Patent Application
20190304646
The present invention relates to a soft magnetic powder and a method for producing a sintered body.
An Fe-based soft magnetic alloy containing Co has a high saturation magnetic flux density, and therefore is used for, for example, a component for an electromagnetic actuator.
For example, JP-A-2006-336038 (Patent Document 1) discloses a high magnetic flux density material containing Co at 48 to 52 mass % and V at 0.8 to 1.6 mass %, with the remainder being Fe and unavoidable impurities. In such a material, the deposition of crystal grains and brittle phases is suppressed, and therefore, the material has sufficient workability although it has a high magnetic flux density.
However, the high magnetic flux density material described in Patent Document 1 has a problem that the specific resistance is low. When the specific resistance is low, an eddy current easily flows in the material, and therefore, eddy current loss is likely to occur. Due to this, when the high magnetic flux density material is applied to, for example, a component for an electromagnetic actuator, there is a concern that the output of the electromagnetic actuator is decreased. Therefore, a high magnetic flux density material having a high specific resistance has been demanded.
An advantage of some aspects of the invention is to solve the above-mentioned problem and the invention can be implemented as the following application example.
A soft magnetic powder according to this application example contains Fe in a proportion of 45.0 mass % or more and 52.0 mass % or less, Co in a proportion of 47.0 mass % or more and 52.0 mass % or less, and V in a proportion of 0.10 mass % or more and less than 2.0 mass %, wherein in a mass-based particle size distribution measured by a laser diffraction particle size distribution analyzer, when a particle diameter at a cumulative frequency from a small diameter side of 10% is represented by D10, a particle diameter at a cumulative frequency of 50% is represented by D50, and a particle diameter at a cumulative frequency of 90% is represented by D90, (D90−D10)/D50 satisfies 1.0 or more and 3.5 or less.
The invention will be described with reference to the accompanying drawings, wherein like numbers reference like elements.
Hereinafter, preferred embodiments of a soft magnetic powder and a method for producing a sintered body according to the invention will be described in detail with reference to the accompanying drawings. In the respective drawings, some portions are displayed by being appropriately enlarged or reduced in size and some portions are schematically shown so that portions to be described are in a recognizable state.
A soft magnetic powder according to an embodiment contains Fe in a proportion of 45.0 mass % or more and 52.0 mass % or less, Co in a proportion of 47.0 mass % or more and 52.0 mass % or less, and V in a proportion of 0.10 mass % or more and less than 2.0 mass %. In the soft magnetic powder, in a mass-based particle size distribution measured by a laser diffraction particle size distribution analyzer, when a particle diameter at a cumulative frequency from a small diameter side of 10% is represented by D10, a particle diameter at a cumulative frequency of 50% is represented by D50, and a particle diameter at a cumulative frequency of 90% is represented by D90, (D90-D10)/D50 satisfies 1.0 or more and 3.5 or less.
According to such a soft magnetic powder, a powder having a sufficiently high saturation magnetic flux density is obtained. When a sintered body produced using such a soft magnetic powder is used for, for example, generating an electromagnetic force necessary for electromagnetic drive such as a component for a dot impact printer (recording device) or a component for an electromagnetic actuator, a high driving force is generated without causing an increase in the size of the component. On the other hand, according to such a soft magnetic powder, a powder having a sufficiently high specific resistance is obtained. Therefore, the specific resistance of a sintered body or a green compact can also be sufficiently increased, and an eddy current flowing therein can be suppressed. As a result, a decrease in the driving force due to the eddy current loss is suppressed, and the output in the entire device including the component can be enhanced.
Hereinafter, the alloy composition of the soft magnetic powder according to the embodiment will be described in more detail.
Fe (iron) has a great influence on the basic magnetic properties and mechanical properties of the soft magnetic powder.
The content of Fe is set to 45.0 mass % or more and 52.0 mass % or less, but is set to preferably 46.0 mass % or more and 51.0 mass % or less, more preferably 47.0 mass % or more and 50.5 mass % or less.
When the content of Fe is less than the above lower limit, the saturation magnetic flux density of the soft magnetic powder may be decreased or the mechanical properties of a sintered body may be deteriorated. On the other hand, when the content of Fe exceeds the above upper limit, the specific resistance of the soft magnetic powder may be decreased, the magnetic permeability may be decreased, or the coercivity may be increased.
