ba ferrite. In addition, in CaLaCo ferrite, the amount of substitution of trivalent La ions for divalent Ca ions and the amount of substitution of divalent Co ions for trivalent Fe ions are significantly different, resulting in an imbalance in the charge balance of the entire crystal. Therefore, it is necessary to maintain the charge balance of the entire crystal by some method. For this reason, the crystal structure of CaLaCo ferrite is more unstable than Sr ferrite and SrLaCo ferrite.

Co in the ferrite compound of the present invention is a divalent Co ion, magnetic moment expected from Hund rule is 3.mu. _B. This value is smaller than 5 [mu] _B is the magnetic moment of the trivalent Fe ions, the magnetic moment of the sites occupied by the Co decreases 2.mu. _B. For this reason, when the amount of Co occupying up-spin sites and down-spin sites in the M-type magnetoplumbite structure is equal, the magnetic moment per unit cell does not change, but occupies up-spin sites and down-spin sites. When the amount of Co is different, the magnetic moment per unit cell changes. That is, if the amount of Co that occupies the down spin site (exists at the down spin site) is larger, the magnetic moment per unit cell increases, and the Co moment that occupies the up spin site (exists at the up spin site). The greater the amount, the lower the magnetic moment per unit cell.

In the ferrite compound of the present invention, the total amount of Co present in the 4f ₁ and 4f ₂ sites that are the down spin sites in the unit cell of the M-type magnetoplumbite structure is the 2s, 4e, and 12k sites that are the up spin sites. More than the total amount of Co present. That is, the amount of Co occupying only 8 down spin sites per unit cell is larger than the amount of Co occupying 16 up spin sites per unit cell. Therefore, it is considered that the magnetic moment per unit cell is improved. Therefore, when the ferrite compound according to the present invention has high saturation magnetization and high _HA and is used as a main compound constituting a ferrite sintered magnet, high _Br. It is considered that H _cJ can be improved while maintaining high H _k / H _cJ . In addition, the amount of Co present at the 4f ₁ and 4f ₂ sites that are the down spin sites is larger than the amount of Co present at the 2a, 4e, and 12k sites that are the up spin sites. There is a possibility that the crystal structure can be further stabilized.

The abundance ratio of Co present at 2a, 4e, 4f ₁ , 4f ₂ and 12k sites in the unit cell of M-type magnetoplumbite structure should be analyzed by X-ray diffraction and neutron diffraction diffraction pattern profile fitting methods. Can do. X-ray diffraction can be performed using a synchrotron radiation facility such as SPring-8 or a commercially available powder X-ray diffractometer, and neutron diffraction can be performed using a facility such as JRR-3 of the Japan Atomic Energy Agency. Can do.

  As a profile fitting method used in the analysis of a diffraction pattern by X-ray diffraction or neutron diffraction, for example, a Rietveld analysis method can be cited. Rietveld analysis is performed by fitting a diffraction pattern calculated from the crystal structure of a substance expected to be contained in a sample to a diffraction pattern obtained by X-ray diffraction, etc. This is a method of analyzing coordinates, types of atoms occupying each site, and occupancy rates. Lead belt analysis software includes commercially available software such as TOPAS (manufactured by Bruker AXS), and RIETAN-FP (F. Izumi and K. Momma, “Three-dimensional visualization in powder diffraction,” Solid State Phenom., 130, 15-20 (2007).). As the crystal structure of the constituent phase, a known structure may be used as the initial structure.

  In addition, if the analysis results with sufficient accuracy and accuracy cannot be obtained only by the profile fitting method of the diffraction pattern by X-ray diffraction or neutron diffraction, the wide-area X-ray absorption fine structure (EXAFS) analysis by X-ray absorption spectroscopy is complemented. By using this method, the accuracy and accuracy of the analysis result can be increased. X-ray absorption spectroscopy measurements can be made, for example, at synchrotron radiation facilities such as SPring-8 and Photon Factory at the High Energy Accelerator Laboratory. Examples of EXAFS analysis software include IFEFFIT (JJ Rehr and RC Albers, Phys. Rev. B, 41, 8139-8149 (1990)), JJ Rehr, SI Zabinsky and RC Albers, Phys. Rev. Lett., 69, 3397. -3400 (1992)., JJ Rehr, J. Mustre de Leon, SI Zabinsky and RC Albers, J. Am. Chem. Soc., 113, 5135-5140 (1991)., J. Mustre de Leon, JJ Rehr, SI Zabinsky and RC Albers, Phys. Rev. B, 44, 4146-4156 (1991).).

The present invention relates to an improvement of CaLaCo ferrite, and the ferrite compound of the present invention contains Ca, La, Fe and Co as essential components. Preferably, it is Ca, La, Ba and / or Sr, element A, Fe, hexagonal M-type magnetoplumbite structure, and Co present at the 2a, 4e and 12k sites which are upspin sites in the unit cell. Co ^UP and the composition formula showing the atomic ratio of the metal element of Co ^DOWN which is Co present in the 4f ₁ and 4f ₂ sites which are the down spin sites: Ca _1-xy La _x A _y Fe _2n-vw Co ^UP _v Co ^{In DOWN} _w , the 1-xy, x, y, v, w, and n indicating the molar ratio are
0.23 ≦ 1-xy ≦ 0.75,
0.2 ≦ x ≦ 0.65,
0 ≦ y ≦ 0.4,
0.2 ≦ v + w <0.65,
w> v,
3 <n <6 and
0 ≦ y / (1-x) <0.56,
Is satisfied.

The above composition formula is shown by the atomic ratio of the metal element, but the composition containing oxygen (O) is the composition formula: Ca _{1 -xy} La _x A _y Fe _{2 n -vw} Co ^UP _v Co ^DOWN _w O _α (however, , 1-xy, x, y, v, w and α and n indicating the molar ratio are
0.23 ≦ 1-xy ≦ 0.75,
0.2 ≦ x ≦ 0.65,
0 ≦ y ≦ 0.4,
0.2 ≦ v + w <0.65,
w> v,
3 <n <6 and
0 ≦ y / (1-x) <0.56,
When La and Fe are trivalent, Ca, A element and Co are divalent, and when x = v + w and n = 6, the stoichiometric composition ratio is α = 19. is there. ).

