WO2003086687A1 - Procede permettant de mouler a la presse de la poudre d'alliage de terre rare, et procede pour produire un objet fritte en alliage de terre rare - Google Patents
Procede permettant de mouler a la presse de la poudre d'alliage de terre rare, et procede pour produire un objet fritte en alliage de terre rare Download PDFInfo
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- WO2003086687A1 WO2003086687A1 PCT/JP2003/004370 JP0304370W WO03086687A1 WO 2003086687 A1 WO2003086687 A1 WO 2003086687A1 JP 0304370 W JP0304370 W JP 0304370W WO 03086687 A1 WO03086687 A1 WO 03086687A1
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- earth alloy
- rare earth
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B30—PRESSES
- B30B—PRESSES IN GENERAL
- B30B11/00—Presses specially adapted for forming shaped articles from material in particulate or plastic state, e.g. briquetting presses, tabletting presses
- B30B11/02—Presses specially adapted for forming shaped articles from material in particulate or plastic state, e.g. briquetting presses, tabletting presses using a ram exerting pressure on the material in a moulding space
- B30B11/022—Presses specially adapted for forming shaped articles from material in particulate or plastic state, e.g. briquetting presses, tabletting presses using a ram exerting pressure on the material in a moulding space whereby the material is subjected to vibrations
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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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/02—Compacting only
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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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/02—Compacting only
- B22F3/03—Press-moulding apparatus therefor
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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
- H01F1/0536—Alloys characterised by their composition containing rare earth metals sintered
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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
- H01F1/06—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 in the form of particles, e.g. powder
- H01F1/08—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 in the form of particles, e.g. powder pressed, sintered, or bound together
- H01F1/086—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 in the form of particles, e.g. powder pressed, sintered, or bound 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
- H01F41/0273—Imparting anisotropy
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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
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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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- 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
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
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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
- H01F1/0573—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 obtained by reduction or by hydrogen decrepitation or embrittlement
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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
Definitions
- the present invention relates to a method for press-forming rare earth alloy powder and a method for producing a sintered rare earth alloy.
- Rare earth alloy sintered magnets are generally manufactured by pressing a rare earth alloy powder, sintering the resulting powder compact, and aging.
- two types of rare earth / cobalt magnets and rare earth / iron / boron magnets are widely used in various fields.
- rare-earth / iron / boron-based magnets hereinafter referred to as “R-Fe-B-based magnets.”
- R is a rare-earth element containing Y
- Fe is iron
- B boron. Since it has the highest maximum magnetic energy product among various magnets and is relatively inexpensive, it is actively used in various electronic devices.
- R - F e- B based sintered magnet is mainly consists of R 2 F e 1 4 tetragonal compound or Ranaru main phase of B, consisting of N d like R-rich phase and B-rich phase .
- a part of Fe is replaced with a transition metal such as C ⁇ Ni, and a part of boron (B) is replaced with carbon (C).
- the R'-Fe-B sintered magnet to which the present invention is preferably applied is, for example, No. 4,770,368 and U.S. Pat. No. 4,792,368.
- an ingot manufacturing method has been used to manufacture an R-Fe-B-based alloy that becomes such a magnet.
- a rare earth metal, electrolytic iron and a ferroboron alloy as starting materials are melted by high frequency, and the obtained molten metal is cooled relatively slowly in a mold to form an alloy ingot. Is done.
- alloy alloys have been ordered relatively quickly (by contacting them with single rolls, twin rolls, rotating discs, or the inner surface of a rotating cylindrical ⁇ type), and solidified alloys that are thinner than ingots ("
- the quenching method typified by the strip casting method and the centrifugal squeezing method has attracted attention.
- the thickness of alloy slabs produced by such a quenching method is generally in the range of about 0.03 mm or more and about 1 Omm or less.
- the molten alloy begins to solidify from the surface in contact with the cooling roll (roll contact surface), and crystals grow columnar from the roll contact surface in the thickness direction.
