JP2007197246A - Mn-Co-Zn FERRITE AND MAGNETIC CORE FOR TRANSFORMER - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide an Mn-Co-Zn ferrite keeping high effective magnetic permeability μ constantly in a wide temperature range of -40 to 85 °C even on a ondition that high direct current field of 33 A/m is applied, and a magnetic core for transformer comprising the the ferrite. <P>SOLUTION: The Mn-C0-Zn ferrite comprises basic components, additive components and inevitable impurities and has a composition containing 51.0-54.0 mol% Fe<SB>2</SB>O<SB>3</SB>, 13.0-18.0 mol% ZnO, 0.04-0.60 mol% CoO and the balance being MnO as the basic components, contains 0.005-0.040 mass% SiO<SB>2</SB>and 0.1-0.04 mass% CaO per total ferrite as the additive components and contains <3 mass ppm P per total ferrite as the impurities. <P>COPYRIGHT: (C)2007,JPO&INPIT

Description

  The present invention relates to an MnCoZn ferrite suitable for use in a pulse transformer or the like of an Ethernet device, and a transformer core made of the ferrite.

  As a transformer of an Ethernet device, a pulse transformer using a soft magnetic material for a magnetic core is used for the purpose of matching impedances at input / output terminals or maintaining electrical insulation. This pulse transformer is required to exhibit a high effective magnetic permeability μ when a DC magnetic field is applied in a wide temperature range of −40 to 85 ° C. according to ANSI X3.263-1995 [R2000] which is a US standard. .

  For the magnetic core made of the soft magnetic material, generally, an ultra-small MnZn ferrite having a toroidal shape and an outer diameter of about 3 mm is used. The characteristics of this MnZn ferrite include, among other soft magnetic materials, that high magnetic permeability and high inductance can be easily obtained, and that it is less expensive than amorphous metal.

  However, since MnZn ferrite is an oxide magnetic material, it has the characteristic that the magnetic properties change greatly due to temperature fluctuations, so that it can obtain stable magnetic properties in a wide temperature range compared to metal magnetic materials. Has the disadvantage of being difficult. Therefore, with normal MnZn ferrite, it is difficult to realize high effective magnetic permeability under the application of a DC magnetic field in a wide temperature range of −40 to 85 ° C. as defined by ANSI X3.263-1995 [R2000]. .

It is known that the addition of CoO having positive magnetic anisotropy is effective for improving the temperature dependence of the magnetic properties of MnZn ferrite. For example, in Patent Document 1, 0.01 to 1.0 mol% cobalt oxide is added to a basic composition composed of 50 to 56 mol% iron oxide, 30 to 36 mol% manganese oxide, and 20 to 6 mol%, An oxide magnetic material having improved temperature dependency of initial permeability in a temperature range of −30 to 90 ° C. is disclosed. In addition, Patent Document 2 describes a MnZn-based ferrite mainly composed of Fe ₂ O ₃ : 51 to 54 mol%, ZnO: 14 to 21 mol%, and the balance MnO, which is used for the same magnetic core as the communication transformer of the present invention. A technique for obtaining MnZn ferrite having excellent magnetic characteristics when a DC bias is superimposed in a wide temperature range of 0 to 70 ° C. by adding an appropriate amount of cobalt oxide is disclosed.
Japanese Patent Publication No.52-31555 JP 2004-196632 A

Certainly, the addition of CoO is effective in improving the temperature dependence of the magnetic properties of MnZn ferrite. However, the size of the ^{Co 2+} ions is smaller compared to that of ^{Mn 2+} ions are substituted by ^{Co 2+} ions, the addition of CoO increases the ^{O 2-} moving speed of a factor governing the sintering rate . Therefore, the MnZn ferrite added with CoO has a tendency to increase the initial permeability significantly because the sintering is promoted and the crystal grains are easily grown as compared with the additive-free MnZn ferrite.

