Patent Application
20170229223
The present disclosure relates to multilayer coil components and, more particularly, to a multilayer coil component including a non-magnetic layer.
When copper is used as an inner conductor of a multilayer coil component, a copper conductor and a ferrite material (magnetic material) need to be fired simultaneously in a reducing atmosphere in which copper is not oxidized. Firing in such a condition causes, for example, a problem in that Fe3+ in the ferrite material is reduced to Fe2+, which lowers the specific resistance of the multilayer coil component. Therefore, a conductor containing silver as a main component has been commonly used. However, it is preferred to use a conductor containing copper as a main component because of low resistance, a lower cost than silver, and low possibility of electrochemical migration.
International Publication No. WO 2014/050867 discloses a multilayer coil component including a coiled conductive part containing copper as a main component and a magnetic part having a Cu content of 5 mol % or less in terms of CuO and having an Fe content of 25 to 47 mol % in terms of Fe2O3 and a Mn content of 1 mol % or more and less than 7.5 mol % in terms of Mn2O3 or having an Fe content of 35 to 45 mol % in terms of Fe2O3 and a Mn content of 7.5 to 10 mol % in terms of Mn2O3. According to the ferrite material containing these components, oxidation of Cu or reduction of Fe2O3 is supposed to be prevented or reduced even when the ferrite material is fired simultaneously with a Cu-based material.
Multilayer coil components are compact and lightweight. However, multilayer coil components commonly have a problem associated with lower rated current than wire wound coil components because the flow of large direct current causes a magnetic body to undergo magnetic saturation and thus reduces inductance. Therefore, there is a need to increase the saturation magnetic flux density of multilayer coil components, in other words, to improve the DC superposition characteristics of multilayer coil components (to obtain stable inductance over a wide range of direct current).
International Publication No. WO 2014/050867, the DC superposition characteristics are improved by forming a non-magnetic layer to provide an open magnetic path in an aspect of the multilayer coil component. This non-magnetic layer is formed of a Zn—Cu-based ferrite material obtained by replacing, with Zn, all of Ni in a Ni—Cu—Zn-based ferrite material, which is used for a magnetic layer.
Studies carried out by the inventors of the present disclosure reveal that a non-magnetic ferrite material having a high Zn content has low specific resistance and provides a multilayer coil component with a low Q value when the non-magnetic ferrite material has been fired in a reducing atmosphere.
The studies further reveal that, when the oxygen partial pressure during firing shifts to a value lower than a set value to create a reducing atmosphere, there are problems in that the multilayer coil component has lower specific resistance, and plating grows to a non-magnetic part when applying plating to an outer electrode. For example, when a large firing furnace is used in scaled-up processes, it is difficult to make the atmosphere in the firing furnace uniform, which may cause variations in oxygen partial pressure in the firing furnace. In this case, a multilayer coil component having low specific resistance is accordingly obtained at a location where the oxygen partial pressure is lower than a set value.
An object of the present disclosure is to provide a multilayer coil component having high specific resistance even after having been fired at a low oxygen partial pressure.
As a result of intensive studies to solve the above-mentioned problems, the inventors of the present disclosure have found that the specific resistance can be improved by adding a predetermined amount of vanadium to a non-magnetic part and adjusting the amounts of other components, such as iron, zinc, manganese, and copper, completing the present disclosure.
According to one aspect of the present disclosure, a multilayer coil component includes a multilayer body including a magnetic part, a non-magnetic part, and a coil conductor, and an outer electrode that is formed on an outer surface of the multilayer body and is electrically coupled to the coil conductor.
The non-magnetic part has
an Fe content of 36.0 to 48.5 mol % in terms of Fe2O3,
a Zn content of 46.0 to 57.5 mol % in terms of ZnO,
a V content of 0.5 to 5.0 mol % in terms of V2O5,
a Mn content of 0 to 7.5 mol % in terms of Mn2O3, and
a Cu content of 0 to 5.0 mol % in terms of CuO
with respect to the sum of the Fe content in terms of Fe2O3, the Zn content in terms of ZnO, the V content in terms of V2O5, and if present, the Cu content in terms of CuO, and the Mn content in terms of Mn2O3.