Co (cobalt) mainly acts to increase the saturation magnetic flux density of the soft magnetic powder.
The content of Co is set to 47.0 mass % or more and 52.0 mass % or less, but is set to preferably 47.5 mass % or more and 51.5 mass % or less, more preferably 48.0 mass % or more and 50.0 mass % or less.
When the content of Co is less than the above lower limit, the specific resistance may be decreased, the coercivity may be increased, or the magnetic permeability may be decreased. On the other hand, when the content of Co exceeds the above upper limit, the saturation magnetic flux density of the soft magnetic powder may be decreased.
V (vanadium) mainly acts to increase the specific resistance of the soft magnetic powder.
The content of V is set to 0.10 mass % or more and less than 2.0 mass %, but is set to preferably 0.50 mass % or more and 1.6 mass % or less, more preferably 0.80 mass % or more and 1.2 mass % or less.
When the content of V is less than the above lower limit, the specific resistance of the soft magnetic powder may be decreased. On the other hand, when the content of V exceeds the above upper limit, the saturation magnetic flux density of the soft magnetic powder may be decreased.
The soft magnetic powder according to the embodiment may contain the following components as needed.
Si (silicon) mainly acts to increase the specific resistance of the soft magnetic powder. On the other hand, when Si is added, the workability of an alloy tends to decrease, however, according to a powder metallurgy technique using the soft magnetic powder, machining can be reduced, and therefore, an adverse effect of the addition of Si can be minimized.
The content of Si is preferably 4.0 mass % or less, more preferably 0.20 mass % or more and 2.5 mass % or less, further more preferably 0.50 mass % or more and 1.5 mass % or less.
When the content of Si is less than the above lower limit, the specific resistance of the soft magnetic powder may not be able to be sufficiently increased depending on the overall composition. On the other hand, when the content of Si exceeds the above upper limit, the saturation magnetic flux density may be decreased depending on the overall composition.
Cr (chromium) mainly acts to enhance the corrosion resistance of the soft magnetic powder.
The content of Cr is preferably 2.0 mass % or less, more preferably 0.10 mass % or more and 1.5 mass % or less, further more preferably 0.30 mass % or more and 1.2 mass % or less.
When the content of Cr is less than the above lower limit, the corrosion resistance of the soft magnetic powder may not be able to be sufficiently enhanced depending on the overall composition. On the other hand, when the content of Cr exceeds the above upper limit, the saturation magnetic flux density may be decreased depending on the overall composition.
Each of Ni (nickel) and Nb (niobium) mainly acts to enhance the mechanical properties of a sintered body.
The content of each of Ni and Nb is preferably 2.0 mass % or less, more preferably 0.10 mass % or more and 1.5 mass % or less, further more preferably 0.30 mass % or more and 1.2 mass % or less.
When the content of each of Ni and Nb is less than the above lower limit, the mechanical properties of a sintered body may not be able to be sufficiently enhanced depending on the overall composition. On the other hand, when the content of each of Ni and Nb exceeds the above upper limit, the saturation magnetic flux density may be decreased depending on the overall composition.
At least one of Mn (manganese), Al (aluminum), Mo (molybdenum), and W (tungsten) mainly acts to enhance the mechanical properties of a sintered body.
The content of Mn is preferably 1.0 mass % or less, more preferably 0.10 mass % or more and 0.80 mass % or less, further more preferably 0.30 mass % or more and 0.60 mass % or less.
The content of Al is preferably 2.0 mass % or less, more preferably 0.10 mass % or more and 1.6 mass % or less, further more preferably 0.30 mass % or more and 1.2 mass % or less.
The content of Mo is preferably 3.5 mass % or less, more preferably 0.10 mass % or more and 2.5 mass % or less, further more preferably 0.30 mass % or more and 2.0 mass % or less.
The content of W is preferably 1.0 mass % or less, more preferably 0.10 mass % or more and 0.80 mass % or less, further more preferably 0.30 mass % or more and 0.60 mass % or less.
When the content of each of Mn, Al, Mo, and W is less than the above lower limit, the mechanical properties of a sintered body may not be able to be sufficiently enhanced depending on the overall composition. On the other hand, when the content of each of Mn, Al, Mo, and W exceeds the above upper limit, the saturation magnetic flux density or the specific resistance may be decreased depending on the overall composition.