  In the composition of the ferrite compound containing oxygen (O), the atomic ratio of oxygen varies depending on the valence of Fe and Co, the n value, and the like. In the ferrite compound, the ratio of oxygen to the metal element changes due to oxygen vacancies when baked in a reducing atmosphere, changes in the valence of Fe in the ferrite compound, changes in the valence of Co, and the like. Therefore, the actual atomic ratio α of oxygen may deviate from 19. Therefore, in the present invention, the composition is expressed by the atomic ratio of the metal element whose composition is most easily specified.

The ferrite compound of the present invention is the main component of a sintered ferrite magnet, that is, the crystal phase (ferrite phase having a hexagonal M-type magnetoplumbite structure) composed of the ferrite compound of the present invention is the main phase. it is thus possible to obtain a ferrite sintered magnet with improved H _cJ while maintaining high B _r and a high H _k / H _cJ. Hereinafter, a ferrite sintered magnet having a crystal phase composed of the ferrite compound of the present invention as a main phase (hereinafter sometimes referred to as “the present ferrite sintered magnet”) will be described.

  As described above, the main phase of the sintered ferrite magnet is a crystal phase composed of the ferrite compound of the present invention, and is a ferrite phase having a hexagonal M-type magnetoplumbite structure. In general, a magnetic material, particularly a sintered magnet, is composed of a plurality of compounds, and a compound that determines the characteristics (physical properties, magnet characteristics, etc.) of the magnetic material is defined as “main phase”. The main phase in the sintered ferrite magnet, that is, a ferrite phase having a hexagonal M-type magnetoplumbite structure also determines basic parts such as physical properties and magnet characteristics of the sintered ferrite magnet.

  In addition to the main phase, the ferrite sintered magnet further includes a first grain boundary phase existing between two main phases and a second grain boundary phase existing between three or more main phases. Contained. The first grain boundary phase existing between the two main phases is a grain boundary phase that is also referred to as a “two-grain grain boundary phase” by those skilled in the art, and is obtained when an arbitrary cross section of a ferrite sintered magnet is observed. This refers to the grain boundary phase that appears linearly at the grain boundaries of the main phase and the main phase. Further, the second grain boundary phase existing between three or more main phases is a grain boundary phase referred to as “multi-point grain boundary phase” by those skilled in the art, and an arbitrary cross section of the ferrite sintered magnet. Is a grain boundary phase that appears between three or more main phases and looks like a substantially triangular shape, a substantially polygonal shape, or an indefinite shape. Since the first grain boundary phase is very thin and difficult to observe with an X-ray diffraction pattern, it is preferably confirmed with a transmission electron microscope or the like having high resolution. In the following description, when the first grain boundary phase and the second grain boundary phase are collectively expressed, they may be simply referred to as “grain boundary phase”.

The sintered ferrite magnet has the main phase, the first grain boundary phase, and the second grain boundary phase, and preferably the second grain boundary phase is scattered in an arbitrary cross section. And the average area of the second grain boundary phase is less than 0.2 μm ² . In a more preferred embodiment, the second grain boundary phase has a structure having 900 or more in a range of 53 × 53 μm ² of an arbitrary cross section. The average area of the second grain boundary phase is obtained by binarizing the reflected electron image (BSE image) of the ferrite sintered magnet cross section by FE-SEM (field emission scanning electron microscope). It can be determined by determining the area and number of phases and dividing the total area by the number.

[2] Method for Producing Ferrite Compound The ferrite compound of the present invention can be formed through the following production steps.
Raw material powder mixing step of mixing raw material powders to obtain mixed raw material powders,
Calcining the mixed raw material powder to obtain a calcined body,
Crushing the calcined body to obtain a calcined powder;
Firing the calcined powder, and including a firing step to obtain a fired body,
In the firing step, the rate of temperature rise in the temperature range of 1100 ° C. to the firing temperature is 1 to 4 ° C./minute, and the temperature drop rate in the temperature range of the firing temperature to 1100 ° C. is 6 ° C./minute or more. In addition, when using the ferrite compound of this invention for a sintered magnet, the shaping | molding process etc. which shape | mold the said calcined body powder and obtain a molded object between the said crushing process and the said baking process are added. Each step will be described below.

(a) Raw material powder mixing step Composition formula indicating the atomic ratio of A element, Fe and Co metal elements in which the ferrite compound is Ca, La, Ba and / or Sr: Ca _1-xy La _x A _y Fe _{2n- In vw} Co _{v + w} , 1-xy, x, y, v, w, and n indicating a molar ratio are
0.23 ≦ 1-xy ≦ 0.75,
0.2 ≦ x ≦ 0.65,
0 ≦ y ≦ 0.4,
0.2 ≦ v + w <0.65,
3 <n <6 and
0 ≦ y / (1-x) <0.56,
The raw material powder is blended so as to satisfy the above. When n indicating the atomic ratio and molar ratio defined above is out of the range, the ferrite compound of the present invention cannot be obtained.

  Note that La can be partially substituted with at least one rare earth element other than La. The substitution amount is preferably 50% or less of La by molar ratio. A part of Co can be substituted with at least one selected from Zn, Ni and Mn.

Regardless of the valence, the raw material powder can use oxides, carbonates, hydroxides, nitrates, chlorides, and the like of each metal. The solution which melt | dissolved raw material powder may be sufficient. Examples of the Ca compound include Ca carbonate, oxide, chloride and the like. Examples of the La compound include oxides such as La ₂ O ₃ , hydroxides such as La (OH) ₃ , carbonates such as La ₂ (CO ₃ ) ₃ · 8H ₂ O, and the like. Examples of the element A compound include Ba and / or Sr carbonates, oxides, and chlorides. Examples of the iron compound include iron oxide, iron hydroxide, iron chloride, and mill scale. Co compounds include oxides such as CoO and Co ₃ O ₄ , and hydroxides such as CoOOH, Co (OH) ₂ , and Co ₃ O ₄ · m ₁ H ₂ O (m ₁ is a positive number). , Carbonates such as CoCO ₃ , and basic carbonates such as m ₂ CoCO ₃ · m ₃ Co (OH) ₂ · m ₄ H ₂ O (m ₂ , m ₃ and m ₄ are positive numbers) Can be mentioned.