According to the present disclosure, a multilayer coil component having high specific resistance even after having been fired at a low oxygen partial pressure is provided when a non-magnetic part has an Fe content of 36.0 to 48.5 mol % in terms of Fe2O3, a Zn content of 46.0 to 57.5 mol % in terms of ZnO, a Mn content of 0 to 7.5 mol % in terms of Mn2O3, and a Cu content of 0 to 5.0 mol % in terms of CuO, and a V content of 0.5 to 5.0 mol % in terms of V2O5.
A multilayer coil component of the present disclosure and a method for producing the multilayer coil component will be described below in detail with reference to the drawings. It should be understood that the structure, the shape, the number of coiling, the configuration, or the like of the multilayer coil component of the present disclosure are not limited to those in the examples illustrated in the figures.
As illustrated in
The magnetic layer 6 is formed of a sintered ferrite that contains Fe, Zn, and Ni and may further contain Mn, Cu, and/or V as desired.
The non-magnetic layer 8 is formed of a sintered ferrite that contains Fe, Mn, and V and may further contain Zn and/or Cu as desired.
The conductive part 3 is formed of a conductor containing a conductive metal, preferably formed of a conductor containing copper or silver as a main component, and more preferably formed of a conductor containing copper as a main component. The main component in the conductor refers to a component present in the largest amount in the conductor. The main component may be, for example, a component present in an amount of 50% by mass or more, preferably 80% by mass or more, more preferably 90% by mass or more, for example, 95% by mass or more, 98% by mass or more, or 99% by mass or more with respect to the entire conductor. In a preferred embodiment, the conductor is composed substantially of copper or silver, and preferably composed substantially of copper.
The metal layers 12 of the outer electrodes 5a and 5b are formed of any conductive metal, but are normally formed of a conductor containing copper or silver as a main component and preferably formed of a conductor containing copper as a main component. The Ni layer 14 has a function of protecting the outer electrode from solder. The Sn layer 16 has a function of improving soldering. In the present disclosure, the Ni layer 14 and the Sn layer 16 are optional and not necessarily present.
The multilayer coil component 1 according to this embodiment is produced in the following manner.
First, a magnetic ferrite material is prepared. The composition of the magnetic ferrite material is not limited. The magnetic ferrite material preferably contains Fe, Zn, and Ni and may further contain Mn, Cu, and/or V as desired.
In an embodiment, the magnetic ferrite material contains Fe, Mn, Zn, Ni, and Cu as main components. The magnetic ferrite material may be normally prepared by mixing Fe2O3, Mn2O3, ZnO, NiO, and CuO powders, which are raw materials of the main components, at a desired ratio, and calcining the mixture. The method for preparing the magnetic ferrite material is not limited to this method.
In this magnetic ferrite material, the Fe content (in terms of Fe2O3) is 25 mol % or more and 47 mol % or less and the Mn content (in terms of Mn2O3) is 1 mol % or more and less than 7.5 mol %, or the Fe content (in terms of Fe2O3) is 35 mol % or more and 45 mol % or less and the Mn content (in terms of Mn2O3) is 7.5 mol % or more and 10 mol % or less. That is, the composition of the magnetic ferrite material is within the range of the area Z illustrated in
The Zn content (in terms of ZnO) in the magnetic ferrite material is preferably 6 to 33 mol % (based on the total main components). A Zn content (in terms of ZnO) of 6 mol % or more results in high magnetic permeability and large inductance. A Zn content (in terms of ZnO) of 33 mol % or less allows the magnetic ferrite material to have a high Curie point (e.g., 130° C. or higher) and ensures a high coil operating temperature.
The Cu content (in terms of CuO) in the magnetic ferrite material is preferably 5 mol % or less (based on the total main components). A Cu content (in terms of CuO) of 5 mol % or less allows the magnetic layer 6 to have high specific resistance. Copper in the magnetic ferrite material is an optional component, and the Cu content may be zero. The Cu content (in terms of CuO) may be 5 mol % or less, and preferably 0.2 mol % or more to obtain a sufficient degree of sintering.
The Ni content (in terms of NiO) in the magnetic ferrite material is not limited, and the Ni content may be the remainder after deduction of Fe, Mn, Zn, and Cu, which are other main components described above.
