WO2013061836A1 - NdFeB系焼結磁石の製造方法 - Google Patents
NdFeB系焼結磁石の製造方法 Download PDFInfo
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- WO2013061836A1 WO2013061836A1 PCT/JP2012/076797 JP2012076797W WO2013061836A1 WO 2013061836 A1 WO2013061836 A1 WO 2013061836A1 JP 2012076797 W JP2012076797 W JP 2012076797W WO 2013061836 A1 WO2013061836 A1 WO 2013061836A1
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- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/0253—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets
- H01F41/0293—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets diffusion of rare earth elements, e.g. Tb, Dy or Ho, into permanent magnets
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- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
- B22F7/02—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C28/00—Alloys based on a metal not provided for in groups C22C5/00 - C22C27/00
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
- H01F1/053—Alloys characterised by their composition containing rare earth metals
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
- H01F1/053—Alloys characterised by their composition containing rare earth metals
- H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
- H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
- H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
- H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
- H01F1/0577—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together sintered
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/0253—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C2202/00—Physical properties
- C22C2202/02—Magnetic
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
Definitions
- the present invention relates to a method for manufacturing a NdFeB (neodymium / iron / boron) based sintered magnet, and more particularly to a method for manufacturing a NdFeB based sintered magnet using a grain boundary diffusion method.
- the “NdFeB-based (sintered) magnet” is a (sintered) magnet having Nd 2 Fe 14 B as a main phase, but is not limited to one containing only Nd, Fe and B, and other than Nd It may contain other elements such as rare earth elements and Co, Ni, Cu, Al.
- NdFeB (neodymium / iron / boron) -based sintered magnets were found by Sagawa (the present inventor) in 1982, but have characteristics far surpassing the conventional permanent magnets. It has the feature that it can be manufactured from relatively abundant and inexpensive raw materials such as Nd (a kind of rare earth), iron and boron. Therefore, NdFeB-based sintered magnets are used for hybrid and electric vehicle drive motors, motor-assisted bicycle motors, industrial motors, voice coil motors such as hard disks, luxury speakers, headphones, permanent magnet magnetic resonance diagnostic devices, etc. Used in various products.
- the NdFeB based sintered magnet used for these applications is required to have a high coercive force H cJ , a high maximum energy product (BH) max and a high squareness ratio SQ.
- the squareness ratio SQ is defined by the ratio H k / H cJ of the magnetic field (H k ) and the coercive force (R H ) corresponding to 90% of the residual magnetic flux density B r in the second quadrant of the magnetization curve.
- Dy and / or Tb which is a heavy rare earth element, is referred to as “R H ”.
- R H a heavy rare earth element
- a coated product containing RH is applied to the surface as a substrate, and the substrate is heated together with the coated material, whereby particles in the substrate are coated from the substrate surface.
- a “grain boundary diffusion method” in which RH is diffused into the substrate through a boundary Patent Document 1.
- the coercive force of the NdFeB-based sintered magnet can be increased by the above method
- the presence of RH in the main phase particles in the sintered magnet is known to reduce the maximum energy product.
- R H is contained in the main phase particles at the stage of the starting alloy, and thus R H is also contained in the main phase particles even in a sintered magnet produced based on the R H.
- a sintered magnet produced by the one-alloy method has an improved coercive force but a reduced maximum energy product.
- most of RH can be present at the grain boundaries between the main phase grains. Therefore, it is possible to suppress a decrease in the maximum energy product compared to the one alloy method.
- the amount of RH which is a rare metal, can be reduced compared to the one alloy method.
- the grain boundary diffusion method has a problem that it is difficult to perform the treatment after the coating material is applied to the substrate.
- the substrate on which the coating material has been applied is placed on a predetermined table such as a tray and then heated in a heating furnace.
- the coating material is applied to the base material at the contact surface between the tray and the base material, the coating material is welded to the tray during heating.
- the present invention is for solving the above-mentioned problems, and the main purpose thereof is a coating containing RH or an RH compound applied to the base material of the NdFeB-based sintered magnet when performing the grain boundary diffusion treatment.