Raw material powders other than CaCO ₃ , Fe ₂ O ₃ and La ₂ O ₃ may be added from the time of raw material mixing, or may be added after calcination. For example, (1) CaCO ₃ , Fe ₂ O ₃ , La ₂ O ₃ and Co ₃ O ₄ are blended, mixed and calcined, and then the calcined body is pulverized and fired to produce a ferrite compound. (2) Mixing CaCO ₃ , Fe ₂ O ₃ and La ₂ O ₃ , mixing and calcining, adding Co ₃ O ₄ to the calcined body, pulverizing and firing to produce a ferrite compound You can also

In order to promote the reaction during calcination, a compound containing B such as B ₂ O ₃ or H ₃ BO ₃ may be added up to about 1% by mass as necessary. H ₃ BO ₃ also has the effect of controlling the shape and size of crystal grains during firing, so it may be added after calcination (before pulverization or before firing), both before and after calcination. It may be added.

  Each prepared raw material powder is mixed and it is set as mixed raw material powder. Mixing of the raw material powders may be performed either by a wet method or a dry method. When stirring with a medium such as a steel ball, the raw material powder can be mixed more uniformly. In the case of the wet type, it is preferable to use water as the dispersion medium. For the purpose of enhancing the dispersibility of the raw material powder, a known dispersant such as ammonium polycarboxylate or calcium gluconate may be used. The mixed raw material slurry may be calcined as it is, or after dehydrating the raw material slurry, it may be calcined.

(b) Calcination process The mixed raw material powder obtained by dry mixing or wet mixing is heated using an electric furnace, gas furnace, etc., and by a solid-phase reaction, a hexagonal M-type magnetoplumbite structure The ferrite compound is formed. This process is called “calcination” and the resulting compound is called “calcination”. The ferrite compound formed by calcination is a precursor of the ferrite compound of the present invention, and at this stage, the crystal structure is not sufficiently stabilized, and the M-type magnetoplumbite structure downs the unit cell. The amount of Co present at the 4f ₁ and 4f ₂ sites that are the spin sites may not be greater than the amount of Co present at the 2a, 4e, and 12k sites that are the up spin sites. In the raw material powder mixing step, CaCO ₃ , Fe ₂ O ₃ and La ₂ O ₃ are blended, mixed and calcined, and then manufactured by a method of adding Co ₃ O ₄ to the obtained calcined body. In this case, the ferrite compound formed by calcining does not contain Co, but by adding Co ₃ O ₄ to the calcined body and passing through the steps described later, the M-type magnetoplumbite structure It is possible to obtain a ferrite compound in which the amount of Co present in the 4f ₁ and 4f ₂ sites which are the down spin sites in the unit cell is larger than the amount of Co present in the 2a, 4e and 12k sites which are the up spin sites. .

  The calcination step is preferably performed in an atmosphere having an oxygen concentration of 5% or more. When the oxygen concentration is less than 5%, abnormal grain growth, generation of a heterogeneous phase, and the like are caused. A more preferable oxygen concentration is 20% or more.

  In the calcination step, a solid phase reaction in which a ferrite compound is formed proceeds with an increase in temperature and is completed at about 1100 ° C. A calcination temperature of less than 1100 ° C. is not preferable because unreacted hematite (iron oxide) remains. On the other hand, when the calcining temperature exceeds 1450 ° C., crystal grains grow too much, and thus, it may take a long time for the grinding in the grinding process. Accordingly, the calcination temperature is preferably 1100 to 1450 ° C, more preferably 1200 to 1350 ° C. The calcination time is preferably 0.5 to 5 hours.

When H ₃ BO ₃ is added before calcination, the ferritization reaction is promoted, and therefore calcination can be performed at 1100 ° C. to 1300 ° C.

(c) Addition of sintering aid When the ferrite compound of the present invention is used in a sintered magnet, a calcined body or a calcined body is used as a sintering aid after the calcining step and before the molding step described later. It is preferable to add 0 to 1.8% by mass of SiO ₂ and 0 to 2% by mass of CaCO ₃ in terms of CaO with respect to 100% by mass of the calcined body or the calcined body powder. For example, the sintering aid may be added by, for example, adding a sintering aid to the calcined body obtained by the calcining step and then performing a grinding step, adding a sintering aid during the grinding step, or grinding. A method of adding a sintering aid to the calcined body after the process and mixing and then performing a molding process can be employed.

In the present invention, the amount of CaCO ₃ added is all expressed in terms of CaO. The addition amount of CaCO ₃ from the addition amount in terms of CaO is calculated by the formula:
(Molecular weight of CaCO ₃ × added amount in terms of CaO) / CaO molecular weight.
For example, when adding 1.5% CaCO ₃ in terms of CaO,
{(40.08 [Ca atomic weight] + 12.01 [C atomic weight] + 48.00 [O atomic weight x 3] = 100.09 [CaCO ₃ molecular weight]) x 1.5 mass% [CaO equivalent amount]} / ( 40.08 [atomic weight of Ca] +16.00 [atomic weight of O] = 56.08 [molecular weight of CaO] = 2.677 mass% [addition amount of CaCO ₃ ].

Since CaLaCo ferrite contains Ca as a main phase component, a liquid phase can be generated and sintered without adding SiO ₂ and CaCO ₃ as sintering aids. That is, the grain boundary phase is formed without adding the SiO ₂ and CaCO ₃ that mainly form the grain boundary phase in the ferrite sintered magnet. On the other hand, when SiO ₂ and CaCO ₃ are added as sintering aids, they become part of the liquid phase component during sintering and become a grain boundary phase after sintering.

In addition to the above-described SiO ₂ and CaCO ₃ , Cr ₂ O ₃ , Al ₂ O _3, etc. can be added after the calcining step and before the molding step described later. Each of these addition amounts is preferably 5% by mass or less.

(d) Grinding step The calcined body is pulverized by a vibration mill, roller mill, hammer mill, jet mill, ball mill, attritor or the like to obtain a calcined powder. The average particle size of the calcined powder is preferably about 0.4 to 0.8 μm (air permeation method). The pulverization step may be either dry pulverization or wet pulverization, but is preferably performed in combination.

  The wet pulverization is performed using water and / or a non-aqueous solvent (an organic solvent such as acetone, ethanol, xylene) as a dispersion medium. By wet pulverization, a slurry in which the dispersion medium and the calcined powder are mixed is generated. It is preferable to add a known dispersant and / or surfactant to the slurry in a solid content ratio of 0.2 to 2% by mass. After the wet pulverization, it is preferable to concentrate and knead the slurry.