In another embodiment, the magnetic ferrite material contains Fe, Zn, Ni, and V, and may further contain Mn and/or Cu as desired. The magnetic ferrite material is normally prepared by mixing Fe2O3, ZnO, NiO, V2O5, Mn2O3, and CuO powders, which are raw materials of the main components, at a desired ratio, and calcining the mixture. The method for preparing the magnetic ferrite material is not limited to this method.
The Fe content (in terms of Fe2O3) in the magnetic ferrite material is preferably 36.0 to 48.5 mol % (based on the total main components). An Fe content (in terms of Fe2O3) of 48.5 mol % or less allows the reduction of Fe3+ to Fe2+ to be suppressed and causes a decrease in specific resistance to be prevented or reduced. An Fe content (in terms of Fe2O3) of less than 36.0 mol % rather causes the specific resistance to be reduced, which results in a failure to ensure electrical insulation. The Fe content is thus preferably 36.0 mol % or more.
The Zn content (in terms of ZnO) in the magnetic ferrite material is preferably 6.0 to 45.0 mol % (based on the total main components). A Zn content (in terms of ZnO) of 6.0 mol % or more results in high magnetic permeability and large inductance. A Zn content (in terms of ZnO) of 45.0 mol % or less can avoid a decrease in Curie point and avoid a decrease in the operating temperature of the multilayer coil component.
The V content (in terms of V2O5) in the magnetic ferrite material is preferably 0.5 to 5.0 mol % (based on the total main components). Firing the multilayer body when the V content (in terms of V2O5) is 0.5 to 5.0 mol % can improve specific resistance and can further reduce variations in specific resistance among multilayer coil components.
The magnetic ferrite material may further contain Cu. The Cu content (in terms of CuO) in the magnetic ferrite material is preferably 0 to 5.0 mol % (based on the total main components). Copper is an optional component, and the Cu content may be zero. In an embodiment, the Cu content (in terms of CuO) in the magnetic ferrite material is 0.1 to 5.0 mol %. Firing the multilayer body in which the magnetic ferrite material contains Cu can improve DC superposition characteristics and can reduce a change in magnetic properties obtained when the multilayer body is subjected to thermal shock testing.
The magnetic ferrite material may further contain Mn. The Mn content (in terms of Mn2O3) in the magnetic ferrite material is preferably 0 to 7.5 mol % (based on the total main components). Manganese is an optional component, and the Mn and Cu contents may be zero. In an embodiment, the Mn content (in terms of Mn2O3) in the magnetic ferrite material is 0.1 to 7.5 mol %. The addition of Mn to the magnetic ferrite material allows the magnetic body to have low magnetic coercive force and thus increases magnetic flux density, which improves magnetic permeability. The addition of Mn also causes the reduction of Mn more preferentially than the reduction of Fe, which can avoid a decrease in specific resistance due to the reduction of Fe.
The Ni content (in terms of NiO) in the magnetic ferrite material is not limited, and the Ni content may be the remainder after deduction of Fe, Zn, V, Cu, and Mn, which are other main components described above.
In the present disclosure, the magnetic ferrite material may further contain additives. Examples of the additives in the magnetic ferrite material include, but are not limited to, Bi. The Bi content (addition amount) in terms of Bi2O3 is preferably 0.1 to 1 part by weight with respect to 100 parts by weight of the total main components (Fe (in terms of Fe2O3), Zn (in terms of ZnO), V (in terms of V2O5), Cu (in terms of CuO), Mn (in terms of Mn2O3), and Ni (in terms of NiO)). A Bi content (in terms of Bi2O3) of 0.1 to 1 part by weight causes low-temperature firing to be promoted and allows abnormal grain growth to be prevented or reduced. An excessive Bi content (in terms of Bi2O3) is not preferred because such a Bi content tends to cause abnormal grain growth. The specific resistance is low at abnormal grain growth sites, and a plating is attached to the abnormal grain growth sites when plating is performed to form the outer electrodes.
With respect to the magnetic part before and after sintering, for example, part of CuO and Fe2O3, which form the magnetic ferrite material before sintering, may be respectively converted into Cu2O and Fe3O4 by firing. However, the amounts of the main components in the magnetic part after sintering, such as the Cu content in terms of CuO and the Fe content in terms of Fe2O3, are respectively considered substantially equal to the amounts of the main components in the magnetic ferrite material before sintering, such as the CuO content and the Fe2O3 content.
