Patent Application
20200135371
The present invention relates to a magnetic core and a coil component.
In the field of electronic devices, a surface-mounting type coil component is widely used as a power inductor. As one of the specific structures of the surface-mounting type coil component, a flat coil structure is known which uses print circuit board technology.
Patent document 1 proposes a coil component having a magnetic core produced using two or more metal magnetic powders having different particle sizes. By using two or more metal magnetic powders having different particle sizes, it is known to improve a permeability.
Patent document 1: 2017-103287
Recently, a magnetic core having even better properties is demanded. The present invention is attained in view of such circumstances and the object is to provide a magnetic core and a coil component having stably excellent permeability and withstand voltage.
In order to attain the above object, the magnetic core according to the present invention includes a metal magnetic powder in which
the metal magnetic powder has a large size powder, an intermediate size powder, and a small size powder,
a particle size of the large size powder is 10 μm or more and 60 μm or less,
a particle size of the intermediate size powder is 2.0 μm or more and less than 10 μm,
a particle size of the small size powder is 0.1 μm or more and less than 2.0 μm,
the large size powder, the intermediate size powder, and the small size powder have an insulation coating, and
when A1 represents an average insulation coating thickness of the large size powder, A2 represents an average insulation coating thickness of the intermediate size powder, A3 represents an average insulation coating thickness of the small size powder, A3 is 30 nm or more and 100 nm or less, A3/A1≥1.3 is satisfied, and A3/A2≥1.0 is satisfied.
By constituting the magnetic core according to the present invention as described in above, a magnetic core stably having excellent permeability and withstand voltage can be obtained.
The small size powder may include a permalloy.
A ratio of the large size powder existing with respect to the metal magnetic powder may be 39% or more and 86% or less in terms of an area ratio in a cross section of the magnetic core.
A1≥10 nm and A2≥10 nm may be satisfied.
A3 may be 40 nm or more and 80 nm or less.
The metal magnetic powder may include a Fe-based nano crystal.
A ratio of the intermediate size powder existing with respect to the metal magnetic powder may be 8% or more and 39% or less in terms of an area ratio in a cross section of the magnetic core.
The insulation coating may be a coating film including a glass made of SiO2 or a phosphate chemical conversion coating including phosphate.
The magnetic core may include a metal magnetic powder including the nano crystal and also a metal magnetic powder which does not include the nano crystal as the metal magnetic powder, and a ratio of the metal magnetic powder including the nano crystal with respect to entire magnetic metal powder may be 40 wt % to 90 wt % in terms of a weight ratio.
The coil component according to the present invention includes the above mentioned magnetic core and a coil.
Hereinafter, the present invention is described based on the embodiments shown in the figures.
As one embodiment of a coil component according to the present invention, a coil component 2 shown in
As shown in
The insulation board 11 is preferably made of a generally available print board material in which a glass cloth is impregnated with epoxy resin; but it is not particularly limited to this.
Also, in the present embodiment, the shape of the resin board 11 is rectangular shape, but it may be any other shape. A method of forming the resin board 11 is not particularly limited and for example it may be formed by an injection molding, a doctor blade method, a screen printing, and the like.
Also, at the upper face (one of the main surface) of the insulation board 11 in Z-axis direction, an internal electrode pattern is formed which is made of an inner conductor path 12 having a circular spiral shape. The inner conductor path 12 becomes a coil at the end. Also, a material of the inner conductor path 12 is not particularly limited.
At an inner end of the inner conductor path 12 of a spiral form, a connecting end 12a is formed. Also, at an outer end of the inner conductor path 12 of a spiral form, a lead contact 12b is formed so that it is exposed at one end along X-axis direction of the magnetic core 10.
At the lower face (the other main surface) of the insulation board 11 in Z-axis direction, the internal electrode pattern is formed which is made of an inner conductor path 13 of a spiral form. The internal conductor path 13 becomes a coil at the end. Also, a material of the inner conductor path 13 is not particularly limited.