- quenched alloys manufactured by strip casting have a size in the short axis direction of about ⁇ .1 m or more and about 100 m or less, and a size in the long axis direction of about 5 wm or more and about 500 um or less.
- the tissue containing the R Ritsuchi phase present distributed in the grain boundary of the R 2 F e 4 B crystalline phases.
- the R-rich phase is a non-magnetic phase in which the concentration of the rare-earth element R is relatively high, and its thickness (corresponding to the width of the grain boundary) is less than about 10 m.
- Quenched alloy is conventional Ingo' Bok ⁇ method (mold ⁇ method) by work made by alloy (Ingo' Bok alloy) compared to relatively short time (cooling rate: 1 ⁇ 2 ° or more CZ seconds , because it is cooled in 1 0 4 ° ⁇ seconds or less), the tissue is miniaturized, and has a feature that the crystal grain size is small, Ru.
- the area of the grain boundary is large and the R-rich phase is widely spread in the grain boundary, there is an advantage that the dispersibility of the R-rich phase is excellent. Because of these characteristics, a magnet having excellent magnetic properties can be manufactured by using a quenched alloy.
- a method called the Ca reduction method (or reduction diffusion method) is known.
- the method includes the following steps. First, a mixed powder containing at least one of the rare earth oxides, iron powder and pure boron powder, and at least one of ferroboron powder and boron oxide in a predetermined ratio, or a mixture of the above constituent elements A mixture containing alloy powder or mixed oxide at a predetermined ratio, mixed with metallic calcium (C a) and calcium chloride (C a C 1), and subjected to reduction diffusion treatment in an inert gas atmosphere. By slurrying the obtained flax product and treating it with water, an R—Fe—B alloy solid can be obtained.
- a solid alloy lump is referred to as an “alloy lump” and includes an alloy ingot obtained by a conventional ingot manufacturing method and an alloy flake obtained by a rapid cooling method such as a strip casting method.
- alloy powders which are not only solid alloys obtained by cooling the molten metal but also solid alloys of various forms, such as solid alloys obtained by the Ca reduction method, are subjected to press forming. Alloy ingot, for example water Crushed by the elemental occlusion method and / or the mechanical grinding method of seeds (for example, a disc mill is used) to obtain a coarse powder (for example, having an average particle size of 1).
- 0 ⁇ ⁇ 50 ⁇ m is obtained by finely pulverizing, for example, a dry pulverization method using a jet mill.
- the average particle size of the R—Fe—B alloy powder used for press molding is preferably in the range of 1.5 m to 6 m from the viewpoint of magnetic properties.
- the “average particle size” of the powder refers to the mass median diameter (mass med i a n d i a m e t ⁇ r: MMD) unless otherwise specified.
- mass median diameter mass median diameter
- powder having such a small average particle size is used, fluidity and press formability (including cavity filling and compressibility) are poor, and productivity is poor.
- scan Bok lip Cass Bok method quenching method (cooling rate 1 0 2 / sec to 1 0 4 / sec) is produced in powder, as compared with the powder produced by Ingo' Bok method, phi Hitoshitsubu ⁇ In addition to the small particle size, the particle size distribution is sharp (steep), so the fluidity is particularly poor. As a result, the amount of powder that is crushed by the cavities varies beyond the allowable range, and the packing density in the cavities becomes uneven. As a result, the mass / dimension of the molded product may vary beyond the allowable range, and the molded product may be chipped or cracked. Furthermore, the magnet was not sufficiently oriented by the orientation magnetic field, and the magnetic properties (for example, residual magnetic flux density) of the finally obtained sintered magnet were low.
- the press forming method of the magnet molded body is roughly classified into two methods depending on the direction of the orientation magnetic field.
- the direction parallel to the pressing direction compression direction
- FIGS. 1 (a) and 1 (b) a method for press-forming a compact for an arcuate magnet will be described.
- Arrow B in FIG. 1 (a) and arrow B in FIG. 1 (b) indicate the direction of the orientation magnetic field during press molding.