The pulverized calcined powder contains ultrafine powder of less than 0.1 μm, which causes abnormal grain growth of ferrite particles generated in the firing process, dehydration deterioration in the molding process, and molding defects. It is preferable to heat-treat the pulverized calcined powder to remove the heat. The heat-treated powder is preferably pulverized again. Thus, the pulverization step comprising the first pulverization step, the step of subjecting the powder obtained by the first pulverization step to heat treatment, and the second pulverization step of pulverizing the powder subjected to the heat treatment again. When the ferrite compound of the present invention is used for a sintered magnet by adopting (hereinafter referred to as “heat treatment re-grinding step”), the H _cJ of the ferrite sintered magnet can be improved.

In the normal pulverization process, ultrafine powder of less than 0.1 μm is inevitably generated, and the presence of the ultrafine powder causes abnormal grain growth of ferrite particles in the firing process, resulting in a decrease in H _cJ , and dehydration in the molding process. It becomes worse, the molded product becomes defective, or the press cycle is lowered due to a long time for dehydration. When the powder containing the ultrafine powder obtained by the first pulverization process is heat-treated, a reaction occurs between the powder having a relatively large particle size and the ultrafine powder, and the amount of the ultrafine powder can be reduced. Then, the particle size is adjusted and necking is removed by the second pulverization step to produce a powder having a predetermined particle size. As a result, it is possible to obtain a powder with a small amount of ultrafine powder and excellent particle size distribution, and when the ferrite compound of the present invention is used for a sintered magnet by suppressing abnormal grain growth of ferrite particles in the firing process, The _HcJ of the ferrite sintered magnet can be improved and the above problems in the molding process can be solved.

_Using the effect of improving H _cJ by the heat treatment re-grinding process, even if the particle size of the powder by the second grinding process is set relatively large (for example, average particle size of 0.8 to 1.0 μm (air permeation method)), H _cJ equivalent to the case of using the powder obtained by the pulverization step (average particle size of about 0.4 to 0.8 μm (air permeation method)) is obtained. Accordingly, the time for the second pulverization step can be shortened, and further improvement of dewaterability and improvement of the press cycle can be achieved.

  As described above, according to the heat treatment re-pulverization process, although various advantages can be obtained, an increase in cost accompanying an increase in the manufacturing process cannot be avoided. However, the improvement effect obtained when the heat treatment re-pulverization step is adopted is much larger than that when the heat treatment re-pulverization step is not adopted, so that the cost increase can be offset. Therefore, in the present invention, the heat treatment re-pulverization step is a practically meaningful step.

  The first pulverization is the same as the normal pulverization described above, and is performed using a vibration mill, roller mill, hammer mill, jet mill, ball mill, attritor or the like. The average particle size of the pulverized powder is preferably about 0.4 to 0.8 μm (air permeation method). The pulverization step may be either dry pulverization or wet pulverization, but is preferably performed in combination.

  The heat treatment performed after the first pulverization step is preferably performed at 600 to 1200 ° C, more preferably 800 to 1100 ° C. The heat treatment time is not particularly limited, but is preferably 1 second to 100 hours, and more preferably about 1 to 10 hours.

  The second pulverization performed after the heat treatment step is performed using a vibration mill, a roller mill, a hammer mill, a jet mill, a ball mill, an attritor or the like, as in the first pulverization. Since almost the desired particle size has already been obtained in the first pulverization step, particle size adjustment and necking removal are mainly performed in the second pulverization step. Therefore, it is preferable to reduce the pulverization conditions by shortening the pulverization time or the like than in the first pulverization step. If pulverization is performed under the same conditions as in the first pulverization step, ultrafine powder is generated again, which is not preferable.

The average particle size of the powder after the second pulverization is about 0.4 to 0.8 μm (air permeation) as in the normal pulverization step when it is desired to obtain a higher H _cJ than the sintered ferrite magnet obtained by the normal pulverization step. If you want to take advantage of advantages such as shortening the pulverization time, further dewaterability, and improving the press cycle, 0.8 to 1.2 μm, preferably about 0.8 to 1.0 μm (air permeation method) Is preferable.

(e) Forming Step When the ferrite compound of the present invention is used for a sintered magnet, the slurry after the pulverizing step is press-molded in a magnetic field or in a non-magnetic field while removing the dispersion medium. In particular, by press molding in a magnetic field, the crystal orientation of the powder particles can be aligned (orientated), and the magnet characteristics of the ferrite sintered magnet can be dramatically improved. Further, in order to improve the orientation, 0.01% to 1% by mass of a dispersant and a lubricant may be added. Moreover, you may concentrate a slurry before shaping | molding as needed. Concentration is preferably carried out by natural sedimentation, centrifugation, filter press or the like.

(f) Firing step The calcined body powder obtained in the pulverization step or the shaped body obtained in the molding step is degreased if necessary and then fired (sintered). Thus, a fired body (sintered magnet) is obtained. In the firing step, the rate of temperature rise in the temperature range from 1100 ° C. to the firing temperature is 1 to 4 ° C./minute, and the rate of temperature drop in the temperature range from the firing temperature to 1100 ° C. is 6 ° C./minute or more. As a result, the amount of Co present in the 4f ₁ and 4f ₂ sites that are the down spin sites in the unit cell of the M-type magnetoplumbite structure is the amount of Co present in the 2a, 4e, and 12k sites that are the up spin sites. More ferrite compounds can be produced.

  It is possible to obtain the ferrite compound of the present invention even at a heating rate of less than 1 ° C / minute, for example, 0.5 ° C / minute. However, if the heating rate is too slow, the production cycle becomes longer and the production cost increases. This is not preferable. Therefore, the temperature rising rate is preferably 1 to 4 ° C./min. A more preferable rate of temperature increase is 1 to 2 ° C./min. Further, the upper limit is not particularly defined if the temperature lowering rate is 6 ° C./min or more, but in order to lower the temperature quickly, a cooling facility and a blower facility are required in the firing furnace, which may increase the production cost. Considering these points, the upper limit of the temperature lowering rate is preferably about 10 ° C./min.