At an inner end of the inner conductor path 13 of a spiral form, a connecting end 13a is formed. Also, at an outer end of the inner conductor path 13 of a spiral form, a lead contact 13b is formed so that it is exposed at one end along X-axis direction of the magnetic core 10.
As shown in
When the inner conductor path 12 of a spiral form is viewed from the upper face 11a of the insulation board 11, the inner conductor path 12 forms a spiral in counterclockwise from the lead contact 12b at the outer end to the connecting end 12a at the inner end.
On the other hand, when the inner conductor path 13 of a spiral form is viewed from the upper face 11a of the insulation board 11, the inner conductor path 13 forms a spiral in counterclockwise from the connecting end 13a at the inner end to the lead contact 13b of the outer end.
Thereby, a direction of magnetic flux generated by electrical current flowing to the inner conductor paths 12 and 13 of a spiral form matches, and the magnetic flux of the inner conductor paths 12 and 13 of a spiral form is superimposed and becomes stronger, thus a larger inductance can be obtained.
The upper core 15 has a center projection part 15a of a circular column shape projecting down in Z-axis direction at a center part of a core main body of a rectangular flat board shape. Also, the upper core 15 has a side projection part 15b of a board shape projecting down in X-axis direction at both ends of Y-axis direction of the core main body of a rectangular flat board shape.
The lower core 16 has a rectangular flat board shape as similar to the core main body of the upper core 15, and the center projection part 15a and the side projection part 15b of the upper core 15 respectively connect with a center part and an end part in Y-axis direction of the lower core 16, thereby the lower core 16 and the upper core 15 are formed integrally.
Note that, in
As shown in
As shown in
Here, in the present embodiment, the magnetic core 10 is constituted by the metal magnetic powder containing resin. The metal magnetic powder containing resin is a magnetic material in which the metal magnetic powder is mixed in a resin.
Here, in the present embodiment, when the magnetic core 10 is cut at an arbitrary cross section and the cross section is observed, the metal magnetic power having three different sizes which are the large size powder, the intermediate size powder, and the small size powder is observed. In other words, the metal magnetic powder has the large size powder, the intermediate size powder, and the small size powder.
The particle size (circular equivalent diameter) of the large size powder is 10 μm or more and 60 μm or less; the particle size of the intermediate size powder is 2.0 μm or more and less than 10 μm; and the particle size of the small size powder is 0.1 μm or more and less than 2.0 μm.
Further in the present embodiment, the large size powder, the intermediate size powder, and the small size powder are insulation coated as shown in
A material of the insulation coating 22 is not particularly limited, and an insulation coating generally used in the present technical field can be used. A coating film including a glass made of SiO2 or a phosphate chemical conversion coating including phosphate is preferably used. For the metal magnetic powder including permalloy, the coating film including a glass made of SiO2 is particularly preferably used. Also, a method of carrying out an insulation coating is not particularly limited, and a method usually used in the present technical field can be used.
In the present embodiment, by suitably regulating the thickness of the insulation coating of the large size powder, the intermediate size powder, and the small size powder, the permeability and the withstand voltage can be maintained good stably. Particularly, it is a characteristic feature to make the thickness of the insulation coating of the small size powder thicker than the thickness of the insulation coating of the large size powder.
Specifically, when A1 represents the average insulation coating thickness of the large size powder, A2 represents the average insulation coating thickness of the intermediate size powder, and A3 represents the average insulation coating thickness of the small size powder, A3 is 30 nm or more and 100 nm or less; and A3/A1≥1.3 and A2≥1.0 are satisfied.
A1 and A2 are not particularly limited. A1≥10 nm and A2≥10 nm may be satisfied.
Also, A3 may be 40 nm or more and 80 nm or less.
The particle size of the metal magnetic powder of the insulation coated metal magnetic powder is a length d1 shown in
Further, a method of measuring A1, A2, and A3 of the magnetic core 10 according to the present invention is not particularly limited. For example, at least 5 places in an arbitrary cross section of the magnetic core 10 were subjected to measure the thickness of the insulation coating of the large size powder, the intermediate size powder, and the small size powder at a magnification of 200000× to 500000×; then the average was calculated. Note that,
The material of the metal magnetic powder is not particularly limited. For example, the metal magnetic powder may be amorphous or it may include a nano crystal. Also, the metal magnetic powder may include permalloy.