- the arc-shaped magnet 1a shown in Fig. 1 (a) is manufactured by cutting the sintered block 1b shown in Fig. 1 (b) from the viewpoint of productivity and magnetic properties. ing.
- a compact for obtaining the sintered block 1b has been formed using a right-angle pressing method. This is because the right-angle press method enables press forming without losing the magnetic field orientation.
- magnets obtained by the right-angle press method have better magnetic properties than magnets obtained by the parallel press method. Have and.
- the yoke member in the vicinity of the through hole (die hole) for forming the cavity in the die made of non-magnetic material (within 15 cm from the inner wall of the die hole in the direction of orientation), the inside of the cavity is formed. Attempts have been made to concentrate the magnetic flux and improve the strength of the alignment magnetic field. This is because the residual magnetic flux density B of the finally obtained magnet increases as the intensity of the orientation magnetic field in the cavity increases. Combining the technique of increasing the strength of the orientation magnetic field in the cavity using such a yoke member with the above-described right-angle pressing method makes it possible to manufacture a permanent magnet having more excellent characteristics.
- the particle size (FS Fine powder with an SS particle size of 6 m or less is used.
- FS Fine powder with an SS particle size of 6 m or less In order to orient such fine powder particles, it is necessary to apply a stronger magnetic field than before.
- the yoke member is used to increase the magnetic field intensity in the cavity, the magnetic field intensity distribution in the cavity is not uniform, and the magnetic field intensity becomes higher near the end of the cavity in the orientation direction. Since the magnetic field strongly attracts the magnet powder in the cavity toward the yoke member, there is a problem that the apparent density of the magnet powder in the center of the cavity is lower than that in the end of the cavity.
- the orientation magnetic field is applied from the initial stage of the compaction process (the stage where the powder density is low and the powder can move in the cavity), the bias of the powder is likely to occur in the cavity. ,.
- the powder collected at the end of the cavity is pushed to the center of the cavity by the lowering and pressing of the upper punch, and moves.
- the orientation is disturbed at both ends of the cavity.
- the degree of orientation and the density of the powder compact are likely to be non-uniform, and the uniformity of the magnet properties tends to deteriorate.
- the magnetic flux itself tends to be bent due to the concentration of the magnetic flux.
- the present invention has been made in view of the above points, and a main purpose of the present invention is to provide a method for press-forming a rare-earth alloy powder that enables production of a sintered magnet having uniform magnetic properties. It is in. Disclosure of the invention
- a method for pressing a rare earth alloy powder according to the present invention is directed to a rare earth using a die formed of a non-magnetic material, the die having a through hole for forming cavities, and yokes arranged on both sides of the through hole.
- a method of pressing a rare earth alloy powder a step of preparing a rare earth alloy powder, a step of filling the rare earth alloy powder in the cavity of the die, and opposing the rare earth alloy powder filled in the cavity. And compressing with a pair of pressurized surfaces, the apparent density of the rare earth alloy powder in the cavity reaches a predetermined value of 47% or more of the true density during the period of the compression step. Only after that, a step of applying a pulse magnetic field substantially perpendicular to the compression direction is included.
- the predetermined value is 3. SS g Z cm 3 or more on Is set to
- the pulse magnetic field is an alternating damping magnetic field.
- the pulse magnetic field is a reverse pulse magnetic field.
- the vibration is supplied from at least one of the pair of pressing surfaces.
- the rare earth alloy powder is a powder produced by a rapid method.
- a method for producing a rare earth alloy sintered body according to the present invention includes a step of producing a molded body by any one of the above rare earth alloy powder press molding methods, and a step of sintering the molded body.
- Fig. 1 (a) is a schematic diagram showing an arcuate magnet, and (b) is a schematic diagram of a sintered block for producing an arcuate magnet.
- FIG. 2 is a schematic diagram showing a configuration of a press device suitably used for press molding of the embodiment according to the present invention.
- FIG. 3 is a perspective view showing a configuration example of a die used for press molding of the embodiment according to the present invention.