- An object of the present invention is to provide a method for producing an NdFeB-based sintered magnet capable of preventing an object from welding to an instrument such as a tray at a low cost.
- Another object of the present invention is to provide a method for producing an NdFeB-based sintered magnet suitable for mass production while easily adjusting the amount of the coated material when performing grain boundary diffusion treatment. It is.
- the manufacturing method of the NdFeB-based sintered magnet according to the present invention made to solve the above problems is as follows. After applying the coating material containing the heavy rare earth element to the base material of the NdFeB-based sintered magnet, the heavy rare earth element in the coating material is heated in the base material by heating the base material coated with the coating material.
- the method for producing a NdFeB-based sintered magnet including a grain boundary diffusion treatment step for diffusing through the grain boundary, Apply the coating on the sheet, The sheet and the substrate are brought into close contact so that the coating applied to the sheet is in contact with the application target surface of the substrate, The grain boundary diffusion treatment is performed by heating the substrate together with the sheet. It is characterized by that.
- a metal or alloy powder containing heavy rare earth element RH or a paste or slurry in which the powder is dispersed in water or a viscous material
- a powder of an alloy with an Fe group transition metal containing RH of 50 wt% or more, a powder of pure metal made only of RH, a powder of these alloys or a pure metal hydride can be used.
- a mixed powder of RH fluoride or oxide powder and Al powder may be used.
- the viscous material it is possible to use liquid paraffin, silicone grease, or the like having an appropriate viscosity that volatilizes during the grain boundary diffusion treatment and is not easily absorbed by the base material.
- viscous material having an appropriate viscosity refers to a material having a viscosity not less than the viscosity of water ( ⁇ 1 mPa ⁇ sec) and not more than the viscosity of the solder paste ( ⁇ 500 Pa ⁇ sec). If the viscosity is within this range, when the powder is mixed with the viscous material, the powder is uniformly dispersed in the viscous material, and the fluidity is such that the viscous material after mixing the powder can be applied to the sheet. Can have.
- the coated surface (coated surface) of the base material is covered with a sheet. Therefore, it can prevent that the coating material apply
- a graphite sheet (a flexible graphite sheet produced by molding graphite) as the sheet.
- heating is performed up to about 900 ° C., but in order to prevent the base material from being oxidized, it is performed in an inert gas atmosphere, a vacuum atmosphere, or an oxygen-free environment. Therefore, even when heated at the above temperature, the graphite sheet does not burn and does not deform. Moreover, the graphite sheet hardly reacts to the base material or the coated material. Heavy rare earth elements in the coating are hardly diffused into the graphite sheet. In addition, from the standpoints of availability, ease of processing, low cost, etc., the graphite sheet is a suitable sheet material and can be easily replaced even if it cannot withstand use.
- the coating material may be peeled off from the base material during the grain boundary diffusion treatment depending on the viscosity of the coating material. In order to prevent this, it is desirable to apply pressure to the sheet during the grain boundary diffusion treatment to improve the adhesion between the substrate and the coated material.
- the sheet may cover the same side surfaces of a plurality of base materials arranged in the horizontal direction.
- a plurality of substrates can be stacked in the vertical direction while covering the upper and lower surfaces of each substrate with a sheet.
- the coated surface of the base material is covered with a sheet, so that the coated material applied to the base material is prevented from being welded to a tray or the like during the grain boundary diffusion treatment. be able to. Moreover, the amount of the applied product can be easily adjusted by providing a recess on the application surface of the sheet. Furthermore, since a plurality of base materials can be collectively covered with a sheet or stacked in the vertical direction with the sheet interposed therebetween, it is suitable for mass production.
- the method for producing the base material of the NdFeB-based sintered magnet is not particularly limited.
- a base material having high magnetic properties can be obtained. Can be manufactured.
- FIG. 1 is an explanatory diagram of a method for producing the NdFeB-based sintered magnet of this example. As shown in this figure, in the manufacturing method of the NdFeB-based sintered magnet of this example, it is made of a material that does not change chemically or physically in the grain boundary diffusion treatment described later, and is a paste-like coating material R containing R H. Is prepared by uniformly applying on one surface (FIG. 1 (a)).