Hereinabove, the composition of the soft magnetic powder according to the invention is described in detail, however, this soft magnetic powder may contain any elements other than the above-mentioned elements. In such a case, the total content of the other elements is preferably 3.0 mass % or less, more preferably 2.0 mass % or less. Further, the content of each of the other elements is preferably 0.50 mass % or less, more preferably 0.30 mass % or less. When the content thereof is within such a range, the above-mentioned effects of the soft magnetic powder are not inhibited whether they are contained inevitably or intentionally, and therefore, the incorporation thereof is permitted.
The composition of the soft magnetic powder can be determined by, for example, Iron and steel—Atomic absorption spectrometric method specified in JIS G 1257 (2000), Iron and steel—ICP atomic emission spectrometric method specified in JIS G 1258 (2007), Iron and steel—Method for spark discharge atomic emission spectrometric analysis specified in JIS G 1253 (2002), Iron and steel—Method for X-ray fluorescence spectrometric analysis specified in JIS G 1256 (1997), gravimetry, titrimetry, and absorption spectroscopy specified in JIS G 1211 to G 1237, or the like. Specifically, for example, an optical emission spectrometer for solids (a spark emission spectrometer, model: Spectrolab, type: LAVMB08A) manufactured by SPECTRO Analytical Instruments GmbH or an ICP device (model: CIROS-120) manufactured by Rigaku Corporation is used.
Further, when C (carbon) and S (sulfur) are determined, particularly, an infrared absorption method after combustion in a stream of oxygen (after combustion in a high-frequency induction heating furnace) specified in JIS G 1211 (2011) is also used. Specifically, a carbon/sulfur analyzer, CS-200 manufactured by LECO Corporation is used.
Further, when N (nitrogen) and O (oxygen) are determined, particularly, Iron and steel—Method for determination of nitrogen content specified in JIS G 1228 (2006) and Method for determination of oxygen content in metallic materials specified in JIS Z 2613 (2006) are also used. Specifically, an oxygen/nitrogen analyzer TC-300/EF-300 manufactured by LECO Corporation is used.
In the soft magnetic powder according to this embodiment, in a mass-based particle size distribution measured by a laser diffraction particle size distribution analyzer, when a particle diameter at a cumulative frequency from a small diameter side of 10% is represented by D10, a particle diameter at a cumulative frequency of 50% is represented by D50, and a particle diameter at a cumulative frequency of 90% is represented by D90, (D90-D10)/D50 which is also called “span” satisfies 1.0 or more and 3.5 or less. Such a soft magnetic powder exhibits favorable flowability when it is molded into a desired shape. That is, such a soft magnetic powder is favorably packed into every corner when it is packed in a molding die and molded. Therefore, the molded density can be increased, and also a sintered body having a high sintered density is obtained. Such a sintered body has a high saturation magnetic flux density.
On the other hand, as described above, the soft magnetic powder according to this embodiment has a sufficiently high specific resistance. This is because by optimizing the span, the distribution on the particle surface, which is a main factor of an inter-particle resistance, is likely to be uniform, and even after sintering, a conduction path is less likely to be formed. Therefore, a sintered body produced using such a soft magnetic powder has a high saturation magnetic flux density and also a high specific resistance. Accordingly, when such a sintered body is used for, for example, a component for a dot impact printer (recording device) or a component for an electromagnetic actuator, a high driving force is generated without causing an increase in the size of the component, and also the component capable of suppressing eddy current loss can be realized.
When (D90−D10)/D50 is less than the above lower limit, the width of the particle size distribution becomes relatively large although it varies depending on the composition of the soft magnetic powder, and therefore, the packing density is decreased, and the saturation magnetic flux density of a sintered body may not be able to be sufficiently increased or a path through which conduction is likely to take place in a sintered body may be likely to be formed. On the other hand, when (D90−D10)/D50 exceeds the above upper limit, the flowability of the soft magnetic powder is deteriorated although it varies depending on the composition of the soft magnetic powder, and therefore, the sintered density is decreased, and the saturation magnetic flux density of a sintered body may not be able to be sufficiently increased or a path through which conduction is likely to take place in a sintered body may be likely to be formed.
Further, (D90−D10)/D50 of the soft magnetic powder preferably satisfies 1.2 or more and 3.0 or less, more preferably satisfies 1.5 or more and 2.5 or less.