- FIG. 4 (a) is a diagram schematically showing the state of the powder particles subjected to vibration in the press molding method according to the present invention
- FIG. 4 (b) is the state of the powder particles before vibration is applied. It is a figure which shows typically.
- BEST MODE FOR CARRYING OUT THE INVENTION compression molding of magnet powder is performed using a die formed of a non-magnetic material.
- the die used in the present invention has a through hole (die hole) for forming a cavity, and a plurality of yoke members arranged on both sides of the die hole.
- the apparent density of the alloy powder (referred to as the “temporary compact (compact) density”) There are things.) If a pulse magnetic field is applied at a stage when the value of the ⁇ ⁇ ⁇ becomes a predetermined value or more, a molded body having a high degree of orientation can be manufactured with a high yield.
- the pulse magnetic field is applied only after the density of the temporary formed body reaches a predetermined value that is equal to or more than 4% of the true density. If a pulse magnetic field is applied after the density of the temporary compact reaches a certain level, powder flow is unlikely to occur during the subsequent compression and compaction process, and orientation disorder is suppressed.
- the density of the temporary compact is too high when the pulsed magnetic field is applied, the space formed around the individual powder particles is too small, and the powder particles are in strong contact with each other. However, after a pulse magnetic field is applied, the powder particles cannot change direction. If the density of the temporary compact exceeds a certain value and becomes too high, it becomes difficult to apply a strong pulsed magnetic field and obtain a magnet with excellent magnetic properties. It is desirable that the density of the temporarily formed body at the start of application of the magnetic field be 53% or less of the true density.
- the frictional resistance between the alloy powders can be reduced by applying the vibration. Therefore, it is preferable to apply the orientation magnetic field while the alloy powder is being vibrated. When vibration is applied to the alloy powder in the compression molding process, the magnetic field can be sufficiently oriented even after the density of the temporary compact has been increased.
- the frictional resistance between the alloy powders can be reduced by applying an alternating damping pulse magnetic field, and the magnetic field can be oriented sufficiently even after the density of the temporary compact increases.
- the rare earth alloy powder used in the present embodiment will be described. Although there are various rare earth alloy powders that can be used in the present invention, R-Fe-B based rare earth alloys are preferably used. The composition and manufacturing method of R—Fe—B based rare earth alloys are described, for example, in US Pat. No. 4,770, R23 and US Pat. No. 4,792,368.
- Nd or Pr is mainly used as R, and F e may be partially replaced by a transition element (for example, Co).
- B may be replaced by C.
- the Nd—Fe—B system solidified alloy (density 7.5 gZcm 3 ) produced by the rapid Use a powder having an average particle size of 1.5 / m to 6 m.
- the surface of the alloy powder is preferably coated with a lubricant such as zinc stearate. Specifically, it can be prepared by the following methods.
- C the composition is as follows: Nd: 3% by mass, B: 1.0% by mass, Dy: 1.2% by mass, AI: 0.1% by mass.
- the illustrated press forming apparatus 10 includes a base plate 12, and the base plate 12 is supported by a plurality of legs 14.
- a die 16 is arranged above the base plate 12.
- the lower surface of the die 16 is connected to the connecting plate 20 via a pair of guide posts 18 penetrating the base plate 12.
- the connecting plate 20 is connected to a lower hydraulic cylinder (not shown) via a cylinder rod 22. Therefore, the die 16 can be moved vertically by the lower hydraulic cylinder.
- a die hole (penetration) penetrating in the vertical direction is almost at the center of the die 16.
- a tip 24 is formed, a lower punch 26 is inserted into the die hole 24 from below, and a cavity 28 is formed in the die hole 24.
- the die 16 has a pair of yoke members 16a and 16b facing each other so as to sandwich the die hole 24 along the direction of the alignment magnetic field (X direction).
- the yoke members 16a and 16b are made of a material having high magnetic permeability such as carbon steel, and are made of, for example, parmundum.
- the die 16 is formed of a non-magnetic material, and a concave portion in which the yoke members 16a and 16b are fitted is formed on the side surface of the die 16.