  However, since a magnetic material having a high initial magnetic permeability is easily magnetized by applying a magnetic field, magnetic saturation is likely to occur, and the magnetic permeability decreases when a high DC magnetic field of 33 A / m is applied. That is, the MnZn ferrite to which CoO is added has a defect that the effective magnetic permeability μ when a DC magnetic field of 33 A / m is applied is deteriorated as compared with the MnZn ferrite without addition. Therefore, in order to achieve high magnetic permeability when a DC magnetic field is applied, it is necessary to moderately reduce the initial magnetic permeability by some means so that magnetic saturation does not easily occur.

  As described above, the initial magnetic permeability increases as the ferrite crystal grain size increases. In order to increase the effective magnetic permeability when a DC magnetic field is applied, it is considered effective to moderately suppress ferrite crystal grain growth. However, Patent Document 1, which is a prior art, has a description regarding the temperature dependence of the initial permeability, but does not describe any ferrite crystal grain size. Further, although Patent Document 2 has a description regarding the average crystal grain size, there is no disclosure of means for realizing the crystal grain size. Therefore, it is impossible to obtain a high effective magnetic permeability when a DC magnetic field is applied by reducing the temperature dependence of the magnetic permeability only by following the contents described in these patent documents.

  Accordingly, an object of the present invention is to provide an MnCoZn ferrite capable of constantly maintaining a high effective magnetic permeability μ even when a high DC magnetic field of 33 A / m is applied in a wide temperature range of −40 to 85 ° C. and its ferrite It is to provide a magnetic core for a transformer.

In order to solve the above-described problems of the prior art, the inventors studied to increase the effective permeability under application of a DC magnetic field by appropriately suppressing the crystal grain growth of MnCoZn ferrite. As a result, it is possible to simultaneously add appropriate amounts of SiO ₂ and CaO to MnCoZn ferrite, and to further reduce the content of P as an impurity inevitably mixed due to the raw material of iron oxide. The present invention has been found by finding it effective.

That is, the present invention is a ferrite composed of a basic component, an additive component, and unavoidable impurities, and the basic components are Fe ₂ O ₃ : 51.0 to 54.0 mol%, ZnO: 13.0 to 18.0 mol. %, CoO: 0.04 to 0.60 mol%, the balance being MnO, and the additive component is SiO ₂ : 0.005 to 0.04 mass% and CaO: 0.1 to 0.4 mass% with respect to the total ferrite. And MnCoZn ferrite characterized by containing less than 3 mass ppm of P as an impurity.

MnCoZn ferrite of the present invention further as an additive _{component, ZrO 2: 0.005~0.075mass%, Ta} 2 O 5: 0.005~0.075mass%, HfO 2: 0.005~0.075mass%, nb ₂ O _5: characterized in that it contains one or more selected from among 0.005~0.075mass%.

  The MnCoZn ferrite of the present invention is characterized by having an effective permeability of 2000 or more when a DC magnetic field of 33 A / m is applied in the entire temperature range of −40 to 85 ° C.

  Moreover, this invention is a magnetic core for transformers which consists of said MnCoZn ferrite.

  According to the present invention, the effective permeability under a DC magnetic field of 33 A / m is maintained at a high value of 2000 or more in a wide temperature range of −40 to 85 ° C., which is impossible with the conventional MnZn ferrite. MnCoZn ferrite can be obtained. Therefore, the MnCoZn ferrite of the present invention can be suitably used particularly as a magnetic core material for a pulse transformer of an Ethernet device.

In order to increase the effective magnetic permeability μ when a DC magnetic field of 33 A / m is applied, the inventors first add SiO ₂ to make the crystal structure uniform, and simultaneously add an appropriate amount of CaO that segregates at grain boundaries. Then, by suppressing the crystal grain growth, an attempt was made to moderately suppress the crystal grain growth of MnCoZn ferrite and to reduce the initial permeability μ _i . However, when CaO is added, a new problem that an abnormal growth of crystal grains often appears. Ingredients that should originally exist at the grain boundaries are taken into the abnormally grown crystal grains. As a result, in the ferrite in which abnormal grains appear, the movement of the domain wall is hindered, so that the effective magnetic permeability is greatly reduced and the strength is also reduced.