  The temperature range in which the heating rate is 1 to 4 ° C./min is 1100 ° C. to the firing temperature. If the rate of temperature rise exceeds 4 ° C./min even in the temperature range of 1100 ° C. or higher, the ferrite compound of the present invention may not be obtained. In addition, if the temperature increase rate in the temperature range of 1100 degreeC-calcination temperature is 1-4 degreeC / min, the temperature increase rate in other temperature will not be specifically limited. In order to set the rate of temperature increase in the temperature range from 1100 ° C. to the firing temperature to 1 to 4 ° C./min, the temperature increase rate is set to 1 to 1 even at a temperature lower than 1100 ° C. It is preferable to keep it at 4 ° C / min.

  The temperature range in which the rate of temperature decrease is 6 ° C./min or more is the firing temperature to 1100 ° C. If the temperature lowering rate temporarily becomes less than 6 ° C./min in the temperature range of 1100 ° C. or higher, the ferrite compound of the present invention may not be obtained. In addition, if the temperature-fall rate in the temperature range of calcination temperature-1100 degreeC is 6 degrees C / min or more, the temperature-fall rate in temperature other than that will not be specifically limited.

  Firing is performed using an electric furnace, a gas furnace, or the like. Firing is preferably performed in an atmosphere having an oxygen concentration of 10% or more. If the oxygen concentration is less than 10%, abnormal grain growth or heterogeneous phase formation may occur, making it difficult to use for sintered magnets, bonded magnets, magnetic recording media, and the like. The oxygen concentration is more preferably 20% or more, and most preferably 100%. The firing temperature is preferably 1150 to 1250 ° C. The firing time is preferably 0.5 to 2 hours. The average crystal grain size of the fired body (sintered magnet) obtained by the firing process is about 0.5 to 2 μm.

  The fired body obtained by the firing step is pulverized (pulverized) as necessary to obtain a powder mainly containing a crystal phase composed of the ferrite compound of the present invention, and a bonded magnet, a magnetic recording medium, etc. These performances can be improved by using them in the above. Moreover, after performing the said shaping | molding process, the sintered magnet obtained by the said baking process can be used as a ferrite sintered magnet as it is. That is, the sintered ferrite magnet has a crystal composed of the ferrite compound of the present invention (a ferrite phase having a hexagonal M-type magnetoplumbite structure) as a main phase.

The feature of the method for producing a ferrite compound of the present invention is that, in the firing (sintering) step, the rate of temperature increase from 1100 ° C. to the firing temperature is slowed (1 to 4 ° C./min), and the firing temperature after firing is 1100 ° C. It is in the point which makes the temperature-falling speed until it is faster than the temperature-raising speed (more than 6 ℃ / min). As a result, the amount of Co present at the 4f ₁ and 4f ₂ sites that are the down spin sites in the unit cell of the M-type magnetoplumbite structure is the amount of Co present at the 2a, 4e, and 12k sites that are the up spin sites. it is possible to obtain more than ferrite compounds, in the ferrite sintered magnet of the ferrite compound as the main constituent, it is possible to improve the H _cJ while maintaining high B _r and a high H _k / H _cJ. The reason for the estimation by the present inventors will be described below, but this reason is estimated from the knowledge obtained at the present time, and is not intended to limit the technical scope of the present invention.

The general firing process of sintered ferrite magnets is classified as liquid phase sintering. In the above-described method for producing a ferrite compound according to the present invention, when SiO ₂ and CaCO ₃ are added as sintering aids, the sintering aid becomes part of the liquid phase component during firing, and no sintering aid is added. In some cases, a part of the main phase forms a liquid phase during firing. These liquid phases become a first grain boundary phase existing between two main phases and a second grain boundary phase existing between three or more main phases after firing.

In the method for producing a ferrite compound of the present invention, the heating rate in the temperature range from 1100 ° C. to the firing temperature is 1 to 4 ° C./min, and the solid phase into the liquid phase is slowly passed through the temperature range. In addition to promoting dissolution and precipitation, each atom moves to a position that stabilizes the crystal structure in the crystal of the M-type magnetoplumbite structure. At this time, the site occupied by Co is optimized, and as a result, the amount of Co present at the 4f ₁ and 4f ₂ sites, which are the down spin sites in the unit cell of the M-type magnetoplumbite structure, is increased at the up spin site. More than the amount of Co present at certain 2a, 4e and 12k sites.

  However, when the temperature is lowered after firing, if the temperature range from 1100 ° C to the firing temperature is passed slowly as in the case of the temperature rise, the solid phase dissolves and precipitates again in the liquid phase, and the M-type magnetoplumbite structure. The movement of atoms in the crystal occurs, and the stabilized crystal structure is broken. Therefore, it is considered that the stable crystal structure formed at the time of temperature rise can be maintained as it is by passing the temperature range quickly by setting the temperature drop rate in the temperature range of the firing temperature to 1100 ° C to 6 ° C / min or more. It is done.

  It is considered that the dissolution and precipitation of the solid phase in the liquid phase and the movement of atoms in the crystal of the M-type magnetoplumbite structure occur not only in the CaLaCo ferrite but also in the SrLaCo ferrite in the firing process. However, CaLaCo ferrite and SrLaCo ferrite differ greatly in the following points.

As described above, in CaLaCo ferrite, when SiO ₂ and CaCO ₃ are added as sintering aids, the sintering aid forms a liquid phase during firing, and when no sintering aid is added, one of the main phases. The part forms a liquid phase during firing. That is, Ca is contained in both the main phase and the liquid phase. In the firing step, when the solid phase is dissolved and precipitated in the liquid phase, it is considered that Ca contained in the main phase and Ca contained in the liquid phase move with each other. That is, the mutual movement of Ca between the main phase and the liquid phase promotes the dissolution and precipitation of the solid phase in the liquid phase, and at this time, the site occupied by Co is optimized. As a result, the amount of Co present at the 4f ₁ and 4f ₂ sites, which are the down spin sites, in the unit cell of the M-type magnetoplumbite structure is the amount of Co present at the 2a, 4e and 12k sites, which are the up spin sites. More than expected.