- the coated material R is a paste in which a powder of metal or alloy containing RH of 50 wt% or more (hereinafter referred to as “ RH powder”) and a viscous material are mixed. Silicone grease or liquid paraffin is used for the viscous material. For example, when silicone grease is used as the viscous material, it is also effective to mix silicone oil or the like for viscosity adjustment. Further, as R H powder in the present embodiment, Tb: 92wt%, Ni: 4.3wt%, Al: powder was used 3.7 wt% of TbNiAl alloy. Of course, heavy rare earth elements such as Dy may be used instead of Tb.
- the distribution of the powder particles when the same amount of RH powder is applied to the surface of the substrate S is uniform when the particle size is small, and the magnetic properties are stably improved by the grain boundary diffusion treatment. Become. Therefore, the smaller the particle size of the RH powder, the better. However, as the particle size is reduced, the effort and cost for miniaturization increase.
- the particle size of the RH powder is desirably 2 ⁇ m or more from the viewpoint of the effort and cost for miniaturization.
- the upper limit of the particle size of the RH powder in consideration of the magnetic characteristics and the distribution uniformity after the grain boundary diffusion treatment is 100 ⁇ m, preferably 50 ⁇ m, more preferably 20 ⁇ m.
- the weight mixing ratio of RH powder and silicone grease can be arbitrarily selected to adjust to the desired paste viscosity, but if the ratio of RH powder is low, RH powder penetrates into the base material during grain boundary diffusion treatment. The amount to do will also decrease. Therefore, the ratio of the RH powder is 80 wt% or more, preferably 85 wt% or more, and more preferably 90 wt% or more. If the amount of the silicone grease is less than 5 wt%, mixing with the RH powder is insufficient, making it difficult to form a paste and making it difficult to apply to the sheet. Therefore, the amount of silicone grease is preferably 5 wt% or more.
- the mixing ratio of silicone oil used for viscosity adjustment can be increased to about 15 wt%, but this reduces the ratio of RH powder, and the RH powder becomes the basis during grain boundary diffusion treatment. Since the amount of penetration into the material also decreases, ideally 5 wt% or less is preferable.
- the application surface of the sheet 10 is directed toward the application target surface of the base material S (the upper surface and the lower surface of the base material S) (FIG. 1 (b)). Thereafter, the substrate S covered with the sheet 10 is placed on the tray 11 (FIG. 1 (c)), placed in the heating furnace 12, and the sheet S together with the sheet 10 in an inert gas atmosphere or oxygen-free. Heat treatment (grain boundary diffusion treatment) is performed (FIG. 1 (d)).
- the manufacturing method of the NdFeB sintered magnet of this example is compared with the conventional method.
- the coating material R on the upper and lower surfaces of the substrate S as shown in FIG. 1
- the substrate 11 is placed as it is (FIG. 2 (a))
- the shape of the substrate is placed on the tray 21.
- a step as a holding portion 211 at the edge of the hole to hold only the end of the lower surface of the base material S (FIG. 2 (b)
- (c) a pointed support on the tray 31 The method of providing the part 311 and restraining the contact area of the tray 31 and the lower surface of the base material S to the minimum (FIG. 2C) has been used.
- the manufacturing cost of the tray 21 is increased by providing the holding unit 211, (ii) the trouble of placing the base material S on the holding unit 211 is required, and (iii) the base material There is a problem that it is necessary to change the shape of the holding portion 211 in accordance with the shape, size, etc. of S, and (iv) it is difficult to apply the coating R to the end portion of the lower surface of the substrate S.
- one sheet 10 (base material) on which the same side surfaces of a plurality of base materials S arranged in the horizontal direction are collected and coated with a coating R is applied.
- the upper and lower surfaces of S may be combined and covered with two sheets 10).
- two sheets 10 coated with the application material R shown in FIG. 3 (a) and a plurality of base materials S are stacked in a plurality of stages in the vertical direction. (Fig. 3 (b)).