Therefore, the inventors focused on the fact that most of Fe ₂ O ₃ which is the main raw material of ferrite is derived from the scale generated in the steel manufacturing process, and this Fe ₂ O ₃ raw material and the abnormal grain growth The relevance of was investigated. As a result, when a small amount of P present in steel (in the scale) as an unavoidable impurity is contained in ferrite, the growth of ferrite crystal grains is promoted, the initial permeability increases, and high direct current increases. It has been found that the effective magnetic permeability is lowered when a magnetic field is applied, and that abnormally grown grains appear when more P is mixed. This abnormal grain growth is observed when CaO is contained in an amount more than an appropriate amount and / or when it contains a large amount of P. Similarly to P, steel contains CaO as an unavoidable impurity. It is presumed that the presence of calcium phosphate Ca ₃ (PO ₄ ) ₂ , which is a Ca compound, promotes crystal grain growth.

However, although Patent Document 1 described above describes the initial permeability, the effective permeability under the application of a DC magnetic field and the regulation of the content to eliminate the influence of P which is an impurity are described. There is no description. Therefore, it is practically difficult to achieve the object of the present invention to obtain a high effective magnetic permeability under a DC magnetic field application in a wide temperature range only by following the same document. Furthermore, since Patent Document 2 states that “P content is preferable”, it is impossible to realize a high effective magnetic permeability under application of a DC magnetic field based on the description in this document. It was.
The present invention is based on the above findings.

Next, the component composition necessary for the MnCoZn ferrite according to the present invention to realize a high effective magnetic permeability of 2000 or more under a DC magnetic field application of 33 A / m in a wide temperature range of −40 to 85 ° C. will be described. .
Fe ₂ O _3: 51.0~54.0mol%
Fe ₂ O ₃ is a basic component that greatly affects the effective magnetic permeability. When the content of Fe ₂ O ₃ is small, the effective magnetic permeability under application of a DC magnetic field in a low temperature range is lowered, so it is necessary to contain 51.0 mol% at least. However, when there is too much Fe ₂ O ₃ , the effective magnetic permeability under the application of a DC magnetic field in a high temperature range decreases, so the upper limit is made 54.0 mol%.

ZnO: 13.0 to 18.0 mol%
ZnO is also a basic component that greatly affects the effective permeability. ZnO has the effect of increasing the effective magnetic permeability under the application of a DC magnetic field as the content increases. In order to achieve a high effective magnetic permeability of 2000 or more, it is necessary to contain at least 13.0 mol%. is there. However, if the content exceeds the appropriate amount, the effective permeability under application of a DC magnetic field at low temperatures decreases, and the Curie temperature, which is the temperature at which the ferromagnetic material loses magnetism, decreases. The effective magnetic permeability under the direct current magnetic field application is also reduced. Therefore, the upper limit is made 18.0 mol%.

CoO: 0.04 to 0.60 mol%
CoO is a basic component having positive magnetic anisotropy, and for the first time by adding CoO, it is possible to obtain a high effective magnetic permeability under application of a high DC magnetic field in a wide temperature range of −40 to 85 ° C. Become. For that purpose, it is necessary to contain CoO at least 0.04 mol%. However, if the amount exceeds the appropriate amount, the effective permeability under the application of a DC magnetic field is decreased in the entire temperature range, so the upper limit needs to be 0.60 mol%.

MnO: Remaining Basic Component The ferrite of the present invention is MnCoZn-based, and the remaining basic components other than Fe ₂ O ₃ , ZnO and CoO are MnO. MnO is an essential component for realizing a high effective magnetic permeability of 2000 or more under application of a direct current magnetic field of 33 A / m.

The MnCoZn ferrite of the present invention needs to contain SiO ₂ and CaO as additive components in the following ranges in addition to the above basic components.
SiO _2: 0.005~0.040mass%
SiO ₂ has the effect of homogenizing the crystal structure of ferrite and reduces the vacancies remaining in the crystal grains to promote the formation of grain boundaries and suppress the grain growth. The MnCoZn ferrite of the present invention is an essential component for realizing a high effective magnetic permeability when a DC magnetic field is applied. To obtain the above effect, SiO ₂ has to contain 0.005 mass% at least. However, when the addition amount is too large, abnormal grains appear on the contrary, and the effective magnetic permeability at the time of applying the DC magnetic field is remarkably lowered. Therefore, it is necessary to keep it at 0.040 mass% or less.