- nonmagnetic material refers to a material having a saturation magnetization of 0.2 Tesla (T) or less.
- the length 16c of the yoke is set to be equal to or longer than the length 24a of the sandwiching / cavity (120%). By doing so, the directions of the lines of magnetic force to be oriented can be made more parallel.
- the lower punch 26 is disposed on the vibration device 30, and the vibration device 30 is disposed on the plate 12. Therefore, the lower punch 26 is fixed on the base plate 12, but can be vibrated in the vertical direction, that is, in the press direction by the vibrating device 30.
- the vibration device 30 for example, a vibration device manufactured by Daiichi Co., Ltd. can be used.
- An upper punch plate 32 is arranged above the die 16. On the lower surface of the upper punch plate 32, an upper punch 34 is provided at a position where it can be inserted into the cavity 28.
- a cylinder rod 36 is provided on the upper surface of the upper punch plate 32.
- An upper hydraulic cylinder (not shown) is connected to the cylinder rod 36.
- a pair of guide posts 38 provided in the vertical direction are inserted near both ends of the upper punch plate 32, and the lower end of the guide post 38 is connected to the upper surface of the die 16.
- the upper punch plate 32 is vertically movable by the upper hydraulic cylinder while being guided by the guide post 38, and accordingly, the upper punch 34 is vertically movable, and is inserted into the cavity 28.
- the powder is compressed by the lower punch 26 and the upper punch 34 in the cavity 28 to form a compact.
- a magnetic field generator 40 for orienting the powder in the cavity 28 is provided.
- the magnetic field generator 40 has a pair of yokes 42 a and 42 b symmetrically arranged so as to sandwich the die 16 from both sides.
- the yokes 42a and 42b are also formed of a material having high magnetic permeability such as carbon steel, like the yoke members 16a and 16b of the die 16.
- Coils 44a and 44b are wound around the yokes 42a and 42b, respectively, and when energized, a pulse magnetic field is formed in a direction indicated by an arrow X to orient the powder in the cavity 28.
- the pulse magnetic field means the magnetic field strength Refers to a magnetic field in which the period during which is 90% or more of the peak value is O.2 seconds or less.
- the press direction and the direction of the orientation magnetic field are perpendicular to each other, and the applied magnetic field strength is, for example, 3 T at the center of the cavity.
- the illustrated press device 1 # is a withdrawal type press device that moves the die 16 up and down, but a double-press type press device that moves both the upper punch 34 and the lower punch 26 may be used.
- the cavity 24 is filled with the above-mentioned alloy powder.
- Filling of the alloy powder is performed by various known methods. For example, a method of filling the alloy powder using its own weight using a feeder box is simple and preferable. By using this method, the alloy powder can be filled into the cavity at an appropriate apparent density (for example, 1. gZ cmS Z. 5 gZcm 3 ). After the cavity is filled with the alloy powder, the amount of the alloy powder to be filled into the cavity 28 can be made substantially constant by, for example, moving a cutting bar along the surface of the die 16. For example, a powder feeding method described in JP-A-2001-9595 can be preferably used.
- the alloy powder in the cavity 28 is uniaxially pressed by moving the upper punch 34 and the lower punch 26 or the lower punch 26 up and down.
- the upper punch 34 is lowered, but when the upper punch 34 is lowered, You can also raise the lower punch 26.
- vibration mechanical vibration
- the alloy powder is vibrated to thereby generate a bridge between the powder particles. Destroy the steel structure and make the powder particles more mobile. This will be described with reference to FIGS. 4 (a) and 4 (b).
- the alloy powder has the same apparent density, and the alloy powder is in a state of being more easily moved when vibration is applied than when vibration is not applied. It is considered that the friction between the alloy powders changes from static friction to dynamic friction by applying vibration to the alloy powder, and the frictional resistance decreases.
- the vibration is preferably applied from the pressing surface (ie, the bottom surface of the upper punch and / or the top surface of the lower punch). Especially mechanically the lower punch.