- the manufacturing method of the NdFeB-based sintered magnet by the grain boundary diffusion method of the present embodiment is a method suitable for low cost, high speed, and mass production.
- the sheet 10 may be peeled off from the substrate S during the grain boundary diffusion treatment.
- the weight 13 is used as a means for improving the adhesion between the sheet 10 and the substrate S.
- a mechanical pressure such as a press cylinder is used. You may use what adds.
- the application region of the coated material R it is also possible to limit the application region of the coated material R to the sheet 10 only to a portion where the base material S is disposed (FIG. 3 (d)). In that case, it is necessary to set the application region of the application R applied to the upper and lower sheets 10 sandwiching the base material S so as to be portions facing the upper and lower surfaces of the base material S.
- the sheet 10 can be a graphite sheet. Moreover, it is desirable to provide the sheet 10 with an uneven shape as shown in FIG. As shown in FIG. 5, such a sheet 10 can be obtained by placing a graphite sheet 10 ⁇ / b> A on a press die 14 and covering the rubber sheet 15 on the graphite sheet 10 ⁇ / b> A and pressing it.
- the first advantage is that, as shown in FIG. 6 (a), if the coated material R is applied to the coated surface of the sheet 10 in a full manner, the number and volume of the concave portions provided on the coated surface side of the sheet 10 That is, the amount of the application R is easily determined. If a plurality of press dies 14 are prepared in advance, the amount of application to the substrate S can be easily adjusted simply by replacing the press dies 14 and recreating the sheet 10. Further, even if the sheet 10 cannot withstand use, it can be easily replaced at low cost.
- the second advantage is that the substrate S and the sheet 10 are sufficiently brought into close contact with each other, so that the surface of the substrate S functions as a lid for the concave portion of the sheet 10 and the coating material R stored in the concave portion leaks out. It becomes difficult (FIG. 6 (b)). Thereby, it is possible to prevent the coated material R from being unevenly distributed on the surface of the substrate S to be coated.
- the above is an advantage in the manufacturing process of the method of this embodiment compared with the conventional method, but the advantage of the method of this embodiment also appears in the magnetic characteristics of the manufactured magnet.
- the magnetic characteristics of the sintered magnet manufactured by the method of this example are shown in Table 1.
- Table 1 the magnetic properties of a sintered magnet produced by subjecting a substrate S placed as shown in FIG. 2C to a grain boundary diffusion treatment are shown.
- Br is the residual magnetic flux density (magnetization J or magnetic flux density B when the magnetic field H of the magnetization curve (JH curve) or demagnetization curve (BH curve) is 0)
- Js is the saturation magnetization.
- H cB is the coercivity defined by the demagnetization curve
- H cJ is the coercivity defined by the magnetization curve
- (BH) Max is the maximum energy product (magnetic flux density B in the demagnetization curve B r / J s is the degree of orientation
- H K is the value of the magnetic field H when the magnetization J is 90% of the residual magnetic flux density B r
- SQ is the squareness (H K / H cJ ). The larger these values, the better the magnet properties are obtained.
- the base material S1 in Table 1 is an NdFeB-based sintered magnet having a length of 7 mm, a width of 7 mm, and a thickness of 4 mm in which the thickness direction is the magnetization direction, which is used as a base material for the comparative examples and examples of Table 1. It is.
- Comparative Example 1 and Comparative Example 2 are magnets manufactured by subjecting a substrate S1 placed as shown in FIG. 2 (c) to grain boundary diffusion treatment, and Comparative Example 1 is an aging treatment after grain boundary diffusion treatment.
- Comparative Example 2 is a magnet that was subjected to aging treatment after the grain boundary diffusion treatment on the magnet of Comparative Example 1.
- Examples 1 to 4 are magnets obtained by the production method of this example
- Examples 1 and 2 are magnets that were not subjected to aging treatment after grain boundary diffusion treatment
- Examples 3 and 4 were Examples 1 and 4, respectively. It is the magnet which performed the aging process after the grain boundary diffusion process with respect to 2 magnets.