On the other hand, SrLaCo ferrite basically does not contain Ca in the main phase. Therefore, during firing, SiO ₂ and CaCO ₃ added as a sintering aid will mainly form a liquid phase, and unlike CaLaCo ferrite, if no sintering aid is added, a preferred firing temperature around 1200 ° C. In the range, almost no liquid phase is formed. The inventors scanned and transmitted the composition of any three grain boundary phases in a SrLaCo ferrite sintered magnet (added 1.2% by mass of SiO ₂ as a sintering aid and 1.5% by mass of CaCO ₃ in terms of CaO). When a point analysis was performed with a scanning electron microscope (STEM) and an FE-TEM equipped with an energy dispersive X-ray spectroscopy (EDS) function, the results shown in Table 1 were obtained. The unit of content is atomic%.

  As shown in Table 1, the grain boundary phase of the SrLaCo ferrite sintered magnet contains Sr, La, and Fe in addition to Si and Ca added as a sintering aid. From this result, it is considered that in the SrLaCo ferrite, when the solid phase is dissolved and precipitated in the liquid phase, the main phase is dissolved and the main phase component is moved to the liquid phase.

  It has been found that the stability of the crystal structure having a hexagonal M-type magnetoplumbite structure is Sr ferrite> SrLaCo ferrite> CaLaCo ferrite. As described above, in CaLaCo ferrite, it is considered that Ca contained in the main phase and Ca contained in the liquid phase are mutually moved. The crystal structure of CaLaCo ferrite is different from that of Sr ferrite and SrLaCo ferrite. Another factor is the instability. Therefore, in SrLaCo ferrite with a stable crystal structure, the main phase dissolves and the main phase component may move to the liquid phase, but the liquid phase component does not move to the main phase. . That is, it is unlikely that a stable SrLaCo ferrite phase will take Ca into an unstable state. Therefore, in SrLaCo ferrite, there is no mutual movement between the main phase and the liquid phase when the solid phase dissolves and precipitates in the liquid phase, and the main phase components Sr and La move unilaterally to the liquid phase. It is thought that there is. The main phase components Sr and La are dissolved in the liquid phase, that is, Sr and La are eluted from the outer shell of the main phase, leaving a spinel structure with low crystal magnetic anisotropy. This is considered to be a factor that decreases the directivity.

  Also in the ferrite compound of the present invention, the component of the ferrite compound moves to the grain boundary phase (liquid phase) in the production process. However, as described above, CaLaCo ferrite contains Ca in both the ferrite compound and the liquid phase, and the mutual movement of Ca between the ferrite compound and the liquid phase promotes dissolution and precipitation of the solid phase in the liquid phase. At this time, the site occupied by Co is optimized.

Thus, it is considered that different phenomena occur in CaLaCo ferrite and SrLaCo ferrite when the solid phase dissolves and precipitates in the liquid phase. Therefore, in the SrLaCo ferrite, as in the ferrite compound of the present invention, the amount of Co present at the 4f ₁ and 4f ₂ sites, which are the down spin sites in the unit cell of the M-type magnetoplumbite structure, is the up spin site. It is considered that the crystal structure does not become larger than the amount of Co present in the 2a, 4e and 12k sites, and such a crystal structure is characteristic of CaLaCo ferrite containing a certain amount of Ca as a main component, or CaLaCo. It is thought that it appears remarkably in ferrite.

  Examples in which the ferrite compound of the present invention is the main constituent of a sintered ferrite magnet will be described below, but the present invention is not limited thereto.

Example 1
Composition formula representing atomic ratio of metal element: Ca _1-xy La _x A _y Fe _{2n-vw Cov + w} , 1-xy = 0.5, x = 0.5, y = 0, y / (1-x) = Prepare raw material powder by blending CaCO ₃ powder, La (OH) ₃ powder, Fe ₂ O ₃ powder and Co ₃ O ₄ powder so that 0, v + w = 0.3 and n = 5.2, and wet ball mill For 4 hours, dried and sized. Subsequently, it was calcined at 1300 ° C. for 3 hours in the atmosphere, and the obtained calcined body was coarsely pulverized with a hammer mill to obtain a coarsely pulverized powder.

SiO ₂ and CaCO ₃ (CaO equivalent value) shown in Table 2 are added to 100% by mass of the coarsely pulverized powder, and a wet ball mill using water as a dispersion medium has an average particle size of 0.55 μm by the air permeation method. Until finely ground. The obtained finely pulverized slurry is molded at a pressure of about 50 MPa while applying a magnetic field of about 1.3 T so that the pressure direction and the magnetic field direction are parallel while removing the dispersion medium, and forming a plurality of cylindrical shapes. A body (axial direction is magnetic field direction) was obtained.

  The obtained molded body was placed in a firing furnace and fired in the atmosphere at a temperature rising rate and a temperature falling rate shown in Table 2 to obtain sintered ferrite magnets (Sample Nos. 1 to 26). The temperature increase rate and temperature decrease rate described in Table 2 indicate the temperature increase rate from 1100 ° C to 1210 ° C (firing temperature) and the temperature decrease rate from 1210 ° C (calcining temperature) to 1100 ° C, respectively. Firing was performed at 1210 ° C. (firing temperature) for 1 hour. The temperature was raised from room temperature to 1100 ° C. at 7.5 ° C./min, and the cooling from 1100 ° C. to room temperature was performed by turning off the firing furnace and opening the firing furnace door.

注１：1100℃から1210℃（焼成温度）までの昇温速度
注２：1210℃（焼成温度）から1100℃までの降温速度
注３：昇温速度が1〜4℃／分、及び降温速度が6℃／分以上の条件を満たすものを○、それ以外のものを×とした。

Note 1: Temperature increase rate from 1100 ° C to 1210 ° C (firing temperature) Note 2: Temperature decrease rate from 1210 ° C (firing temperature) to 1100 ° C Note 3: Temperature increase rate is 1 to 4 ° C / min, and temperature decrease rate The sample satisfying the condition of 6 ° C./min or more was marked with “◯”, and the other sample was marked with “x”.

The measurement results of the B _r and H _cJ of the sintered ferrite magnet of the sample No.1~8 Figure 1 shows the results of measurement of H _k / H _cJ in FIG. In Figure 1, a plot of black circles shows the value of B _r, plots of black triangles indicates a value of H _cJ. In H _k / H _cJ , H _k is the value of H at the position where J becomes 0.95 J _r in the second quadrant of the J (magnetization magnitude) −H (magnetic field strength) curve ( The same shall apply hereinafter.