CaO: 0.100 to 0.400 mass%
CaO has the effect of segregating to the crystal grain boundaries of ferrite and suppressing crystal grain growth. By adding an appropriate amount, CaO moderately lowers the initial permeability, and thus has a high effective permeability when a DC magnetic field is applied. It is a component that contributes to realization. Therefore, CaO is an essential additive component in the present invention, and it is necessary to contain at least 0.100 mass%. However, when the addition amount is excessive, abnormal grains appear and the effective magnetic permeability when a DC magnetic field is applied is remarkably lowered. Therefore, it is necessary to keep it to 0.400 mass% or less.

P: less than ₃ massppm P is an impurity component inevitably contained in iron oxide as a raw material for Fe ₂ O ₃ , and is one of the most important components in the present invention. There is no problem if the P content is less than a very small amount of 3 mass ppm. However, when 3 mass ppm or more is contained, the crystal grain growth of ferrite is promoted and the initial magnetic permeability is increased, resulting in a decrease in effective magnetic permeability when a DC magnetic field is applied. In addition, when P is contained in a large amount, abnormal grain growth is induced, and the effective permeability when a DC magnetic field is applied is remarkably reduced. Therefore, in order to remove these adverse effects, it is necessary to limit P to less than 3 massppm.

In order to control the P content within the above range, it is desirable to use a high-purity material having a low P content as a raw material such as Fe ₂ O ₃ , MnO, and ZnO. Also, the medium used for mixing and pulverization in a ball mill or the like may be mixed due to wear, so that it is desirable to use a medium having a low P content.

The MnCoZn ferrite of the present invention includes ZrO ₂ : 0.005 to 0.075 mass%, Ta ₂ O ₅ : 0.005 to 0.075 mass%, HfO as optional addition components in addition to the essential addition components. _{2: 0.005~0.075mass%, Nb 2 O} 5: one or more selected from among 0.005～0.075Mass% may be added.
Since these additive components are all compounds having a high melting point, when added to MnCoZn ferrite, they have the function of reducing crystal grains, thereby suppressing the formation of coarse crystal grains and applying a DC magnetic field. It has the effect of improving the effective magnetic permeability at the time. This effect can be obtained by single addition or complex addition. However, if the addition amount is less than the above appropriate range, the effect is not obtained, and in the case of a large amount, the occurrence of abnormal grains is induced, and the effective permeability when applying a DC magnetic field is reduced. It is desirable to be within the above range.

Next, the manufacturing method of the MnCoZn ferrite of this invention is demonstrated.
The raw powders of Fe ₂ O ₃ , ZnO, CoO and MnO are weighed so that the basic component composition of the ferrite after firing becomes a predetermined value, and these are sufficiently mixed and then calcined. A predetermined amount of the above-described additive components are added to the baked powder and pulverized. At this time, it is necessary to perform sufficient homogenization so that the added component distribution is not biased. An organic binder such as polyvinyl alcohol is added to the raw material powder having the target composition as described above, granulated, pressed into a predetermined core shape, fired under appropriate conditions, and a ferrite fired body (core Product).
The thus obtained MnCoZn ferrite exhibits a high effective magnetic permeability of 2000 or more under a DC magnetic field of 33 A / m in a wide temperature range of −40 to 85 ° C., which was impossible with the conventional MnZn ferrite. It will be a thing.

Each raw material powder was weighed so that the ratio of Fe ₂ O ₃ , ZnO, CoO and MnO would be the values shown in Table 1 when all Fe and Mn contained in the ferrite were converted as Fe ₂ O ₃ and MnO. The raw material powder was mixed for 16 hours using a ball mill, and then calcined at 925 ° C. for 3 hours in air. At this time, all raw materials including iron oxide are all high-purity materials, and a ball mill as a mixing and grinding medium is also used with a low P content. The amount was suppressed to 2 massppm.
Next, to this calcined powder, SiO ₂ and CaO are added so as to have the ratio shown in Table 1 and pulverized with a ball mill for 12 hours, and the obtained pulverized powder is granulated by adding polyvinyl alcohol, and 118 MPa Was applied to form a toroidal core having an outer diameter of 25 mm, an inner diameter of 15 mm, and a height of 5 mm. Thereafter, the compact was charged into a firing furnace and fired at a maximum temperature of 1350 ° C. to obtain a ferrite fired body sample.