Particularly, the large size powder and the small size powder may include the nano crystal. Here, the nano crystal is a crystal having a crystal particle size of nano order; and it is a crystal of 1 nm or more and 100 nm or less. Also, the nano crystal does not necessarily have to be included in all of the large size powder, but preferably 30% or more in terms of number of the large size powder includes the nano crystal.
Further, the intermediate size powder may include the nano crystal and 30% or more in terms of number of the intermediate size powder may include the nano crystal. By including the nano crystal in the intermediate size powder, the permeability further improves.
Note that, in the powder including the nano crystal, usually a plurality of nano crystals is included in one particle of powder. That is, the particle size of the powder and the crystal particle size are different.
In the present embodiment, by including the nano crystal in the large size powder, the permeability of the magnetic core improves. Also, the withstand voltage is suitably maintained without significantly decreasing.
Hereinafter, the nano crystal is described in further detail.
The nano crystal of the present embodiment is preferably a Fe-based nano crystal. The Fe-based nano crystal has a particle size of nano order and a crystal structure of Fe is bcc (body centered cubic) structure.
In the present embodiment, the Fe-based nano crystal preferably has an average particle size of 5 to 30 nm. A soft magnetic alloy precipitated with such Fe-based nano crystal tends to have a high saturated magnetic flux density and a low coercivity.
The composition of the Fe-based nano crystal in the present embodiment is not particularly limited. For example, M may be included besides Fe. Note that, M is one or more selected from the group consisting of Nb, Hf, Zr, Ta, Mo, W, and V.
The composition of the metal magnetic powder including the Fe-based nano crystal is not particularly limited. For example, it may be a soft magnetic alloy having a main component made of a compositional formula of (Fe(1−(α+β))X1αX2β)(1−(a+b+c+d+e+f+g))MaBbPcSidCeSfTig; in which
X1 is one or more selected from the group consisting of Co and Ni,
X2 is one or more selected from the group consisting of Al, Mn, Ag, Zn, Sn, As, Sb, Cu, Cr, Bi, N, O, and rare earth elements,
M is one or more selected from the group consisting of Nb, Hf, Zr, Ta, Mo, W, and V; and the main component may satisfy the following
0.020≤a≤0.14,
0.020<b≤0.20,
0≤c≤0.15,
0≤d≤0.14,
0≤e≤0.030,
0≤f≤0.010,
0≤g≤0.0010,
α≥2 0,
β≥0, and
0≤α+β≤0.50.
Hereinafter, each component of the metal magnetic powder including the Fe-nano crystal is described in detail.
M is one or more selected from the group consisting of Nb, Hf, Zr, Ta, Mo, W, and V.
A content (a) of M satisfies 0.020≤a≤0.14. When “a” is small, a crystal having larger size than the nano crystal tends to be formed easily during the production of the metal magnetic powder. Also, a resistivity of the metal magnetic powder tends to decrease easily, the coercivity tends to increase easily, and the permeability tends to decrease easily. When “a” is large, a saturation magnetic flux density of the metal magnetic powder tends to decease easily.
A content (b) of B satisfies 0.020<b≤0.20. When “b” is small, a crystal having larger size than the nano crystal tends to be formed easily during the production of the metal magnetic powder. Also, the resistivity of the metal magnetic powder tends to decrease easily, the coercivity tends to increase easily, and the permeability tends to decrease easily. When “b” is large, the saturation magnetic flux density of the metal magnetic powder tends to decease easily.
A content (c) of P satisfies 0≤c≤0.15. That is, P may not be included. When “c” is large, the saturation magnetic flux density of the metal magnetic powder tends to decease easily.
A content (d) of Si satisfies 0≤d≤0.14. That is, Si may not be included. When “d” is too large, the coercivity of the metal magnetic powder tends to increase easily.
A content (e) of C satisfies 0≤e≤0.030. That is, C may not be included. When “e” is large, the resistivity of the metal magnetic powder tends to decrease easily, and the coercivity tends to increase easily.