- the use of the vibrating structure can efficiently impart kinetic energy to the alloy powder and simplify the structure of the press device.
- the amplitude of the vibration is preferably between 0.001 mm and 0.2 mm. If the vibration amplitude is less than 0.001 mm, the bridge structure of the powder particles may not be sufficiently destroyed. If the vibration amplitude is more than 0.2 mm, the powder particles may enter the gap between the die and the lower punch, for example. This is because it becomes easy to get stuck and damages the die and lower punch.
- the frequency of the vibration is preferably 5 Hz or more and 10 ⁇ 0 Hz or less. If the frequency of vibration is less than 5 Hz, the bridge structure of the powder particles may not be sufficiently destroyed.On the other hand, if the frequency of vibration exceeds 1 000 Hz, the device that generates vibration is too costly. Not practical.
- vibration is applied so as to obtain the state shown in FIG. 2 (b).
- the vibration may be stopped at the time when the apparent density reaches a predetermined value due to the compression, or may be continued after reaching the desired value.
- the pulse magnetic field (maximum magnetic field strength: Apply 2 to 5 T, pulse width: 0.05 seconds, and apply vibration (amplitude: 0.01 to 0.1 mm, frequency: 40 to 8 Hz) from the lower punch.
- Vibration fills the alloy powder, it is preferable to present the formation of Canon Activity by lowering the upper punch to the forming density is 3. 55 0 3 ⁇ 3. 90 g / cm 3. Further, it is preferable to apply the pulsed magnetic field in a state in which the upper and lower punches are stopped and while applying vibration. Then, in the present embodiment, the density of the final molded product 4. 0 g Zc m 3 ⁇ 4. 4 pressure rejoin so that gZ cm 3.
- the size of the compact can be, for example, 6 mm x 4 mm x 2 mm.
- a sintered body can be obtained by performing aging treatment at 6 ° 0 ° for 1 to 3 hours.
- the timing of applying the pulse magnetic field is set to a point in time when the density of the temporary compact reaches a predetermined value of 3.55 gX cm 3 or more, the residual magnetic flux density further increases by applying vibration.
- the timing for applying the pulsed magnetic field is preferably set when the density of the preliminarily formed body reaches a predetermined value of 3.6 gZ cm 3 or more, and 3. When the density is set to 8 cm 3 or more, a sufficient effect is obtained. can get. However, when the pulsed magnetic field is applied after the density of the preliminarily compact exceeds 4.0 gZ cm 3 , the residual magnetic flux density tends to decrease, and it is known that the powder particles are not sufficiently oriented. . From the above, the density of the temporary compact was 3.
- the pulse magnetic field May be applied a plurality of times, or a static magnetic field may be applied together with the pulse magnetic field.
- the degree of orientation can be made uniform by adjusting the application timing of the pulse magnetic field. .
- the magnetic powder rotates by the magnetic field whose direction is reversed, and can destroy the bridge structure formed by the alloy powder filled in the cavity.
- the destruction of such a bridge structure can be performed not only by the application of the alternating decay pulse but also by the application of the inversion pulse.
- a sintered body was produced in the same manner as in the above embodiment. Specifically, a sintered body was produced under the following conditions.
- Raw material powder Composition: Nd: 30% by mass, B: 1.0% by mass, Dy: 1.2% by mass, A ⁇ : 0.2% by mass, Co: 0.9% by mass, balance Used a powder that had been coarsely ground by hydrogen grinding and then finely ground by a jet mill.
- the peak intensity was 3 as the orientation magnetic field. Compression molding was performed by applying a pulse magnetic field of T (pulse width: 0.05 seconds).
- Shape and size of compact 6mm X40mm X20mm Sintering conditions: After sintering at about 105 ° C for 5.5 hours in Ar atmosphere, about 500 ° in Ar atmosphere Perform aging treatment for 3 hours at C. .
- a sintered body was prepared in the same manner as in the example except that a static magnetic field of 1 T was applied as an orientation magnetic field.