- the temperature was raised from room temperature to 450 ° C. over 1 hour, heated at 450 ° C. for 1 hour, and then over 2 hours. The temperature was raised to 875 ° C., then heated for 10 hours while maintaining the temperature at 875 ° C., and then cooled to room temperature.
- the aging treatment of Comparative Example 2 and Examples 3 and 4 was performed by heating at 480 ° C.
- the coated product R a paste in which 0.07 g of silicone oil was added to 10 g of a mixture of the above TbNiAl alloy powder and silicone grease in a weight ratio of 80:20 was used. Further, in Comparative Examples 1 and 2, 10 mg of each paste was applied to both 7 mm ⁇ 7 mm magnetic pole faces of the substrate S1, for a total of 20 mg. In Examples 1 to 4, after applying 9 mg of paste to each of the two sheets 10 and a total of 18 mg and pasting them on both magnetic pole surfaces of the substrate S1, the pressure ( 2 kgf / cm 2 ( ⁇ 20 MPa) ( Hereinafter, this pressure is referred to as “contact pressure”), whereby the sheet 10 is brought into close contact with the sample S1.
- contact pressure 2 kgf / cm 2 ( ⁇ 20 MPa
- the adhesion pressure is preferably in the range of 0.01kgf / cm 2 ( ⁇ 0.1MPa) ⁇ 10kgf / cm 2 ( ⁇ 100MPa).
- the adhesion pressure is less than 0.01 kgf / cm 2 adhesion becomes insufficient, is greater than 10 kgf / cm 2 is not suitable for mass production.
- the graphite sheet having the uneven shape shown in FIG. 4 was used. Zirconia plates were used for the tray 11 of the example and the tray 31 of the comparative example.
- the coercive force H cJ is greatly improved as compared with the base material S1 by the grain boundary diffusion treatment, while the residual magnetic flux density B r.
- the maximum energy product (BH) Max slightly decreases, the magnets of Comparative Examples 1 and 2 have a greater degree of change in their magnetic properties than the magnets of Examples 1 to 4. It is considered that the difference in magnetic characteristics between the comparative example and the example is caused by the coating amount of the coated material R.
- the magnets of Examples 1 to 4 had improved squareness SQ compared to the magnets of Comparative Examples 1 and 2.
- used for applications such as voice coil motors such as hard disks, drive motors for hybrid and electric vehicles, motors for electric assist type bicycles, industrial motors, high-class speakers, headphones, and permanent magnet magnetic resonance diagnostic devices
- the NdFeB-based sintered magnet is required to have a high coercive force H cJ , a high maximum energy product (BH) max and a high squareness ratio SQ.
- H cJ coercive force
- BH maximum energy product
- Table 1 the production method of the NdFeB-based sintered magnet of this example is a production method suitable for producing a sintered magnet having excellent squareness. Further, it can be seen from Table 1 that the squareness SQ can be further improved by applying the aging treatment.
- Table 2 shows the experimental results when a paste obtained by adding 0.03 g of silicone oil to 10 g of a mixture of the above TbNiAl alloy powder and silicone grease in a weight ratio of 80:20 is used as the coating R. Shown in The paste used in the experiment of Table 2 has a higher viscosity than the paste used in the experiment of Table 1.
- the base material S2 in Table 2 is an NdFeB system having a length of 7 mm, a width of 7 mm, and a thickness of 4 mm used as a base material when the magnets of Comparative Examples 3 to 6 and Examples 5 to 8 are produced by grain boundary diffusion treatment. It is a sintered magnet.
- Comparative Examples 3 to 6 the amount of the coating material used in Comparative Examples 3 to 6 is 20 mg of 10 mg ⁇ 2, and the amount of the coating material used in Examples 5 to 8 is 14 mg of 7 mg ⁇ 2.
- Comparative Examples 3 and 4 Examples 5 and 6 were magnets that were not subjected to aging treatment after grain boundary diffusion treatment, Comparative Examples 5 and 6, and Examples 7 and 8 were Comparative Examples 3 and 4, and Examples 5 and 6, respectively.