A content (f) of S satisfies 0≤f≤0.010. That is, S may not be included. When “f” is large, the coercivity tends to increase easily.
A content (g) of Ti satisfies 0≤g≤0.0010. That is, Ti may not be included. When “g” is large, the coercivity tends to increase easily.
A content (1−(a+b+c+d+e+f+g)) of Fe is preferably 0.73≤(1−(a+b+c+d+e+f+g))≤0.95. By having (1−(a+b+c+d+e+f+g)) within the above range, the Fe-based nano crystal becomes easy to obtain.
Also, part of Fe may be substituted by X1 and/or X2.
X1 is one or more selected from the group consisting of Co and Ni. Regarding a content of X1, it may be α=0. That is, X1 may not be included.
Also, a number of X1 atoms in the entire composition is preferably 40 at % or less when a number of atoms of the entire composition is 100 at %. That is, 0≤α{1−(a+b+c+d+e+f+g)}≤0.40 is preferably satisfied.
X2 is one or more selected from the group consisting of Al, Mn, Ag, Zn, Sn, As, Sb, Cu, Cr, Bi, N, 0, and rare earth elements. Regarding a content of X2, it may be β=0. That is, X2 may not be included. Also, a number of X2 atoms in the entire composition is preferably 3.0 at % or less when a number of atoms of entire composition is 100 at %. That is, 0≤β{1−(a+b+c+d+e+f+g)}≤0.030 is preferably satisfied.
In regards with a substitution amount of Fe which can be substituted by X1 and/or X2, it may be half or less of Fe in terms of a number of atoms. That is, it may be 0≤α+β≤0.50. When α+β>0.50, it becomes difficult to obtain the Fe-nano crystal.
Also, elements other than mentioned in above may be included within the range which does not significantly influence the properties. For example, these may be included in 0.1 wt % or less with respect to 100 wt % of the metal magnetic powder.
In the present embodiment, at an arbitrary cross section of the magnetic core 10, a ratio of the large size powder existing with respect to the metal magnetic powder may be 24% or more and 86% or less, 39% or more and 86% or less, and 39% or more and 81% or less in terms of an area ratio.
By making the ratio of the large size power existing in the metal magnetic powder to 39% or more in terms of an area ratio, the permeability of the magnetic core improves. Also, the withstand voltage can be suitably maintained. Further, change in the permeability is small with respect to the change of a ratio of the large size powder existing in the magnetic powder, thus the permeability is maintained good.
In the present embodiment, in an arbitrary cross section of the magnetic core 10, a ratio of the intermediate size powder existing with respect to the metal magnetic powder may be 8% or more and 39% or less, 8% or more and 31% or less, and 10% or more and 31% or less in terms of an area ratio.
In the present embodiment, the small size powder preferably includes permalloy and 30% or more of the small size powder in terms of a number of the small size powder may include permalloy. The permeability further improves by including permalloy in the small size powder.
In the present embodiment, in an arbitrary cross section of the magnetic core 10, a ratio of the small size powder existing with respect to the metal magnetic powder may be 7% or more and 35% or less, 7% or more and 28% or less, and 9% or more and 28% or less in terms of an area ratio.
Note that, the large size powder, the intermediate size powder, and the small size powder may all include the nano crystal, and a content ratio of the metal magnetic powder of the magnetic core 10 tends to easily decrease and also the permeability tends to easily decrease. Also, the nano crystal is expensive, therefore preferably the metal magnetic powder including the nano crystal and the metal magnetic powder which does not include the nano crystal are included at the same time. Specifically, a ratio of the metal magnetic powder including the nano crystal in terms of a weight ratio is preferably 40 wt % to 90 wt %.
Permalloy of the present embodiment is Ni—Fe based alloy and it is an alloy including 28 wt % or more of Ni and the rest made of Fe and other elements. A content of other elements is not particularly limited and it is 8 wt % or less when the Ni—Fe alloy is 100 wt %.