A magnetic sheet is prepared by using the magnetic ferrite material. For example, a magnetic sheet may be obtained as follows: mixing/kneading the magnetic ferrite material with an organic vehicle containing a binder resin and an organic solvent; and forming the mixture into a sheet. The method for preparing the magnetic sheet is not limited to this method. Separately, a non-magnetic ferrite material is prepared. The non-magnetic ferrite material contains Fe, Zn, and V, and may further contain Mn and/or Cu as desired. The non-magnetic ferrite material is normally prepared by mixing Fe2O3, ZnO, V2O5, Mn2O3, and CuO powders, which are raw materials of the main components, at a desired ratio, and calcining the mixture. The method for preparing the non-magnetic ferrite material is not limited to this method.
The Fe content (in terms of Fe2O3) in the non-magnetic ferrite material is 36.0 to 48.5 mol % (based on the total main components). An Fe content (in terms of Fe2O3) of 48.5 mol % or less allows the reduction of Fe3+ to Fe2+ to be suppressed and causes a decrease in specific resistance to be prevented or reduced. An Fe content (in terms of Fe2O3) of less than 36.0 mol % rather causes the specific resistance to be reduced, which results in a failure to ensure electrical insulation. The Fe content is thus preferably 36.0 mol % or more.
The V content (in terms of V2O5) in the non-magnetic ferrite material is 0.5 to 5.0 mol % (based on the total main components). The V content (in terms of V2O5) is preferably 0.5 mol % or more and less than 4.0 mol %, more preferably 0.5 to 3.5 mol %, and still more preferably 0.5 to 3.0 mol %. Firing the multilayer body in which the V content (in terms of V2O5) in the non-magnetic ferrite material is 0.5 to 5.0 mol % can improve specific resistance and can further reduce variations in specific resistance among multilayer coil components.
The Zn content (in terms of ZnO) in the non-magnetic ferrite material is 46.0 to 57.5 mol % (based on the total main components).
In the present disclosure, the non-magnetic ferrite material may further contain Cu. The Cu content (in terms of CuO) in the ferrite material is 0 to 5.0 mol % (based on the total main components). Copper is an optional component, and the Cu content may be zero. In an embodiment, the Cu content (in terms of CuO) in the ferrite material is 0.1 to 5.0 mol %. Firing the multilayer body in which the ferrite material contains Cu provides a high degree of sintering. A Cu content (in terms of CuO) of 5 mol % or less results in reduced production of a different phase (CuO phase) and suppresses a decrease in the specific resistance of the non-magnetic part.
In the present disclosure, the non-magnetic ferrite material may further contain Mn. The Mn content (in terms of Mn2O3) in the ferrite material is 0 to 7.5 mol % (based on the total main components). Manganese is an optional component, and the Mn content may be zero. In an embodiment, the Mn content (in terms of Mn2O3) in the ferrite material is 0.1 to 7.5 mol %. Since Mn is more preferentially reduced than Fe when Mn is added, a decrease in specific resistance due to the reduction of Fe can be avoided.
With regard to the non-magnetic part before and after sintering, for example, part of CuO and Fe2O3, which form the non-magnetic ferrite material before sintering, may be respectively converted into Cu2O and Fe3O4 by firing. However, the amounts of the main components in the non-magnetic part after sintering, such as the Cu content in terms of CuO and the Fe content in terms of Fe2O3, are respectively considered substantially equal to the amounts of the main components in the non-magnetic ferrite material before sintering, such as the CuO content and the Fe2O3 content.
A non-magnetic sheet is prepared by using the non-magnetic ferrite material. For example, the non-magnetic sheet may be obtained as follows: mixing/kneading the non-magnetic ferrite material with an organic vehicle containing a binder resin and an organic solvent; and forming the mixture into a sheet. The method for preparing the non-magnetic sheet is not limited to this method.
Separately, a conductive paste is prepared. The conductive paste is preferably, but not necessarily, for example, a paste containing silver or copper and more preferably a paste containing copper. For example, a commercially available ordinary copper paste containing copper in a powder form may be used, but the conductive paste is not limited to this paste.
Next, a multilayer body is obtained by stacking the magnetic sheets and the non-magnetic sheets with conductive paste layers each interposed therebetween such that the conductive paste layers are connected to each other in a coiled manner through via-holes that penetrate through the magnetic sheets and the non-magnetic sheets.