- the grain boundary diffusion treatment, aging treatment, adhesion pressure, sheet and tray conditions in Table 2 are the same as the experimental conditions in Table 1.
- the magnets of Examples 5 to 8 have a lower coercive force H cJ than the magnets of Comparative Examples 3 to 6. This is because the sheet 10 peeled from the substrate S during the grain boundary diffusion treatment.
- the adhesion when the sheet 10 is adhered to the substrate S according to the paste viscosity so that the sheet 10 does not peel from the substrate S during the grain boundary diffusion treatment. It is desirable to optimize the pressure, the presence / absence of the weight 13 and the weight of the weight 13 as shown in FIGS.
- Table 3 shows a weight of 36 g per one base material (7 mm square area) on the base material S2 with the sheet 10 interposed therebetween under the same experimental conditions as in Examples 5 to 8 in Table 2.
- the magnetic characteristics of the magnet manufactured by placing the shim 13 are shown.
- Examples 9 to 11 were magnets that were not subjected to the aging treatment after the grain boundary diffusion treatment, and Examples 12 to 14 were subjected to the aging treatment after the grain boundary diffusion treatment for the magnets of Examples 9 to 11, respectively. Magnet.
- the sheet 10 is placed on the base material S2 with the sheet 10 interposed therebetween, so that the adhesiveness between the two is maintained without peeling the sheet 10 from the base material S2 during the grain boundary diffusion treatment. I was able to.
- the coercive force H cJ was greatly improved.
- the squareness SQ is somewhat low in Examples 10 and 11, but the magnets of Examples 13 and 14 in which the magnets of Examples 10 and 11 are subjected to an aging treatment have an extremely good result of 95% or more. was gotten.
- the squareness SQ of Example 12 was the highest as compared with the magnets of other Comparative Examples and Examples.
- a weight 13 of 36 g per base material was used.
- the pressure applied during the grain boundary diffusion treatment was 0.1 MPa or more (about 5 g or more per base material). If so, equivalent results were obtained.
- group sintered magnet which concerns on this invention was demonstrated using the Example, the manufacturing method of this invention is not limited only to this.