Note that, a content ratio of Ni in permalloy is preferably 40 to 85 wt %, and particularly preferably 75 to 82 wt %. An initial permeability improves and the core loss decreases by having the content ratio of Ni within the above mentioned range.
A content ratio of the metal magnetic powder in the metal magnetic powder containing resin is preferably 90 to 99 wt %, and more preferably 95 to 99 wt %. When the amount of the metal magnetic powder is decreased with respect to the resin, the saturation magnetic flux density and the permeability decrease; and on the other hand, when the amount of the metal magnetic powder is increased, the saturation magnetic flux density and the permeability increase. Therefore, the saturation magnetic flux density and the permeability can be regulated by the amount of the metal magnetic powder.
The resin included in the metal magnetic powder containing resin functions as an insulation binder. As a material of the resin, liquid epoxy resin or powder epoxy resin is preferably used. Also, a content ratio of the resin is preferably 1 to 10 wt % and more preferably 1 to 5 wt %. Also, when the metal magnetic powder and the resin are mixed, preferably the metal magnetic powder containing resin solution is obtained using a resin solution. A solvent of the resin solution is not particularly limited.
Hereinafter, a method of producing the coil component 2 is described.
First, the inner conductor paths 12 and 13 having a spiral form are formed to the insulation board 11 by a plating method. A condition for plating is not particularly limited. Also, methods other than a plating method can be used.
Next, to both surfaces of the insulation board 11 formed with the inner conductor paths 12 and 13, the protective insulation layer 14 is formed. A method of forming the protective insulation layer 14 is not particularly limited. For example, the insulation board 11 is immersed in the resin solution diluted with a high boiling point solvent and then it is dried, thereby the protective insulation layer 14 can be formed.
Next, the magnetic core 10 made of the upper core 15 and the lower core 16 shown in
The metal magnetic powder of the present embodiment is produced by mixing a plurality of metal magnetic powders having a different particle size distribution. Here, by regulating the particle size distribution, a mixing ratio, and the like of the plurality of metal magnetic powders, the cross section area ratio of the large size powder, the intermediate size powder, and the small size powder of the magnetic core 10 obtained at the end can be regulated.
One example of relatively easily regulating the cross section area ratio of the large size powder, the intermediate size powder, and the small size powder of the magnetic core 10 is described. In this method, a metal magnetic powder which will mainly become the large size powder, a metal magnetic powder which will mainly become the intermediate size powder, and a metal magnetic powder which will mainly become the small size powder in the magnetic core 10 obtained at the end are prepared separately. In this case, in order to sufficiently minimize a variation of the particle size of each metal magnetic powder, D50 of the metal magnetic powder which will mainly become the large size powder is set to 15 to 40 μm, D50 of the metal magnetic powder which will mainly become the intermediate size powder is set to 3.0 to 8.0 μm, and D50 of the metal magnetic powder which will mainly become the small size powder is set to 0.5 to 1.5 μm.
When D50 of each metal magnetic powder is within the above mentioned range, difference between a weight ratio of the large size powder included in the metal magnetic powder as the raw material and a cross section area ratio of the large size powder in the metal magnetic powder of the magnetic core 10 obtained at the end can be within about ±1%. For example, when the weight ratio of the large size powder is 40 wt %, the cross section area ratio of the large size powder at an arbitrary cross section of the magnetic core 10 can be 39 to 41%.
The large size powder, the intermediate size powder, and the small size powder are preferably spherical shape. In the present embodiment, specifically a spherical shape refers to a case having a spherical degree of 0.9 or more. Also, the spherical degree can be measured by a dynamic image analysis particle size analyzer.
Further, a method of producing the metal magnetic powder including the nano crystal (particularly the Fe-based nano crystal) is described. The method of producing the metal magnetic powder including the nano crystal (particularly the Fe-based nano crystal) is not particularly limited and from the point of easily making the metal magnetic powder including the nano crystal (particularly the Fe-based nano crystal) into a spherical shape, preferably it is produced by a gas atomization method.