A method for forming the multilayer body is not limited, and the multilayer body may be formed by using, for example, a sheet lamination method or a printing lamination method. In the sheet lamination method, a multilayer body can be obtained as follows: appropriately making via-holes in the magnetic sheets or the non-magnetic sheets; applying a conductive paste in a predetermined pattern to form conductive paste layers (while filling the via-holes with the conductive paste when the via-holes are present); stacking and pressure-bonding the magnetic sheets and the non-magnetic sheets on each of which the conductive paste layer has been formed appropriately; and cutting into a predetermined size. In the printing lamination method, a multilayer body can be obtained as follows: applying a magnetic ferrite paste, a non-magnetic ferrite paste, and a conductive paste in a predetermined order to a substrate, such as PET (polyethylene terephthalate) film, by using the magnetic ferrite material and the non-magnetic ferrite as pastes; appropriately repeating formation of the magnetic paste layer, the non-magnetic paste layer, and the conductive paste layer; and finally cutting into a predetermined size. This multilayer body may be prepared by once producing a matrix of plural multilayer bodies and then separating them into individual pieces (element isolation) with a dicing machine or the like or may be prepared individually in advance.
Next, the magnetic sheets and the conductive paste layers are fired by subjecting the unfired multilayer body obtained as described above to a heat treatment at a predetermined oxygen partial pressure, which provides magnetic layers 6, non-magnetic layers 8, and conductive layers 10. In the multilayer body 2 thus obtained, the magnetic layers 6 form magnetic parts, the non-magnetic layers 8 form non-magnetic parts, and the conductive layers form the conductive part 3.
The oxygen partial pressure during such firing is not limited. When the conductive part contains Cu as a main component, the oxygen partial pressure is preferably the Cu—Cu2O equilibrium oxygen partial pressure or less (reducing atmosphere), and more preferably the Cu—Cu2O equilibrium oxygen partial pressure. The heat treatment of the unfired multilayer body at such an oxygen partial pressure can avoid oxidation of Cu in the conductive part and also allows the unfired multilayer body to be sintered at a temperature lower than the temperature in the case of a heat treatment in the air. The firing temperature may be, for example, 950° C. to 1100° C. The present disclosure is not restricted by any theory. When firing is performed in a low oxygen concentration atmosphere, oxygen defects are formed in the crystal structure, mutual diffusion of Fe, Zn, V, Cu, Mn, and Ni through these oxygen defects is promoted, which improves low-temperature sintering properties.
Next, outer electrodes 5a and 5b are formed on the end surfaces of the multilayer body 2 obtained as described above. The outer electrodes 5a and 5b may be formed by, for example, applying a paste containing a copper or silver powder, glass, and the like to a predetermined area, and subjecting the resulting structure to a heat treatment, for example, at 700° C. to 850° C. to bake copper or silver in an appropriate atmosphere, for example, in an atmosphere in which copper is not oxidized, when the conductive part contains Cu as a main component.
The multilayer coil component 1 according to this embodiment is produced as described above.
In the multilayer coil component of the present disclosure, the non-magnetic part contains vanadium and thus has high specific resistance and is less affected by variations in oxygen partial pressure in mass production, which results in a few variations in specific resistance, compared with a related non-magnetic layer free of vanadium. The present disclosure is not restricted by any theory, but the reasons why adding vanadium to the non-magnetic part improves specific resistance and reduces variations in specific resistance may be considered as described below. A decrease in specific resistance may result from the reduction of Fe3+ to Fe2+ and subsequent hopping conduction between B sites. When V (V2O5) is present here, V5+ is reduced to V4+ or V3+, and the presence of this V at B sites suppresses hopping conduction and thus improves specific resistance.
The specific resistance (log ρ) of the non-magnetic part in the multilayer coil component of the present disclosure may be preferably 4.5 ωcm or more, more preferably 4.8 ωcm or more, and still more preferably 5.0 ωcm or more.
In a preferred embodiment, the conductive part in the multilayer coil component of the present disclosure is formed of a conductor containing copper. The magnetic parts, the non-magnetic parts, and the conductive part in the multilayer coil component are simultaneously fired preferably at the Cu—Cu2O equilibrium oxygen partial pressure or less (in a reducing atmosphere). Firing at the Cu—Cu2O equilibrium oxygen partial pressure or less prevents oxidation of copper in the conductive part. When the non-magnetic part has a particular composition as described above, even simultaneous firing in a reducing atmosphere allows the non-magnetic part to maintain high specific resistance.