  Each sample obtained in this manner was wound with 10 turns, and an LCR meter (4284A: manufactured by Hewlett Packard) was applied with a DC magnetic field of 33 A / m applied by a DC application device (42841A: manufactured by Hewlett Packard). ) Was used to measure the effective magnetic permeability μ under the conditions of a voltage of 100 mV and a frequency of 100 kHz at temperatures of −40 ° C., 0 ° C., 23 ° C., 70 ° C., and 85 ° C.

The results of the above measurements are shown together in Table 1. As can be seen from Table 1, Sample Nos. 1-3, 1-5, 1-9, and 1-12, which are examples of the present invention, were applied at a direct current magnetic field of 33 A / m at all temperatures from -40 ° C to 85 ° C. The effective magnetic permeability μ is always 2000 or more.
On the other hand, in the comparative example (sample number 1-1) in which Fe ₂ O ₃ is more than 54.0 mol%, μ at 85 ° C. is reduced to less than 2000. On the contrary, in the comparative example (sample number 1-2) containing less than 51.0 mol% of Fe ₂ O ₃ , μ at −40 ° C. is reduced to less than 2000.
Moreover, in the comparative example (sample number 1-4) which does not contain CoO, although an average crystal grain diameter is in the range of the present invention, μ at −40 ° C. and 85 ° C. does not reach 2000. On the other hand, in the comparative example (Sample Nos. 1-6) containing a large amount of CoO, the average crystal grain size was larger than 8 μm and μi increased, so that the effective permeability μ decreased in the entire temperature range, and −40 It is less than 2000 at ℃, 70 ℃ and 85 ℃.
Moreover, in the comparative example (sample number 1-7) containing more ZnO than this invention range, (micro | micron | mu) in -40 degreeC, 70 degreeC, and 85 degreeC has fallen to less than 2000. However, on the contrary, in the comparative example (sample number 1-8) in which ZnO is insufficient, μ decreases to less than 2000 in the entire temperature range.
In addition, when attention is paid to the contents of SiO ₂ and CaO, in these comparative examples (sample numbers 1-10 and 1-11), which are less than the scope of the present invention, coarse crystal grains appear, the average crystal grain size Becomes larger than 8 μm, μ decreases in the entire temperature range, and is 2000 or less at −40 ° C. and 85 ° C. On the other hand, in either of the comparative examples (Sample Nos. 1-13, 1-14, 1-15) which are larger than the range of the present invention, abnormal grains appear and the crystal grain size becomes a value two orders of magnitude larger. The magnetic permeability μ is greatly reduced in the entire temperature range.

Using various iron oxide raw materials with different P contents, the P content contained in the ferrite sample after firing was calculated to be 5, 15 and 30 massppm, and the contained Fe and Mn were determined. When all converted to Fe ₂ O ₃ and MnO, the same as Example 1 of the present invention (Sample No. 1-5), Fe ₂ O ₃ : 52.0 mol%, ZnO: 16.0 mol%, CoO: 0 .4Mol%, materials were weighed so that a composition of the remainder MnO, a ball mill and mixed for 16 hours using a performs calcination 925 ° C. × 3 hours in air, the SiO ₂ to the calcined powder 0.010mass %, CaO 0.150 mass%, pulverized in a ball mill for 12 hours, added polyvinyl alcohol to the obtained pulverized powder and granulated, applied a pressure of 118 MPa, outer diameter 25 mm, A toroidal core having an inner diameter of 15 mm and a height of 5 mm was molded, and then this molded body was placed in a firing furnace and fired at a maximum temperature of 1350 ° C. to obtain a ferrite fired body sample.

  Each of these samples was wound with 10 turns, and the effective permeability μ at a voltage of 100 mV and a frequency of 100 kHz was applied with a DC magnetic field of 33 A / m using the same DC application device and LCR meter as in Example 1. Was measured at temperatures of −40 ° C., 0 ° C., 23 ° C., 70 ° C. and 85 ° C.