In the gas atomization method, first, pure metal of each metal element included in the metal magnetic powder obtained at the end is prepared and weighed so that the metal magnetic powder obtained at the end has the same composition. Then, the pure metal of each metal element is melted and mixed to produce a mother alloy. Note that, a method of melting the pure metal is not particularly limited and for example, a method of melting at high frequency heat at inside of a chamber which has been vacuumed may be mentioned. Note that, the mother alloy and a soft magnetic alloy obtained at the end have the same composition. Next, the produced mother alloy is heated and melted to obtain a molten metal (molten). A temperature of the molten metal is not particularly limited, and for example it can be 1200 to 1500° C.
Then, the molten is injected into the chamber thereby the metal magnetic powder is produced. The particle size distribution of the metal magnetic powder can be regulated by a method usually used in a gas atomization method. Here, preferably a gas injection temperature is 50 to 200° C. and a vapor pressure inside the chamber is preferably 4 hPa or less. This is because the metal magnetic powder including the Fe-based nano crystal can be easily obtained by a heat treatment mentioned in below. At this point, the metal magnetic powder may only consist of amorphous or the metal magnetic powder may have a nanohetero structure. The nanohetero structure in the present embodiment refers to a structure wherein a nano crystal having a particle size of 30 nm or less exist in the amorphous.
Next, a heat treatment is carried out to the metal magnetic powder produced. When the metal magnetic powder is only consisted of amorphous, the heat treatment must be carried out; but if the metal magnetic powder has a nanohetero structure, then the heat treatment does not necessarily have to be carried out. This is because the metal magnetic powder already includes the nano crystal.
For example, by carrying out a heat treatment at 400 to 600° C. for 0.5 to 10 minutes, the metal magnetic powders sinter and prevent the powders from becoming large while promoting a diffusion of the elements. Further, it can be reached to thermodynamic equilibrium in short period of time thus strain and stress can be removed. As a result, the metal magnetic powder including the Fe-based nano crystal can be obtained easily. Note that, the metal magnetic powder including the Fe-based nano crystal after the heat treatment may or may not include amorphous.
Also, a method of calculating the average particle size of the Fe-based nano crystal included in the metal magnetic powder obtained by the heat treatment is not particularly limited. For example, it can be calculated by observing with a transmission electron microscope. Also, a method of verifying bcc (body centered cubic structure) of the crystal structure is not particularly limited. For example, it can be verified using X-ray diffraction measurement.
Next, a solvent portion of the metal magnetic powder containing resin solution coated by printing is evaporated to form the magnetic core 10.
Further, a density of the magnetic core 10 is improved. A method of improving the density of the magnetic core 10 is not particularly limited, and for example, a method by press treatment may be mentioned.
Further, the upper face 11a and the lower face 11b of the magnetic core 10 are ground so that the magnetic core 10 has a predetermined thickness. Then, the resin is thermoset to crosslink. A method of grinding is not particularly limited, and for example a method of using a fixed grinding stone may be mentioned. Also, the temperature and time for thermosetting is not particularly limited, and it may be regulated accordingly depending on a type of the resin and the like.
Then, the insulation board 11 formed with the magnetic core 10 is cut into dices. A method of cutting is not particularly limited, and for example, a method of dicing may be mentioned.
According to the above method, the magnetic core 10 before forming the terminal electrode 4 shown in
Also, after cutting, the diced magnetic core 10 is subjected to an etching treatment. An etching condition is not particularly limited.
Next, an electrode material forming an inner layer 4a is prepared. A type of the electrode material is not particularly limited. For example, a conductive powder containing resin may be mentioned which contain a conductive powder such as Ag powder and the like in a thermosetting resin such as epoxy resin similar to the epoxy resin used for the above mentioned metal magnetic powder containing resin. In case of using the conductive powder containing resin as the electrode material, the electrode material is coated to both ends in X-axis direction of the magnetic core 10 carried out with the etching treatment and heated to cure the thermosetting resin, thereby the inner layer 4a is formed.
Next, the product formed with the inner layer 4a is carried out with a contact plating by a barrel plating and the outer layer 4b is formed. The outer layer 4b may be a multilayer structure of 2 layers or more. A method for forming the outer layer 4b and the material of the outer layer 4b are not particularly limited and it may be formed for example by plating Ni on the inner layer 4a, then further plating Sn on Ni plating. The coil component 2 can be produced by the above mentioned method.