Further, when the above-mentioned D50 is defined as the average particle diameter of the soft magnetic powder, the average particle diameter D50 of the soft magnetic powder is preferably 0.50 μm or more and 50.0 μm or less, more preferably 1.0 μm or more and 30.0 μm or less, further more preferably 3.0 μm or more and 20.0 μm or less. By using the soft magnetic powder having such an average particle diameter D50, a sintered body which is dense and has a high saturation magnetic flux density and also high mechanical properties is obtained.
When the average particle diameter D50 of the soft magnetic powder is less than the above lower limit, the soft magnetic powder is too fine, and therefore, the packing property of the soft magnetic powder may be easily deteriorated. Due to this, the sintered density of a sintered body is decreased, and the saturation magnetic flux density or the magnetic permeability may be decreased. On the other hand, when the average particle diameter D50 of the soft magnetic powder exceeds the above upper limit, the flowability of the soft magnetic powder is deteriorated, and therefore, the sintered density is decreased, and the saturation magnetic flux density or the magnetic permeability may not be able to be sufficiently increased likewise.
The particle size distribution of the soft magnetic powder may be any distribution, and the number of peaks in the particle size distribution may be one or more than one.
The specific surface area of the soft magnetic powder as measured by a BET method is preferably 0.15 m2/g or more and 0.80 m2/g or less, more preferably 0.20 m2/g or more and 0.70 m2/g or less. The soft magnetic powder having such a specific surface area exhibits a favorable packing property when it is molded. Therefore, a sintered body having a high sintered density, a high saturation magnetic flux density, and high mechanical properties can be obtained.
The measurement of the specific surface area by the BET method is performed using, for example, a BET specific surface area measurement device HM1201-010 manufactured by Mountech Co., Ltd. The amount of a sample is set to 5 g.
The tap density of the soft magnetic powder slightly varies depending on the particle diameter or the alloy composition, and therefore is not particularly limited, but is preferably 3.6 g/cm3 or more and 5.5 g/cm3 or less, more preferably 3.8 g/cm3 or more and 5.2 g/cm3 or less. The soft magnetic powder having such a tap density exhibits a favorable packing property when it is molded. Therefore, a sintered body having a high sintered density, a high saturation magnetic flux density, and high mechanical properties can be obtained.
The tap density of the soft magnetic powder is measured in accordance with the method for measuring the tap density of metallic powders specified in JIS Z 2512:2012, and the unit is, for example, [g/cm3].
Such a soft magnetic powder may be produced by any method, but is produced by, for example, various atomization methods such as a water atomization method, a gas atomization method, and a spinning water atomization method, a reducing method, a carbonyl method, a pulverization method, or the like. Among these, as the soft magnetic powder, a powder produced by an atomization method is preferably used. That is, the soft magnetic powder is preferably an atomized powder. According to this, a sintered body having a high sintered density, a high saturation magnetic flux density, and high mechanical properties is obtained.
The metal powder produced by an atomization method has a spherical shape relatively close to a perfect sphere, and therefore has excellent dispersibility and flowability in an organic binder. Therefore, from this viewpoint, the sintered density is increased.
In the water atomization method, a molten raw material is caused to collide with jets of cooling water so as to atomize the raw material into a fine powder, whereby a metal powder is produced.
At this time, when the melting point of the raw material is denoted by Tm, the temperature of the molten raw material is set to preferably Tm+20° C. or higher and Tm+200° C. or lower, more preferably Tm+50° C. or higher and Tm+150° C. or lower. According to this, the particle size distribution such as the average particle diameter or the span is optimized, and also the powder properties such as the specific surface area can be optimized. Therefore, the above-mentioned soft magnetic powder can be efficiently produced.
When the melting temperature is increased, the average particle diameter tends to decrease or the specific surface area tends to increase. On the other hand, when the melting temperature is decreased, the average particle diameter tends to increase or the specific surface area tends to decrease.
The pressure of the cooling water is not particularly limited, but is set to preferably 50 MPa or more and 200 MPa or less, more preferably 70 MPa or more and 150 MPa or less. According to this, the particle size distribution is optimized, and also the powder properties such as the tap density can be optimized. Therefore, the above-mentioned soft magnetic powder can be efficiently produced.
When the pressure of the cooling water is increased, the average particle diameter tends to decrease or the tap density tends to decrease. On the other hand, when the pressure of the cooling water is decreased, the average particle diameter tends to increase or the tap density tends to increase.