The measurement results of the B _r and H _cJ of the sintered ferrite magnet of the sample No.9~18 3 shows the results of measurement of H _k / H _cJ in FIG. 3, the solid line represents the value of B _r, the dotted line indicates the value of H _cJ. 3 and 4, the black circle plot is a sample (No. 9 to 13) with a heating rate of 1 ° C./min, and the black triangle plot is a sample with a heating rate of 4 ° C./min (No. 14 to 18). ).

The measurement results of the B _r and H _cJ of the sintered ferrite magnet of the sample No.19~26 5 shows the results of measurement of H _k / H _cJ in FIG. 5, a plot of black circles shows the value of B _r, plots of black triangles indicates a value of H _cJ.

As shown in FIG. 1 and FIG. 2, in the sample (No. 1 to 8) to which 0.6% by mass of SiO ₂ and 0.7% by mass of CaCO ₃ in terms of CaO were added, the heating rate was 1 to 4 ° C./min. when the range, although B _r and H _k / H _cJ is reduced slightly, H _cJ has significantly improved, H _k / H _cJ was in a 85% or more.

As shown in FIG. 3 and FIG. 4, 0.6% by mass of SiO ₂ and 0.7% by mass of CaCO ₃ in terms of CaO are added, and the temperature rise rate is 1 ° C./min. sample heating rate is 4 ° C. / min (No.14~18), upon the temperature decrease rate and 6 ° C. / min or more, B _r is slightly improved, H _cJ was significantly improved. Further, H _k / H _cJ was maintained at 85% or more. Entire B _r and H _k / H _cJ are found the following 1 ° C. / min sample heating rate (No.9~13), heating rate 4 ° C. / min sample (No.9~13) than It was a little expensive.

As shown in FIG. 5 and FIG. 6, in the sample (No. 19 to 26) to which 1.2% by mass of SiO ₂ and 1.5% by mass of CaCO ₃ in terms of CaO were added, the rate of temperature increase was from 1 ° C./min to 4 ° C./min. when a minute range, decrease in B _r is hardly observed, H _cJ will have significantly has improved, is obtained a very high value ever exceeding 500 kA / m (about 6.3 kOe) It was. H _k / H _cJ was slightly lower than 85%, but remained high.

Next, Samples Nos. 3, 6, 8, 9, and 13 were pulverized to obtain a pulverized sintered body powder. The obtained sintered powder is packed into a vanadium cylinder with an inner diameter of 15 mm, and at room temperature using a high-resolution powder neutron diffractometer (HRPD) in JRR-3 of JAEA. Powder neutron diffraction measurement was performed. The obtained diffraction profile was analyzed by Rietveld using RIETAN-FP, and the Fe sites (2a, 4e, 4f ₁ , 4f) in the unit cell of hexagonal M-type magnetoplumbite structure (hereinafter referred to as “M-type”) The abundance ratio of Co at ₂ and 12k sites) was determined.

  In addition, the sintered powder was mixed with boron nitride powder to form a pellet and SPX-8 BL14B and High Energy Accelerator Laboratory (KEK) Photon Factory BL9A were used for X-ray absorption fine structure (EXAFS) measurements. went. The obtained X-ray absorption spectrum is analyzed in a complementary manner to the Rietveld analysis result using IFEFFIT, and the most probable crystal structure model is determined as the abundance ratio of Co at the Fe site in the unit cell in the M-type structure. did.

Table 3 shows the analysis results of the abundance ratio of Co at the Fe site in the unit cell in the M-type structures of sample Nos. 3, 6, 8, 9, and 13. In Table 3, v indicates the total amount of Co existing at the 2a, 4e, and 12k sites that are the up spin sites, and w indicates the total amount of Co that exists at the 4f ₁ and 4f ₂ sites that are the down spin sites.

  As shown in Table 3, w> v for sample Nos. 3, 6 and 13 (examples of the present invention) in which the heating rate was 1 to 4 ° C./min and the cooling rate was 6 ° C./min or more. ing. On the other hand, sample No. 8 (comparative example) with a temperature decrease rate of 6 ° C / min but a temperature increase rate of 6.67 ° C / min, and sample No. 8 with a temperature increase rate of 1 ° C / min but a temperature decrease rate of 1 ° C / min .9 (comparative example) shows that w <v.

As described above, the sintered ferrite magnet of the ferrite compound of the present invention has as a main constituent, since it is possible to improve the H _cJ while maintaining high B _r and a high H _k / H _cJ, sufficient to thinning Yes.

Example 2
In the composition formula representing the atomic ratio of the metal element: Ca _1-xy La _x A _y Fe _{2 n-vw} Co _{v + w} , n = 5.3, Ba as the element A (y) is blended as shown in Table 4, With respect to 100% by mass of coarsely pulverized powder, 0.6% by mass of SiO ₂ and 0.7% by mass of CaCO ₃ in terms of CaO were added, the firing temperature was 1200 ° C., and the temperature increase rate and temperature decrease rate shown in Table 4 were obtained. Except for the above, the sintered ferrite magnets of Sample Nos. 27 to 31 were obtained in the same manner as Example 1. Note that BaCO ₃ powder was used as the Ba raw material. B _r of resultant sintered ferrite magnet, the measurement result of H _cJ and H _k / H _cJ shown in Table 5. Further, among sample Nos. 27 to 31, for sample Nos. 29, 30 and 31, the abundance ratio of Co at the Fe site in the unit cell in the M-type structure was determined in the same manner as in Example 1. The results are shown in Table 6. In Table 6, v represents the total amount of Co present at the 2a, 4e, and 12k sites that are the up spin sites, and w represents the total amount of Co present at the 4f ₁ and 4f ₂ sites that are the down spin sites.

As is clear from Table 5, the ferrite sintered magnets of sample Nos. 27 to 29 (examples of the present invention) having a heating rate of 1 ° C./min to 4 ° C./min and a cooling rate of 6 ° C./min or more. has a high B _r and high H _cJ and high H _k / H _cJ even when containing a element, as is apparent from Table 6, has a sample No.29 in w> v I understand that. On the other hand, as apparent from Table 5 and Table 6, sample No. 30 (comparative example) with a temperature rising rate of 1 ° C./min but a temperature decreasing rate of 1 ° C./min, and a temperature decreasing rate of 6 ° C./min. In sample No. 31 (comparative example) with a temperature rate of 6.67 ° C./min, w <v, _indicating that H _cJ and H _k / H _cJ are low.