In the present embodiment, the magnetic core 10 is constituted by the metal magnetic powder containing resin thus a resin exists between the metal magnetic powders and fine gaps are formed; thereby the saturation magnetic flux density can be increased. Therefore, the magnetic saturation can be prevented without forming air gaps between the upper core 15 and the lower core 16. Therefore, there is no need to mechanically process the magnetic core with high precision to form gaps.
Further, the coil component 2 according to the present embodiment is formed as a collective body on the board surface, thereby the position of the coil is highly precise and can be made more compact and thinner. Further, in the present embodiment, the metal magnetic material is used in the magnetic body and it has better DC superimposition property than ferrite, thus process to form magnetic gaps can be omitted.
Note that, the present invention is not to be limited to the above mentioned embodiment, and can be variously modified within the scope of the present invention. For example, even in case of embodiments other than a coil component shown in
Hereinafter, the present invention is described based on the examples.
A toroidal core was produced to evaluate properties of a metal magnetic powder containing resin of a coil component according to the present invention. Hereinafter, a method of producing the toroidal core is described.
First, a large diameter powder 1, an intermediate size powder 1, and a small size powder 1 were prepared which were included in a metal magnetic powder in order to produce the metal magnetic powder included in the toroidal core.
First, as the large size powder 1 and the intermediate size powder 1, a nano crystal alloy powder having a composition of Fe:79.9 at %, Cu:0.1 at %, Nd:7.0 at %, B: 10.0 at %, P:3.0 at %, and S:0.1 at % was prepared. Note that, the total of the above composition does not add up to 100.0 at % since the composition was rounded off to one decimal places.
A method of producing a nano crystal alloy powder used for the large size powder 1 and the intermediate size powder 1 is described.
First, a raw material metal was weighed so that it satisfied the above alloy composition. Then, it was melted by high frequency heating thereby a mother alloy was produced.
Then, the produced mother alloy was heated and melted to form a metal in a melted state of 1250° C. Then, the metal was injected by a gas atomization method to form powder. A gas injection temperature was 150° C., a vapor pressure inside a chamber was 3.8 hPa. Also, the vapor pressure was adjusted by using Ar gas which was dew point adjusted. Also, a particle size distribution was regulated so that D50 was as shown in Tables 2 to 5.
Then, for each powder, a heat treatment was performed at 500° C. for 5 minutes to produce a nano crystal alloy powder.
As the small size powder 1, permalloy powder (Ni content ratio 78.5 wt %) was prepared. Note that, D50 of the small size powder 1 was 0.7 μm.
Next, the above mentioned large size powder 1, the intermediate size powder 1, and the small size powder 1 were carried out with coating.
The metal magnetic powders were coated by forming an insulation coating made of glass including SiO2 (hereinafter, it may be simply referred as a glass coating). The glass coating was formed by spraying a solution including SiO2 to the metal magnetic powder. Note that, the average thickness A1, A2, and A3 (average insulation coating thickness) of the glass coating was set to satisfy the thickness shown in Table 1 and Table 2. Also, STEM was used to confirm that the average insulation coating thickness satisfied the thickness shown in Table 1 and Table 2.
Then, the large size powder 1, the intermediate size powder 1, and the small size powder 1 were mixed so that the blending ratio satisfied the weight ratio shown in Table 1 and Table 2; thereby the metal magnetic powder was made. Note that, in Table 1 and Table 2, L1 represents the large size powder 1, M1 represents the intermediate size powder 1, and S1 represents the small size powder 1.
Further, the metal magnetic powder containing resin was produced by kneading the metal magnetic powder with epoxy resin. A weight ratio of the metal magnetic powder formed with an insulation coating in the metal magnetic powder containing resin was 97.5 wt %. Note that, as the epoxy resin, phenol novolac type epoxy resin was used.
