WO2002030595A1 - Procede de fabrication par coulee de bandes d'un alliage brut pour aimant permanent nanocomposite - Google Patents
Procede de fabrication par coulee de bandes d'un alliage brut pour aimant permanent nanocomposite Download PDFInfo
- Publication number
- WO2002030595A1 WO2002030595A1 PCT/JP2001/008317 JP0108317W WO0230595A1 WO 2002030595 A1 WO2002030595 A1 WO 2002030595A1 JP 0108317 W JP0108317 W JP 0108317W WO 0230595 A1 WO0230595 A1 WO 0230595A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- alloy
- cooling roll
- raw material
- molten
- amorphous
- Prior art date
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/02—Amorphous alloys with iron as the major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0611—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by a single casting wheel, e.g. for casting amorphous metal strips or wires
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y25/00—Nanomagnetism, e.g. magnetoimpedance, anisotropic magnetoresistance, giant magnetoresistance or tunneling magnetoresistance
-
- 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
-
- 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
- H01F1/0579—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B with exchange spin coupling between hard and soft nanophases, e.g. nanocomposite spring magnets
-
- C—CHEMISTRY; METALLURGY
- 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
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/03—Amorphous or microcrystalline structure
-
- 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
- H01F1/058—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IVa elements, e.g. Gd2Fe14C
Definitions
- the present invention relates to a raw material alloy for a permanent magnet used for various types of cameras, sensors, sensors, speakers, and the like, and a method for producing the same. More specifically, the present invention relates to a nano component manufactured by using a strip casting method. The present invention relates to a raw material alloy for a jet-type permanent magnet and a method for producing the same. Background art
- Nanocomposite permanent magnets with magnetically coupled tissue structures have been developed.
- the powder of the nanocomposite permanent magnet is used as an isotropic bonded magnet by being solidified into a predetermined shape using a resin material.
- a rapidly solidified alloy having an amorphous structure or a structure containing a large amount of amorphous phase is often used as a starting material.
- the rapidly solidified alloy is crystallized by heat treatment, the average crystal grain size in the end is 1 0- 9 n!
- the microstructure of the magnetic alloy after the crystallization heat treatment largely depends on the microstructure of the rapidly solidified alloy before the crystallization heat treatment. Therefore, the alloy melt that determines the microstructure of the rapidly solidified alloy (such as the proportion of the amorphous phase) is determined. How to select the quenching condition of the hot water is important for producing nanocomposite magnets with excellent magnetic properties.
- a rapid cooling method using an apparatus as shown in FIG. 1 is known.
- a molten alloy is sprayed from a nozzle having an orifice at the bottom onto a rotating orifice formed by copper or the like, and the molten alloy is rapidly cooled to form an amorphous ribbon-shaped solidified alloy. Make it.
- the molten alloy melted in the melting furnace is poured into a container having an injection nozzle at the bottom, and then the molten metal is injected from a nozzle by applying a certain pressure to the molten metal in the container.
- the jet-cast method By injecting the molten metal through the nozzle while applying pressure in this way, a strip of molten metal (flow of molten metal) having a relatively high flow velocity can be approximately vertically injected near the uppermost portion of the rotating roll.
- the injected molten metal forms a paddle (puddle) on the surface of the rotating roll, and the roll contact surface of this paddle is rapidly cooled to form a thin strip. Is produced.
- the processing rate is increased to a level that can be used for industrial mass production (for example, about 1.5 kg / min or more)
- the injection rate increases as the molten metal supply rate (melt injection speed) increases.
- Nozzle wear becomes severe.
- the supply amount of the molten metal fluctuates during the processing, so that a stable quenched state cannot be maintained.
- the cost of the nozzle becomes huge.
- the injection speed of the molten metal is restricted by the diameter of the nozzle, there is a problem that it is difficult to increase the throughput.
- a strip casting method is also known.
- a molten alloy is supplied from a melting furnace onto a chute (tundish), and the molten alloy on the chute is brought into contact with a cooling roll to produce a quenched alloy.