The thus obtained soft magnetic powder may be classified as needed. Examples of the classification method include dry classification such as sieve classification, inertial classification, centrifugal classification, and wind power classification, and wet classification such as sedimentation classification. By such classification, the particle size distribution such as the average particle diameter or the span, the specific surface area, the tap density, or the like can be appropriately adjusted.
Next, a sintered body produced using the soft magnetic powder according to the embodiment will be described.
This sintered body is a sintered body obtained by firing the above-mentioned soft magnetic powder. Such a sintered body has a high saturation magnetic flux density and also a high specific resistance.
The saturation magnetic flux density of the sintered body is preferably 2.2 T or more, more preferably 2.3 T or more, further more preferably 2.4 T or more. When such a sintered body is used for, for example, a component for a dot impact printer (recording device) or a component for an electromagnetic actuator, a high driving force is generated without causing an increase in the size of the component. Therefore, the performance of a device including such a component can be enhanced.
The saturation magnetic flux density of the sintered body is measured using, for example, a vibrating sample magnetometer (VSM).
The specific resistance of the sintered body is preferably 20 μΩcm or more, more preferably 22 μΩcm or more and 200 μΩcm or less, further more preferably 25 μΩcm or more and 150 μΩcm or less. Such a sintered body can suppress the eddy current loss small when an electromagnetic force is generated. Therefore, a decrease in the electromagnetic force due to eddy current loss can be suppressed.
The specific resistance of the sintered body is determined as a volume resistivity using, for example, a resistivity meter or the like adopting a four-terminal method.
The sintered body produced from the soft magnetic powder as described above may be used for any application. Examples of such application include a component for a dot impact printer (recording device), a component for an electromagnetic actuator, a component for a magnetic head, a component for a solenoid valve, a component for an electric motor, a component for a power generator, a component for a magnetostrictive sensor, a component for a speaker, a component for an electron microscope, and a component for a high magnetic field electromagnet.
Next, a method for producing a sintered body according to an embodiment will be described.
The method for producing a sintered body shown in
First, the soft magnetic powder and an organic binder are mixed, thereby obtaining a mixture. Examples of the mixture include a kneaded material (compound) obtained by kneading the soft magnetic powder and an organic binder and a granulated powder obtained by granulating a slurry containing the soft magnetic powder and an organic binder.
In the preparation of the kneaded material, for example, various types of kneaders such as a pressure or double-arm kneader-type mixer, a roll-type kneader, a Banbury-type kneader, and a single-screw or twin-screw extruder can be used.
In the preparation of the granulated powder, for example, a spray dryer, a tumbling granulator, a tumbling fluidized bed granulator, or the like can be used.
The organic binder preferably contains an unsaturated glycidyl group-containing polymer. The unsaturated glycidyl group-containing polymer is a polymer containing an unsaturated glycidyl group-containing monomer as a repeating unit. Examples of the unsaturated glycidyl group-containing monomer include glycidyl (meth)acrylate, allyl glycidyl ether, α-ethyl glycidyl ether, crotonyl glycidyl ether, glycidyl crotonate, monoalkyl itaconate monoglycidyl ester, monoalkyl fumarate monoglycidyl ester, monoalkyl maleate monoglycidyl ester, and alicyclic epoxy group-containing (meth)acrylate, and the organic binder contains one type or two or more types among these. Further, glycidyl (meth)acrylate is particularly preferably used.
Examples of a component to be contained in the organic binder include, other than the unsaturated glycidyl group-containing polymer, various types of resins including polyolefins such as polyethylene, polypropylene, polybutylene, and polypentene, polyolefin-based copolymers such as polyethylene-polypropylene copolymers and polyethylene-polybutylene copolymers, styrenic resins such as polystyrene, acrylic resins such as poly(methyl methacrylate) and poly(butyl methacrylate), polyvinyl chloride, polyvinylidene chloride, polyamide, polyesters such as polyethylene terephthalate and polybutylene terephthalate, polyether, polyvinyl alcohol, polyacetal, or copolymers thereof and the like, various types of waxes, higher fatty acids (for example, stearic acid), higher alcohols, higher fatty acid esters, higher fatty acid amides, and phthalate esters, and among these, one type or two or more types are used.