Although an embodiment of the present disclosure is described above, the present disclosure is not limited to this embodiment, and various modifications can be made.
To produce non-magnetic layers, Fe2O3, ZnO, V2O5, Mn2O3, and CuO powders were weighed so as to obtain the compositions with the ratios indicated by sample numbers 1 to 29 in Table 1. Sample numbers 2 to 7, 10 to 16, 19 to 24, and 26 to 28 correspond to Examples of the present disclosure, and sample numbers 1, 8, 9, 17, 18, 25, and 29 (with symbol “*” in Table) correspond to Comparative Examples.
Next, the weighed materials for each of sample numbers 1 to 29 were placed in a pot mill made of vinyl chloride together with pure water and PSZ (partial stabilized zirconia) balls, followed by sufficient wet grinding and mixing. The ground material was dried by evaporation and then calcined at a temperature of 750° C. for 2 hours. The calcined powder thus obtained was placed in the pot mill made of vinyl chloride again together with ethanol (organic solvent) and PSZ balls, followed by sufficient grinding and mixing. A polyvinyl butyral-based binder (organic binder) was further added, and the mixture was mixed well to obtain a ceramic slurry. Next, the obtained ceramic slurry was formed into a sheet having a thickness of 25 μm by a doctor blade method. The formed product thus obtained was punched out into a size of 50 mm in length and 50 mm in width to provide non-magnetic sheets made of a ferrite material.
Next, the non-magnetic sheets were stacked such that the thickness after firing was 0.5 mm, and were pressure-bonded at a pressure of 100 MPa and a temperature of 60° C. for 1 minute to produce a pressure-bonded block. The pressure-bonded block thus obtained was punched out with a dice into disk-shaped samples having a diameter of 10 mm and ring-shaped samples having an outer diameter of 20 mm and an inner diameter of 12 mm.
These samples were placed in a firing furnace and degreased well by heating to 400° C. in nitrogen. Next, the samples were fired at 1000° C. for 3 hours while the oxygen partial pressure was controlled at the Cu—Cu2O equilibrium oxygen partial pressure by using a N2—H2-H2O gas mixture.
To both sides of the disk-shaped sample thus obtained, a copper paste (copper paste for forming outer electrodes) containing a Cu powder, glass frit, varnish, and an organic solvent was applied and baked at 800° C. for 5 minutes in an atmosphere in which copper is not oxidized, forming electrodes.
A DC voltage of 50 V was applied across the electrodes, and the resistance after 1 minute was measured. Specific resistance log ρ (ω·cm) was obtained from this measured resistance and the sample size. The mean of 10 samples was calculated, and the results are shown in Table 2.
The ring-shaped sample was placed in a magnetic material test fixture (model: 16454 A-s) available from Agilent Technologies, Inc., and the initial magnetic permeability μ at 1 MHz was measured by using an impedance analyzer (model: E4991A) available from Agilent Technologies, Inc. The mean of 30 samples was calculated, and the results are shown in Table 2.
To produce magnetic layers, Fe2O3, Mn2O3, ZnO, NiO, and CuO powders were provided and weighed so as to obtain the composition with 46.5 mol % of Fe2O3, 2.5 mol % of Mn2O3, 30.0 mol % of ZnO, 20.0 mol % of NiO, and 1.0 mol % of CuO. These weighed materials were placed in a pot mill made of vinyl chloride together with pure water and PSZ balls, followed by sufficient wet grinding and mixing, as in Example 1. The ground material was dried by evaporation and then calcined at a temperature of 750° C. for 2 hours. The calcined powder thus obtained was placed in the pot mill made of vinyl chloride again together with ethanol (organic solvent) and PSZ balls, followed by sufficient wet grinding and mixing. A polyvinyl butyral-based binder (organic binder) was further added, and the mixture was mixed well to obtain a ceramic slurry.
Next, the obtained ceramic slurry was formed into a sheet having a thickness of 25 μm by a doctor blade method. The formed sheet was punched out into a size of 50 mm in length and mm in width to provide magnetic sheets made of a ferrite material.