Further, the obtained metal magnetic powder containing resin was filled into a metal mold having a predetermined toroidal shape and it was heated at 100° C. for 5 hours to evaporate a solvent component. Then, a pressing treatment was performed at a pressure of 3 t/cm2 and grinding was carried out using a fixed grinding stone so that a thickness was uniformly 0.7 mm. Then, the epoxy resin was crosslinked by thermosetting at 170° C. for 90 minutes, thereby a toroidal core (outer diameter of 15 mm, inner diameter of 9 mm, and thickness of 0.7 mm) was obtained.
Also, the obtained metal magnetic powder containing resin was filled into a metal mold having a predetermined rectangular parallelepiped shape. As similar to a method of forming the toroidal core, the magnetic material of rectangular parallelepiped shape (4 mm×4 mm×1 mm) was obtained. Further, at both ends of each surface having a size of 4 mm×4 mm of the rectangular parallelepiped shape magnetic material, terminal electrodes having a width of 1.3 mm was provided. A distance between the terminal electrodes were 1.4 mm.
Next, a ratio of a large size powder 2, an intermediate size powder 2, and a small size powder 2 existing in the obtained toroidal core was measured. Note that, in Table 1 and Table 2, L2 represents the large size powder 2, M2 represents the intermediate size powder 2, and S2 represents the small size powder 2.
The obtained toroidal core was cut at an arbitrary cross section, and the cross section was observed in an observation field of 0.128 mm×0.96 mm at a magnification of 1000× using SEM. Then, in the cross section, a powder having a particle size (circle equivalent diameter) of 10 μm or more and 60 μm or less was considered as the large size powder 2; a powder having a particle size of 2.0 μm or more and less than 10 μm was considered as the intermediate size powder 2; and a powder having a particle size of 0.1 μm or more and less than 2.0 μm was considered as the small size powder 2. Then, an area ratio (cross section area ratio) of the large size powder 2, the intermediate size powder 2, and the small size powder 2 at the cross section was verified. Note that, for calculating the area ratio, five different observation fields were identified and the area ratio of each powder in each observation field was calculated, then an average was calculated. Results are shown in Table 1 and Table 2.
Also, regarding all samples shown in Table 1 and Table 2, it was confirmed using SEM/EDS that at least 30% or more of the large size powder 2 in terms of number of the large size powder was derived from the large size powder 1. Also, it was confirmed that at least 30% or more of the intermediate size powder 2 was derived from the intermediate size powder 1; and at least 30% or more of the small size powder 2 was derived from the small size powder 1.
Further, the cross section of each sample was observed using STEM at a magnification of 250000× to verify the average insulation coating thickness of the large size powder 2, the intermediate size powder 2, and the small size powder 2. Specifically, the thickness of the insulation coating 22 was measured by visually observing STEM images such as the STEM image of the large size powder 20a shown in
A coil was wound around the toroidal core and the initial permeability μi was evaluated. Results are shown in Table 1 and Table 2.
A coil was wound around for 30 windings, and an inductance at a frequency of 1 MHz was measured using a LCR meter, thereby the initial permeability μi was calculated from the inductance. In the present examples, when μi was 35 or more, it was considered good; when μi was 40 or more, it was considered even better; when μi was 45 or more, it was considered particularly good; and when μi was 50 or more, it was considered excellent.
Further, voltage was applied to the terminal electrodes of the rectangular parallelepiped shape magnetic material, and the voltage was measured when current of 2 mA flew (withstand voltage), thereby an insulation breakdown intensity was measured. In the present examples, a withstand voltage of 650 V or more was considered good.
Sample No. 1 to 35 shown in Table 1 were examples and comparative examples in which A2=20 nm, A3=40 nm, and varied A1. Further,
All of the examples shown in Table 1 had good μi and withstand voltage. Further, according to
Further, according to
Sample No. 11 to 15 and 41 to 65 shown in Table 2 are examples and comparative examples in which A1=30 nm, A2=20 nm, and varied A3. Further,
All of the examples shown in Table 2 had good μi and withstand voltage. Further, according to
Further, according to
The magnetic core shown in
| Number | Date | Country | Kind |
|---|---|---|---|
| 2018-205404 | Oct 2018 | JP | national |