Among these, the organic binder preferably contains an unsaturated glycidyl group-containing polymer, a styrenic resin, a wax, and a phthalate ester. According to a combination of these components, a sintered body having a particularly high saturation magnetic flux density and particularly excellent mechanical properties can be produced.
Examples of the styrenic resin include polymers and copolymers containing a styrene monomer as a repeating unit, and polystyrene that is a homopolymer is preferably used.
As the wax, a petroleum-based wax or a modified wax thereof is preferably used, and paraffin wax, microcrystalline wax, carnauba wax, or a derivative thereof is more preferably used, and paraffin wax or carnauba wax is further more preferably used.
Examples of the phthalate ester include dimethyl phthalate, diethyl phthalate, butyl phthalate, dibutyl phthalate, diisobutyl phthalate, and dioctyl phthalate, and among these, one type or a combination of two types is used.
The mixture may contain, other than the above-mentioned components, another additive, for example, an antioxidant, a degreasing accelerator, a surfactant, or the like.
The content of the organic binder in the mixture is preferably 3 parts by mass or more and 9 parts by mass or less, more preferably 4 parts by mass or more and 9 parts by mass or less, further more preferably 5 parts by mass or more and 8 parts by mass or less with respect to 100 parts by mass of the soft magnet powder.
Subsequently, the obtained kneaded material is molded. By doing this, a molded body having a desired shape and size is produced.
As the molding method, for example, an injection molding method, a compression molding method, an extrusion molding method, or the like is used. The shape and size of the molded body to be produced are determined in anticipation of shrinkage by the subsequent degreasing and sintering.
The thus obtained molded body may be subjected to post-processing such as machining or laser processing as needed.
In addition, the obtained molded body may be subjected to a degreasing process. By doing this, a part or the whole of the organic binder contained in the molded body can be removed (degreased).
The molded body after degreasing may also be subjected to post-processing as needed.
Subsequently, the obtained molded body is fired. By doing this, the soft magnetic powder is sintered, and a sintered body is obtained.
The firing temperature of the molded body is not particularly limited, but is preferably 1050° C. or higher and 1600° C. or lower, more preferably 1050° C. or higher and 1400° C. or lower.
The firing time of the molded body is not particularly limited, but is preferably 1 hour or more and 25 hours or less, more preferably 2 hours or more and 20 hours or less.
The firing atmosphere is not particularly limited, but is preferably an inert gas atmosphere or a reduced pressure atmosphere, more preferably a reduced pressure inert gas atmosphere. According to this, while suppressing oxidation or denaturation of the soft magnetic powder, the decomposed component of the organic binder can be efficiently discharged by performing gas exchange around the molded body and vacuum evacuation.
It is expected that the relative density of the sintered body to be obtained is, for example, 95% or more, preferably 96% or more. Such a sintered body has a high sintered density, a high saturation magnetic flux density, and excellent mechanical properties.
Further, the obtained sintered body may be subjected to various types of post-processing, for example, machining such as cutting, pressing, or polishing, electric discharge processing, laser processing, etching, etc. By performing such post-processing, deburring can be performed, or the dimensional accuracy can be further improved.
Further, the obtained sintered body may be subjected to a HIP process (hot isostatic pressing process) or the like as needed. By doing this, the density of the sintered body can be further increased.
The conditions for the HIP process are set, for example, as follows: the temperature is 850° C. or higher and 1100° C. or lower, and the time is 1 hour or more and 10 hours or less.
The applied pressure is preferably 50 MPa or more, more preferably 100 MPa or more.
As described above, the method for producing a sintered body according to the embodiment includes a mixing step of mixing the soft magnetic powder according to the above-mentioned embodiment and an organic binder, thereby obtaining a mixture, a molding step of molding the mixture, thereby obtaining a molded body, and a firing step of firing the molded body, thereby obtaining a sintered body.
According to such a method for producing a sintered body, a sintered body having a high saturation magnetic flux density and a high specific resistance can be produced.
Next, a yoke case will be described as an application example of the sintered body.
A yoke case 1 shown in
The yoke case 1 has a recessed shape opened to the upper side. What corresponds to the bottom of this recessed portion is a case body 10. On an inner edge (an edge on the central hole 101 side) of the case body 10, an edge portion 111 protruding upward is provided, and on an outer edge (an edge on the opposite side to the central hole 101) of the case body 10, an edge portion 112 protruding upward is provided. That is, the yoke case 1 includes the case body 10 corresponding to the bottom of the recessed shape, and the edge portion 111 and the edge portion 112 corresponding to the side walls of the recessed shape.