- the chute is a molten metal guiding means for controlling the flow velocity of the molten metal so as to temporarily store the molten metal and rectifying the flow, thereby realizing a stable and continuous supply of the molten metal to the cooling rolls.
- the molten metal in contact with the outer peripheral surface of the cooling roll moves along the roll peripheral surface as if dragged by the rotating cooling roll, and is cooled in this process.
- the cooling of the molten metal is substantially completed on the roll.
- the strip casting method does not use a jet nozzle as in the jet casting method, but continuously supplies the molten alloy onto a rotating roll via a chute, so it is suitable for mass production, and the production cost is low. It is possible to achieve a reduction.
- the strip casting method is unsuitable for producing an amorphous solidified alloy because the amount of molten alloy supplied to the roll is large and the quenching rate tends to be slow. When the quenching rate is slow, an alloy that does not contain much amorphous phase (that is, contains a lot of crystalline structure) is produced. Easy to do. If there is a large amount of crystalline structure in the alloy structure, the crystal structure becomes coarse in the subsequent crystallization heat treatment, with the already crystalline part being the nucleus, so that a nanocomposite magnet with excellent magnetic properties can be produced. You can't get it.
- the strip casting method is often used to produce a metal piece that has been completely crystallized (for example, Japanese Patent Application Laid-Open No. H08-229641).
- the quenched alloy thus obtained is generally used as a raw material alloy for sintered magnets having the R 2 Fe 14 B phase as a main phase, and cannot be used as a raw material alloy for nanocomposite magnets.
- the present invention has been made in view of the above circumstances, and has as its object to provide a low-cost raw material alloy for a nanocomposite permanent magnet having good magnetic properties. Disclosure of the invention
- Method for manufacturing a magnet material alloy of the present invention F eioa- x - y - z R x Q y M z (where R is P r, Nd, 1 or more kinds of D y or T b, Q is One or two of B or C, M is Co, Al, Si, Ti, V, Cr, Mn, Ni, Cu, Ga, Zr, Nb, Mo, Ag, One or more of Pt, Au, and Pb, where x, y, and z in the formula are 1 atomic% ⁇ x ⁇ 6 atomic%, 15 atomic% ⁇ y ⁇ 30 atomic%, respectively.
- a predetermined contact width along a direction of the axis of the cooling roll under vacuum or reduced pressure So as to contact with the cooling roll, before Forming a ribbon-shaped alloy containing an amorphous structure by using a strip casting method of cooling while moving the molten alloy along the outer peripheral surface of the cooling roll by rotating the cooling roll.
- the cooling roll is rotated at a peripheral speed of 3 mZ seconds or more and less than 20 mZ seconds, and the supply speed per unit contact width is 0.2 kg_minZcm or more and 5.2 kg / min Zcm or less.
- the molten alloy is continuously supplied to the cooling roll as described above.
- the molten alloy is supplied to the cooling roll at a supply speed of 3 kgZmin or more.
- the molten alloy is brought into contact with the cooling roll using a shot capable of controlling at least a part of the flow of the molten alloy toward the cooling port, and the chute is provided with a cooling medium.
- a plurality of molten metal discharge portions having a predetermined tapping width are provided in the vicinity of the roll and along the axial direction of the cooling roll.
- a plurality of ribbon-shaped alloys are formed from the contacted molten alloy.
- the predetermined contact width is from 0.5 cm to 10.0 cm.
- the ribbon-shaped alloy has a metal structure composed of an amorphous structure of substantially 60% by volume or more.
- the method includes a step of continuously crushing the ribbon-shaped alloy and collecting the crushed alloy so as to have a bulk density of 1 gZcm 3 or more.
- Material alloy for a magnet of the invention the be any work made by the material alloy for a magnet by the manufacturing process, the intrinsic coercive force H c j before heat treatment for crystallization is not more than 10 k A / m. In a preferred embodiment, the thickness of the raw material alloy for a magnet is 70 to 250 m.