- the surface magnetic flux density was measured at two points (center and end) along the direction of the orientation magnetic field.
- the difference in surface magnetic flux density was 10%, but in the comparative example, the difference in surface magnetic flux density was 10%.
- the Nd—Fe—B-based alloy powder produced by a strip casting method which has excellent magnetic properties but is particularly low in fluidity, is used.
- rare earth alloy powder produced by another method is used. Needless to say, the effects of the present invention can be obtained after use.
- the alloy powder is used after being subjected to a surface treatment with a lubricant.
- a surface treatment with a lubricant.
- other surface treatments may be performed.
- granulated powder may be used. Since the granulated powder can be disintegrated using vibration and / or an orientation magnetic field, a sufficient degree of orientation can be obtained.
- the present invention there is provided a method for right-angle press forming rare earth alloy powder, which enables production of a sintered magnet having excellent magnetic properties.
- the compact obtained by the press molding method of the present invention has a sufficiently high compactness (the compact has a compact density and the degree of orientation of the alloy particles is sufficiently high, so that a sintered magnet having excellent magnetic properties can be obtained. According to the present invention, the productivity of sintered magnets having different shapes can be significantly improved.
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- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Mechanical Engineering (AREA)
- Powder Metallurgy (AREA)
- Manufacturing Cores, Coils, And Magnets (AREA)
Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AU2003236275A AU2003236275A1 (en) | 2002-04-12 | 2003-04-04 | Method for press molding rare earth alloy powder and method for producing sintered object of rare earth alloy |
DE10392157T DE10392157B4 (de) | 2002-04-12 | 2003-04-04 | Verfahren zum Pressen eines Seltenerdmetall-Legierungspulvers und Verfahren zur Herstellung eines Sinterkörpers aus einer Seltenerdmetall-Legierung |
US10/489,338 US7045092B2 (en) | 2002-04-12 | 2003-04-04 | Method for press molding rare earth alloy powder and method for producing sintered object of rare earth alloy |
Applications Claiming Priority (2)
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JP2002-110950 | 2002-04-12 | ||
JP2002110950 | 2002-04-12 |
Publications (1)
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WO2003086687A1 true WO2003086687A1 (fr) | 2003-10-23 |
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PCT/JP2003/004370 WO2003086687A1 (fr) | 2002-04-12 | 2003-04-04 | Procede permettant de mouler a la presse de la poudre d'alliage de terre rare, et procede pour produire un objet fritte en alliage de terre rare |
Country Status (5)
Country | Link |
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US (1) | US7045092B2 (ja) |
CN (1) | CN100528420C (ja) |
AU (1) | AU2003236275A1 (ja) |
DE (1) | DE10392157B4 (ja) |
WO (1) | WO2003086687A1 (ja) |
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EP1557850A2 (en) * | 2004-01-26 | 2005-07-27 | TDK Corporation | Method for compacting magnetic powder in magnetic field, and method for producing rare-earth sintered magnet |
WO2019163766A1 (ja) * | 2018-02-23 | 2019-08-29 | Tdk株式会社 | 希土類磁石の製造方法 |
CN115635078A (zh) * | 2022-12-07 | 2023-01-24 | 成都大学 | 一种快速冷却的粉末冶金模具 |
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- 2003-04-04 WO PCT/JP2003/004370 patent/WO2003086687A1/ja active Application Filing
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EP1557850A2 (en) * | 2004-01-26 | 2005-07-27 | TDK Corporation | Method for compacting magnetic powder in magnetic field, and method for producing rare-earth sintered magnet |
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Also Published As
Publication number | Publication date |
---|---|
US7045092B2 (en) | 2006-05-16 |
CN1533313A (zh) | 2004-09-29 |
CN100528420C (zh) | 2009-08-19 |
US20040241033A1 (en) | 2004-12-02 |
DE10392157T5 (de) | 2004-10-28 |
DE10392157B4 (de) | 2007-01-25 |
AU2003236275A1 (en) | 2003-10-27 |
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