- the case where the coated material R is applied to both the upper surface and the lower surface of the base material S via the sheet 10 is shown, but the coated material R is applied only to one surface depending on the use of the manufactured magnet.
- the coated material R is applied only to one surface depending on the use of the manufactured magnet.
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Abstract
Description
これに対し、二合金法では、RHの多くを主相粒子間の粒界に存在させることができる。そのため、一合金法に比べて最大エネルギー積の低下を抑えることが可能となる。また、一合金法に比べてレアメタルであるRHの使用量を減らすことができる。
重希土類元素を含む塗布物をNdFeB系焼結磁石の基材に塗布した後に、該塗布物が塗布された基材を加熱することにより、前記塗布物中の重希土類元素を該基材中に粒界を通じて拡散させる粒界拡散処理工程を含むNdFeB系焼結磁石の製造方法において、
シートに前記塗布物を塗布し、
前記シートに塗布された塗布物が前記基材の塗布対象面に接するように、該シートと該基材を密着させ、
前記シートごと前記基材を加熱することにより前記粒界拡散処理を行う、
ことを特徴とする。
また、前記シートには、前記粒界拡散処理中、製造したNdFeB系焼結磁石の性能に影響を与えない程度に化学的、物理的に変化しない素材のものを用いることが望ましい。
また、本実施例ではRH粉末として、Tb:92wt%、Ni:4.3wt%、Al:3.7wt%のTbNiAl合金の粉末を使用した。もちろん、Tbの代わりにDy等の重希土類元素を使用しても良い。なお、同量のRH粉末を基材Sの表面に塗布した場合の粉末粒子の分布は粒径が小さい方が一様になり、粒界拡散処理によって安定的に磁気特性が向上するようになる。従って、RH粉末の粒径は小さければ小さい方が望ましいが、粒径を小さくするにつれて、微細化のための手間やコストが大きくなる。この微細化のための手間やコストの点からRH粉末の粒径は2μm以上が望ましい。また、粒界拡散処理後の磁気特性と分布の一様性を勘案したRH粉末の粒径の上限は100μm、好ましくは50μm、更に好ましくは20μmである。
RH粉末とシリコーングリースの重量混合比は所望のペースト粘度に調整すべく任意に選択できるが、RH粉末の比率が低ければ、粒界拡散処理の際にRH粉末が基材内部に侵入する量も低下してしまう。従って、RH粉末の比率は80wt%以上、好ましくは85wt%以上、更には90wt%以上がより好ましい。なお、シリコーングリースの量が5wt%未満になるとRH粉末との混合が不十分でペースト化できずシートへの塗布が困難になるので、シリコーングリースの量は5wt%以上が好ましい。また、粘度調整のために用いるシリコーンオイル等の混合比率は15wt%程度まで増やすことも可能であるが、それによってRH粉末の比率が低くなり、粒界拡散処理の際にRH粉末が基材内部に侵入する量も低下してしまうため、理想的には5wt%以下が好ましい。
以上のように、本実施例の粒界拡散法によるNdFeB系焼結磁石の製造方法は、低コスト、高速化、大量生産に向いた方法である。
第1の利点は、図6(a)に示すように、塗布物Rをシート10の塗布面に摩り切り一杯に塗布すれば、シート10の塗布面側に設けた凹部の数及び容積によって、塗布物Rの量が簡単に決まることである。また、プレス型14を予め複数用意しておけば、プレス型14を交換し、シート10を作製し直すだけで、基材Sへの塗布量を容易に調整することができる。また、シート10が使用に耐えられなくなっても、簡単に且つ低コストで交換することができる。
また、表1の基材S1は、表1の比較例と実施例の磁石の基材として使用する、厚さ方向が磁化方向である縦7mm×横7mm×厚さ4mmのNdFeB系焼結磁石である。比較例1及び比較例2は、図2(c)に示すように載置した基材S1に粒界拡散処理を施すことにより製造した磁石であり、比較例1は粒界拡散処理後に時効処理を行わなかった磁石、比較例2は比較例1の磁石に対して粒界拡散処理後に時効処理を行った磁石である。実施例1~4は本実施例の製造方法により得られた磁石であり、実施例1及び2は粒界拡散処理後に時効処理を行わなかった磁石、実施例3及び4はそれぞれ実施例1及び2の磁石に対して粒界拡散処理後に時効処理を行った磁石である。
比較例1及び2と実施例1~4の粒界拡散処理はいずれも、室温から1時間かけて450℃まで昇温した後、450℃に保ったまま1時間加熱し、それから2時間かけて875℃まで昇温した後、875℃に保ったまま10時間加熱し、その後室温まで冷却することにより行った。
比較例2と実施例3及び4の時効処理は、480℃で1.5時間加熱することにより行った。