Further, the yoke case 1 includes a core 12 that is provided in a region between the edge portion 111 and the edge portion 112 of the case body 10 in a plan view and protrudes upward. This core 12 is spaced apart from the edge portions 111 and 112 in a plan view. The protruding height of the core 12 is the same as the protruding heights of the edge portions 111 and 112.
The yoke case 1 includes twelve cores 12. At this time, when a straight line connecting each core 12 to the center of the central hole 101 is drawn, the separation angle between adjacent cores is equal in the whole yoke case 1. That is, a figure obtained by arranging the cores 12 forms a shape that satisfies a 12-fold rotational symmetry with the center of the central hole 101 as the axis of rotation.
On the other hand, the yoke case 1 includes through-holes 131 and 132 that are provided in a region between the edge portion 111 and the edge portion 112 of the case body 10 in a plan view and penetrate through the case body 10 in the thickness direction. Each of these through-holes 131 and 132 is spaced apart from the edge portions 111 and 112 and the cores 12 in a plan view.
The yoke case 1 includes twelve through-holes 131. These through-holes 131 are provided between the cores 12 and the edge portion 111 in a plan view.
Similarly, the yoke case 1 includes twelve through-holes 132. These through-holes 132 are provided between the cores 12 and the edge portion 112 in a plan view.
A figure obtained by arranging these through-holes 131 or 132 also forms a shape that satisfies a 12-fold rotational symmetry with the center of the central hole 101 as the axis of rotation.
Such a yoke case 1 includes the sintered body of the soft magnetic powder according to the embodiment described above. According to this, the yoke case 1 has soft magnetic properties. Then, by winding a winding wire (not shown) around each core 12, an electromagnetic coil is formed. Therefore, by allowing an electric current to flow through the winding wire, a component including the yoke case 1 can generate an electromagnetic force for operating as an electromagnetic actuator.
As described above, the sintered body of the soft magnetic powder according to the embodiment has a high saturation magnetic flux density and also a high specific resistance. Therefore, also the yoke case 1 and the core 12 included in the yoke case 1 have a high saturation magnetic flux density and a high specific resistance. As a result, in the electromagnetic actuator including the yoke case 1, a high driving force is generated without causing an increase in the size of the component, and also the eddy current loss is suppressed, and a decrease in the driving force due to the eddy current loss is suppressed. Therefore, in a device including the electromagnetic actuator, the output can be enhanced while avoiding an increase in the size.
Next, a dot impact printer (recording device) including the yoke case will be described.
A printer 100 shown in
The printer 100 shown in
The left side frame 16 and the right side frame 17 are erected on both ends of the base frame 14, respectively. Between the left side frame 16 and the right side frame 17, a carriage shaft 24 is stretched and pivotally supported, and the platen 21 is stretched and rotatably disposed as shown in
The sheet guide 22 is disposed between the left side frame 16 and the right side frame 17, and a sheet is conveyed between the sheet guide 22 and the platen 21.
Here, the recording head 18 includes the above-mentioned yoke case 1. Around the cores 12 (see
As described above, the yoke case 1 includes the sintered body of the soft magnetic powder according to the embodiment, and therefore has a high saturation magnetic flux density and a high specific resistance. As a result, in the recording head 18 including the yoke case 1, a high driving force is generated without causing an increase in the size of the component, and also the eddy current loss is suppressed, and a decrease in the driving force due to the eddy current loss is suppressed. Therefore, in the printer 100, the output can be enhanced while avoiding an increase in the size.
Hereinabove, the invention is described based on preferred embodiments, however, the invention is not limited thereto.
For example, the shape of the yoke case is not limited to the shape shown in the drawing, and may be any shape. For example, the number of cores is not limited to 12, and may be smaller or larger than 12. Further, the number of through-holes may be increased or decreased according to the number of cores.
Next, specific Examples of the invention will be described.
First, a soft magnetic powder having a composition shown in Table 1 produced by a water atomization method was prepared. With respect to this soft magnetic powder, the average particle diameter was measured using a laser diffraction particle size distribution analyzer (Microtrack HRA9320-X100, manufactured by Nikkiso Co., Ltd.). The measurement result is shown in Table 1.