  The obtained results are shown in FIG. 1 together with the results of Sample Nos. 1-5 of Example 1. From the same figure, in Sample No. 1-5 of the present invention example in which P was suppressed to less than 3 mass ppm, no coarse crystal grains were observed, and a DC magnetic field of 33 A / m was applied in the entire temperature range of −40 to 85 ° C. In the comparative examples (sample numbers 2-1 and 2-2) containing 5 massppm and 15 massppm of P, coarse crystal grains appear, whereas the effective magnetic permeability in FIG. The effective magnetic permeability under the application of a 33 A / m DC magnetic field is reduced, and the value is less than 2000 on the low temperature side or the high temperature side. Further, in the comparative example (sample number 2-3) containing 30 mass ppm of P, as a result of abnormal grain growth, the effective magnetic permeability is greatly reduced, and μ is below 2000 in the entire temperature range.

The same basic components as in Example 2 are used, and the same amount of SiO ₂ and CaO as in Example 2 is added to the calcined powder in which the P content is suppressed to 2 massppm, and Nb ₂ O ₅ , Ta are added as additional components. ₂ O ₅ , HfO ₂ and ZrO ₂ were added so that the final composition would be the values shown in Table 2, pulverized with a ball mill for 12 hours, and the resulting pulverized powder was granulated by adding polyvinyl alcohol, and a pressure of 118 MPa Was added to a toroidal core having an outer diameter of 25 mm, an inner diameter of 15 mm, and a height of 5 mm. Thereafter, the molded body was placed in a firing furnace and fired at a maximum temperature of 1350 ° C. to obtain a ferrite fired body sample.

  Each of these samples was wound with 10 turns, and the effective permeability μ at a voltage of 100 mV and a frequency of 100 kHz was applied with a DC magnetic field of 33 A / m using the same DC application device and LCR meter as in Example 1. Was measured at temperatures of −40 ° C., 0 ° C., 23 ° C., 70 ° C. and 85 ° C.

The obtained results are shown together in Table 2. From Table 2, all of the present invention examples (sample numbers 3-1 to 3-15) to which one or more of Nb ₂ O ₅ , Ta ₂ O ₅ , HfO ₂ and ZrO ₂ were added in an appropriate amount The appearance of coarse crystal grains is suppressed, and as a result, an excellent characteristic that the effective magnetic permeability μ under a direct current magnetic field of 33 A / m exhibits 2000 or more in the entire temperature range of −40 to 85 ° C. is obtained. It has been. Further, when compared with Sample Nos. 1-5 of the inventive examples to which these additive components are not added, μ shows an equal or higher value. However, in any of the comparative examples (sample numbers 3-16 to 3-18) in which one of these four components is contained in a large amount exceeding the appropriate range, as a result of abnormal grain growth, the effective permeability is in the entire temperature range. However, it has dropped significantly.

It is a graph which shows the influence which content of P contained in a ferrite has on the effective magnetic permeability μ when a DC magnetic field is applied.

Claims (4)

A ferrite composed of a basic component, an additive component, and unavoidable impurities, the basic components being Fe ₂ O ₃ : 51.0 to 54.0 mol%, ZnO: 13.0 to 18.0 mol%, CoO: 0.00. 04~0.60mol%, consists composition of the remainder MnO, _SiO 2 as an additive component relative to the total ferrite: 0.005~0.04mass% and CaO: containing 0.1~0.4mass%, as impurities An MnCoZn ferrite containing less than 3 massppm of P with respect to the total ferrite. As additional components, ZrO ₂ : 0.005 to 0.075 mass%, Ta ₂ O ₅ : 0.005 to 0.075 mass%, HfO ₂ : 0.005 to 0.075 mass%, Nb ₂ O ₅ : 0. The MnCoZn ferrite according to claim 1, comprising one or more selected from 005 to 0.075 mass%. 3. The MnCoZn ferrite according to claim 1, wherein an effective permeability when a direct current magnetic field of 33 A / m is applied is 2000 or more in a whole temperature range of −40 to 85 ° C. 4. The magnetic core for transformers which consists of a MnCoZn ferrite of any one of Claims 1-3.

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