塗布物Rには、上記のTbNiAl合金粉末とシリコーングリースを重量比で80:20の割合で混合した混合物10gにシリコーンオイルを0.07g添加したペーストを使用した。また、比較例1及び2では、基材S1の7mm×7mmの両磁極面にそれぞれ10mgずつ、合計20mgのペーストを塗布した。実施例1~4では、2枚のシート10にそれぞれ9mgずつ、合計18mgのペーストを塗布し、基材S1の両磁極面にそれぞれ貼り付けた後、2kgf/cm2(≒20MPa)の圧力(以下、この圧力のことを「密着圧」と称する)を印加することにより、サンプルS1にシート10を密着させた。なお、密着圧は0.01kgf/cm2 (≒0.1MPa)~10kgf/cm2 (≒100MPa)の範囲とすることが望ましい。密着圧が0.01kgf/cm2より小さくては密着性が不十分となり、10kgf/cm2より大きくては量産に向かない。
シート10には、図4に示した凹凸形状を有するグラファイトシートを用いた。
実施例のトレイ11及び比較例のトレイ31には、ジルコニア製の板を用いた。
また、時効処理を施すことで、より角型性SQを向上させることができることが表1より分かる。
なお、表2の基材S2は、比較例3~6及び実施例5~8の磁石を粒界拡散処理により製造する際の基材として使用する縦7mm×横7mm×厚さ4mmのNdFeB系焼結磁石である。また、比較例3~6に使用する塗布物の量は10mg×2の20mg、実施例5~8に使用する塗布物の量は7mg×2の14mgである。比較例3及び4、実施例5及び6は粒界拡散処理後に時効処理を行わなかった磁石、比較例5及び6、実施例7及び8はそれぞれ比較例3及び4、実施例5及び6の磁石に対して粒界拡散処理後に時効処理を行った磁石である。表2の粒界拡散処理、時効処理、密着圧、シート及びトレイの条件は、表1の実験条件と同じである。
なお、表3の実験では基材1個あたり36gの重し13を用いたが、この実験において粒界拡散処理の間に印加する圧力は0.1MPa以上(基材1個あたり約5g以上)であれば、同等の結果が得られた。
10A…グラファイトシート
11、21、31…トレイ
12…加熱炉
13…重し
14…プレス型
15…ゴムシート
211…保持部
311…支持部
Claims (11)
- 重希土類元素を含む塗布物をNdFeB系焼結磁石の基材に塗布した後に、該塗布物が塗布された基材を加熱することにより、前記塗布物中の重希土類元素を該基材中に粒界を通じて拡散させる粒界拡散処理工程を含むNdFeB系焼結磁石の製造方法において、
シートに前記塗布物を塗布し、
前記シートに塗布された塗布物が前記基材の塗布対象面に接するように、該シートと該基材を密着させ、
前記シートごと前記基材を加熱することにより前記粒界拡散処理を行う、
ことを特徴とするNdFeB系焼結磁石の製造方法。 - 前記シートの塗布面側に、多数の凹部が設けられていることを特徴とする請求項1に記載のNdFeB系焼結磁石の製造方法。
- 前記凹部の数又は深さを調整することによって、前記塗布物の量を調整することを特徴とする請求項2に記載のNdFeB系焼結磁石の製造方法。
- 前記シートにグラファイトシートを用いることを特徴とする請求項1~3のいずれかに記載のNdFeB系焼結磁石の製造方法。
- 前記粒界拡散処理の間、前記シートを前記基材に密着させておくことを特徴とする請求項1~4のいずれかに記載のNdFeB系焼結磁石の製造方法。
- 前記粒界拡散処理中に前記シートに圧力を印加し、前記基材と前記塗布物の密着性を高めることを特徴とする請求項5に記載のNdFeB系焼結磁石の製造方法。
- 水平方向に並べた複数個の基材の同じ側の面を一枚のシートでまとめて覆うことを特徴とする請求項1~6のいずれかに記載のNdFeB系焼結磁石の製造方法。
- 複数個の基材を、各基材の上面と下面をそれぞれシートで覆いつつ鉛直方向に重ねることを特徴とする請求項1~7のいずれかに記載のNdFeB系焼結磁石の製造方法。
- 前記粒界拡散処理の後に時効処理を行うことを特徴とする請求項1~8のいずれかに記載のNdFeB系焼結磁石の製造方法。
- 前記シートが、前記基材よりも前記重希土類元素の拡散性の低い素材であることを特徴とする請求項1~9のいずれかに記載のNdFeB系焼結磁石の製造方法。
- 前記シートが、前記粒界拡散処理において化学的、物理的に変化しない素材であることを特徴とする請求項1~10のいずれかに記載のNdFeB系焼結磁石の製造方法。
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JPWO2013061836A1 (ja) | 2015-04-02 |
US20150041022A1 (en) | 2015-02-12 |
EP2772926A4 (en) | 2015-07-22 |
EP2772926A1 (en) | 2014-09-03 |
CN103890880B (zh) | 2016-08-24 |
JP6100168B2 (ja) | 2017-03-22 |
CN103890880A (zh) | 2014-06-25 |
KR20140084275A (ko) | 2014-07-04 |
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