Subsequently, an unsaturated glycidyl group-containing polymer, a styrenic resin, and paraffin wax were each frozen and ground, whereby a binder powder was obtained.
Subsequently, the soft magnetic powder, the binder powder, and a phthalate ester were mixed and kneaded at a kneading temperature of 160° C. for 30 minutes using a pressure kneader. This kneading was performed in a nitrogen gas atmosphere.
Subsequently, the obtained kneaded material was crushed using a pelletizer, whereby pellets having an average particle diameter of 5 mm were obtained.
Subsequently, by using the obtained pellets, molding was performed using an injection molding machine under the following molding conditions: material temperature: 190° C., and injection pressure: 10.8 MP (110 kgf/cm2). By doing this, a molded body was obtained.
Subsequently, the obtained molded body was subjected to a degreasing process by heating at 475° C. for 5 hours in a nitrogen atmosphere. By doing this, a degreased body was obtained.
Subsequently, the obtained degreased body was subjected to a firing process by heating at 1100° C. for 8 hours in an argon atmosphere. By doing this, a sintered body was obtained.
The obtained sintered body was an annular plate-shaped body (yoke case) as shown in
The respective components of the organic binder are as follows.
E denotes a repeating unit containing ethylene, GMA denotes a repeating unit containing glycidyl methacrylate, VA denotes a repeating unit containing vinyl acetate, and MA denotes a repeating unit containing methyl acrylate.
In the above notation, E denotes a repeating unit containing ethylene, GMA denotes a repeating unit containing glycidyl methacrylate, and VA denotes a repeating unit containing vinyl acetate.
Wax
Sintered bodies were obtained in the same manner as in Example 1 except that the production conditions were changed as shown in Table 1, respectively.
In Table 1, those corresponding to the invention are denoted by “Example”, and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
With respect to the sintered bodies obtained in the respective Examples and Comparative Examples, the density was measured by a method in accordance with the Archimedes' method (specified in JIS Z 2501). Then, the relative density of the sintered body was calculated from the measured sintered density and the true density of the soft magnetic powder.
Then, the calculated relative density was evaluated in the light of the following evaluation criteria.
A: The relative density is 98.0% or more.
B: The relative density is 97.5% or more and less than 98.0%.
C: The relative density is 97.0% or more and less than 97.5%.
D: The relative density is 96.5% or more and less than 97.0%.
E: The relative density is 96.0% or more and less than 96.5%.
F: The relative density is less than 96.0%.
The evaluation results are shown in Table 1.
With respect to the sintered bodies obtained in the respective Examples and Comparative Examples, the saturation magnetic flux density was measured using a vibrating sample magnetometer.
Then, the measured saturation magnetic flux density was evaluated in the light of the following evaluation criteria.
A: The saturation magnetic flux density is 2.4 T or more.
B: The saturation magnetic flux density is 2.3 T or more and less than 2.4 T.
C: The saturation magnetic flux density is 2.2 T or more and less than 2.3 T.
D: The saturation magnetic flux density is 2.1 T or more and less than 2.2 T.
E: The saturation magnetic flux density is 2.0 T or more and less than 2.1 T.
F: The saturation magnetic flux density is less than 2.0 T.
The evaluation results are shown in Table 1.
With respect to the sintered bodies obtained in the respective Examples and Comparative Examples, the volume resistivity was measured by a four-terminal method.
Then, the measured volume resistivity was evaluated in the light of the following evaluation criteria.
Evaluation Criteria for Volume Resistivity
A: The volume resistivity is 25 μΩcm or more.
B: The volume resistivity is 23 μΩcm or more and less than 25 μΩcm.
C: The volume resistivity is 21 μΩcm or more and less than 23 μΩcm.
D: The volume resistivity is 19 μΩcm or more and less than 21 μΩcm.
E: The volume resistivity is 17 μΩcm or more and less than 19 μΩcm.
F: The volume resistivity is less than 17 μΩcm.
The evaluation results are shown in Table 1.
As apparent from Table 1, it was confirmed that the sintered bodies obtained in the respective Examples all have a high saturation magnetic flux density and a high specific resistance.
The entire disclosure of Japanese Patent Application No. 2018-064788 filed Mar. 29, 2018 is expressly incorporated herein by reference.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2018-064788 | Mar 2018 | JP | national |