Example 3
In the composition formula representing the atomic ratio of the metal element: Ca _1-xy La _x A _y Fe _{2n-vw Cov + w} , the element A is Sr, and 1-xy, x, y, y / (1-x), v + w and n were blended as shown in Table 7, the firing temperature was 1200 ° C., and the temperature increase rate and temperature decrease rate shown in Table 7 were the same as in Example 1, Sample No. 32 to 36 sintered ferrite magnets were obtained. SrCO ₃ was used as the Sr raw material. B _r of resultant sintered ferrite magnet, the measurement result of H _cJ and H _k / H _cJ shown in Table 8. Further, for sample Nos. 32, 35, and 36 among sample Nos. 32 to 36, the abundance ratio of Co at the Fe site in the unit cell in the M-type structure was determined in the same manner as in Example 1. The results are shown in Table 9. In Table 9, v represents the total amount of Co present at the 2a, 4e, and 12k sites that are the up spin sites, and w represents the total amount of Co present at the 4f ₁ and 4f ₂ sites that are the down spin sites.

As is apparent from Table 8 and Table 9, sample No. 32 having a temperature increase rate of 1 ° C./min to 4 ° C./min, a temperature decrease rate of 6 ° C./min or more, and y / (1-x) is less than 0.56. ferrite sintered magnet of (invention example) it can be seen that shows the w> v, and the high B _r and high H _cJ and high H _k / H _cJ. On the other hand, as apparent from Table 8, sample No. 33 (comparative example) with y / (1-x) of less than 0.56 but with a heating rate of 1 ° C / min but a cooling rate of 1 ° C / min. Sample No. 34 (comparative example) with a temperature decrease rate of 6 ° C / min but a temperature increase rate of 6.67 ° C / min. The temperature increase rate was 1 ° C / min to 4 ° C / min and the temperature decrease rate was 6 ° C / min or more. However, sample No. 35 (comparative example) in which y = 0.4 and y / (1-x) = 0.672, and the rate of temperature increase from 1 ° C / min to 4 ° C / min and the rate of temperature decrease is 6 ° C / min or more Even if 1-xy = 0, y = 0.8 and y / (1-x) = 1.000, the sample No.36 (comparative example) has low H _cJ and H _k / H _cJ. Thus, it can be seen that Sample No. 35 and Sample No. 36 have w <v.

Example 4
In the composition formula representing the atomic ratio of the metal element: Ca _1-xy La _x A _y Fe _{2n-vw Cov + w} , the element A is Sr, and 1-xy, x, y, y / (1-x), A calcined body obtained by calcining a raw material powder containing v + w and n as shown in Table 10 was coarsely pulverized and finely pulverized in the same manner as in Example 1. The obtained finely pulverized slurry was dried at 150 ° C. for 8 hours, and the finely pulverized powder obtained through a mesh having an opening of 100 μm was heated at a rate of temperature increase and decrease as shown in Table 10, except that the firing temperature was 1200 ° C. Firing was carried out in the same manner as in Example 1. The obtained fired body was crushed with an agate mortar to obtain ferrite fired body powders (ferrite compounds) of Sample Nos. 37 to 39. SrCO ₃ was used as the Sr raw material.

Table 11 shows the measurement results of the saturation magnetization σ _s and _HA of the obtained fired ferrite powder (ferrite compound). In addition, Table 12 shows the abundance ratio of Co at the Fe site in the unit cell in the M-type structures of Sample Nos. 37, 38 and 39 obtained in the same manner as in Example 1. In Table 12, v indicates the total amount of Co existing at the 2a, 4e, and 12k sites that are the up spin sites, and w indicates the total amount of Co that exists at the 4f ₁ and 4f ₂ sites that are the down spin sites.

As apparent from Table 11 and Table 12, the sintered ferrite powder of the sample No. 37 (the ferrite compound of the present invention) having a temperature increase rate of 1 ° C./min and a temperature decrease rate of 6 ° C./min is w> v. High σ _s and high _HA . On the other hand, Sample No. 38 (comparative example) with a temperature decrease rate of 6 ° C / min but a temperature increase rate of 6.67 ° C / min, even if the temperature increase rate is 1 ° C / min and the temperature decrease rate is 6 ° C / min, In sample No. 39 (comparative example) in which xy = 0 and y = 0.8 and y / (1-x) = 1.0, w <v and σ _s and _HA are low.

The ferrite compound according to the present invention can exhibit high performance when used in sintered magnets, bonded magnets, magnetic recording media and the like. Especially when the main constituents of the ferrite sintered magnet, with improved H _cJ while maintaining high B _r and a high H _k / H _cJ, sintered ferrite magnets which can respond to thinning are obtained, which ferrite sintered The magnetized magnet can be suitably used for electric parts for automobiles such as various motors, generators, and speakers, parts for electric devices, and the like, and in particular, can contribute to reducing the size, weight and efficiency of these parts.

Claims (2)

A ferrite compound having a hexagonal M-type magnetoplumbite structure and containing Ca, La, Fe and Co as essential components,
The total amount of Co present at the 4f ₁ and 4f ₂ sites which are the down spin sites in the unit cell of the M-type magnetoplumbite structure is greater than the total amount of Co present at the 2a, 4e and 12k sites which are the up spin sites. A ferrite compound characterized by a large amount. 2a, 4e and 12k which are up-spin sites in a unit cell of element A, which is Ca, La, Ba and / or Sr, Fe, hexagonal M-type magnetoplumbite structure in the ferrite compound according to claim 1. Compositional formula showing the atomic ratio of Co ^UP that is Co at the site and Co ^DOWN that is Co ^DOWN that is at the 4f ₁ and 4f ₂ sites that are the down spin sites: Ca _1-xy La _x A _y Fe _{In 2n-vw} Co ^UP _v Co ^DOWN _w , 1-xy, x, y, v, w, and n indicating a molar ratio are
0.23 ≦ 1-xy ≦ 0.75,
0.2 ≦ x ≦ 0.65,
0 ≦ y ≦ 0.4,
0.2 ≦ v + w <0.65,
w> v,
3 <n <6 and
0 ≦ y / (1-x) <0.56
A ferrite compound characterized by satisfying

Images