Next, via-holes were formed, by using a laser beam machine, at predetermined positions in the non-magnetic sheets of sample numbers 1 to 27 produced in Example 1 and the magnetic sheets produced as described above. Subsequently, a coil pattern was formed by applying a Cu paste containing a Cu powder, varnish, and an organic solvent to the surface of each magnetic sheet by screen printing, and filling the via-holes with the Cu paste.
The non-magnetic sheets of any one of sample numbers 1 to 29 and the magnetic sheets thus produced were stacked so as to obtain the arrangement (including three layers of any one of sample numbers 1 to 29) as illustrated in
Some of the ceramic multilayer bodies thus produced were placed in a firing furnace and degreased well by heating to 400° C. in nitrogen. Next, the ceramic multilayer bodies were fired at 1000° C. for 3 hours while the oxygen partial pressure was controlled at the Cu—Cu2O equilibrium oxygen partial pressure by using a N2—H2-H2O gas mixture. Separately, the other ceramic multilayer bodies were fired similarly at an oxygen partial pressure of 0.1 times the Cu—Cu2O equilibrium oxygen partial pressure.
Next, the copper paste for forming outer electrodes used in Example 1 was applied to both sides of the fired ceramic multilayer body and dried. The copper paste was then baked at 800° C. for 5 minutes in an atmosphere in which copper is not oxidized. Furthermore, Ni plating and Sn plating were sequentially performed by electroplating to form outer electrodes having an electrode structure as illustrated in
The distance between the position of the end of the outer electrode and the furthest position to which the plating elongated was measured by observing the sample surfaces (two LT surfaces defined by the longitudinal dimension (L) and the thickness dimension (T)) of samples (n=10 for each sample) each having any one of the non-magnetic layers of sample numbers 1 to 29 through an optical microscope. The measurement was performed at three locations at which the non-magnetic layer was formed, namely, at six locations on both sides for each sample (n=10), so that a total of 120 pieces of data was obtained from each sample. A sample was rated A when the length of plating elongation was 100 μm or less at all locations, while a sample was rated B (poor) when the length of plating elongation was more than 100 μm at least one location. This evaluation was performed for the samples that had been fired at the Cu—Cu2O equilibrium oxygen partial pressure and the samples that had been fired at an oxygen partial pressure of 0.1 times the Cu—Cu2O equilibrium oxygen partial pressure. The results are all shown in Table 2.
As is apparent from the above description, the results in Example 1 indicate that the samples of sample numbers 2 to 7, 10 to 16, 19 to 24, and 26 to 28 within the scope of the present disclosure have a magnetic permeability of 1.0 and thus are non-magnetic. It is found that the non-magnetic layers within the scope of the present disclosure have a specific resistance log ρ as high as 4.5 or more even after having been fired at the Cu—Cu2O equilibrium oxygen partial pressure. It is also found that the samples of sample numbers 1, 8, 9, 17, 18, 25, and 29, in which at least one component in the non-magnetic ferrite material is out of the scope of the present disclosure, have a small specific resistance (log ρ of less than 4) or have magnetism.
The results in Example 2 indicate that the samples including the non-magnetic ferrite material within the scope of the present disclosure do not undergo a defect caused by plating elongation even after the samples have been fired at the Cu—Cu2O equilibrium oxygen partial pressure.
Furthermore, it is also found that, when the amount of V2O5 added is 0.5 mol % or more and less than 4.0 mol %, a defect caused by plating elongation does not occur even in the case of firing at an oxygen partial pressure of 0.1 times the Cu—Cu2O equilibrium oxygen partial pressure. This indicates that the multilayer coil component can be stably produced even when the oxygen partial pressure changes to a value lower than a set value to create a low-oxygen atmosphere during firing.
The multilayer coil component obtained in the present disclosure may be used, for example, in a wide range of applications of electronic devices.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2014-226305 | Nov 2014 | JP | national |
This application claims benefit of priority to Japanese Patent Application 2014-226305 filed Nov. 6, 2014, and to International Patent Application No. PCT/JP2015/081076 filed Nov. 4, 2015, the entire content of which is incorporated herein by reference.
| Number | Date | Country | |
|---|---|---|---|
| Parent | PCT/JP2015/081076 | Nov 2015 | US |
| Child | 15494965 | US |