- the method for evaluating a raw material alloy for a magnet includes the steps of: measuring a coercive force of a solidified alloy produced by quenching a molten metal of a magnetic alloy; and Estimating the proportion of amorphous contained in the solidified alloy.
- the method for evaluating a raw material alloy for a magnet includes the steps of: measuring a crystallization heating value of a solidified alloy produced by quenching a melt of a magnetic alloy; andbased on the measured crystallization heating value. Estimating the proportion of amorphous material contained in the solidified alloy.
- the method of manufacturing a raw material alloy for a magnet according to the present invention includes the steps of: estimating a proportion of amorphous contained in the solidified alloy by using any one of the above-described evaluation methods; Crystallization heat treatment of the solidified alloy produced under the condition of not less than the above ratio.
- FIG. 1 is a side view showing a nozzle and a rotating roll in a conventional jet casting method.
- FIG. 2 is a cross-sectional view showing the entire configuration of an apparatus for producing a quenched alloy by a strip casting method according to an embodiment of the present invention.
- FIG. 3 is a top view showing a cooling roll and a chute in the apparatus shown in FIG.
- FIG. 4 is a thermal analysis curve of the sample powder before heat treatment produced in the example.
- Figure 5 shows the magnetic hiss of the sample powder before heat treatment produced in the example. It is a teresis loop.
- FIG. 6 is an enlarged view near the origin of FIG. BEST MODE FOR CARRYING OUT THE INVENTION
- the inventor of the present invention aimed at obtaining a raw material alloy for a nanocomposite type permanent magnet which has a low production cost and exhibits good magnetic properties by performing a heat treatment, and rapidly solidified a large amount of an amorphous phase.
- the method of producing the alloy was studied.
- By using the conventional jet casting method it is possible to produce a quenched alloy containing many amorphous phases, which is suitable as a raw material alloy for nanocomposite permanent magnets.
- Many problems arise as described above. Therefore, the present inventor has dared to select a strip cast method in which an amorphous phase is less likely to be formed than a jet cast method, and to use a strip cast method to produce a solidified alloy containing a large amount of an amorphous phase. The method was examined.
- the composition formula was F e 10 .
- z R x Q y M z (where R is one or more of Pr, Nd, Dy or Tb, Q is one or two of B or C, M is Co, Al, S i , Ti, V, Cr, Mn, Ni, Cu, Ga, Zr, Nb, Mo, Ag, Pt, Au, Pb , Y, and z are 1 atomic% ⁇ x ⁇ 6 atomic%, 15 atomic% ⁇ y ⁇ 30 atomic%, 0 atomic% ⁇ z ⁇ 7 thick%, respectively.
- We found that a molten metal with high amorphous forming ability could be obtained, and decided to rapidly cool it by strip casting.
- the present inventors have increased the proportion of the amorphous phase when the molten alloy having the above specific composition is quenched by the strip method.
- the quenching conditions for reducing the temperature were studied in detail.
- the supply speed per unit contact width is set to 0.2 kg / min Z on the cooling roll rotating at a peripheral speed of 3 m / sec or more and less than 2 O mZ seconds
- the strip casting method in which the molten metal is continuously supplied at a pressure of not less than cm and not more than 5.2 kg / min / cm, a raw material alloy for permanent magnet powder having an amorphous structure occupying 60% by volume or more can be produced. all right. Also, according to this method, it is possible to produce a quenched alloy with a molten metal processing amount of 3 kg / min or more.
- an appropriate range of the molten metal supply speed is defined by the supply speed per unit contact width as described above.
- the molten metal comes into contact with the cooling roll so as to have a predetermined contact width along the axial direction of the cooling roll.However, the cooling condition of the molten metal largely depends on the molten metal supply speed per the above unit contact width. Because you do.
- the supply speed per unit contact width is typically defined as the supply speed (unit: kg / min) of the molten metal supplied on the melt for guiding the molten metal. It is divided by the width (that is, the contact width of the molten metal) (unit: cm).
- the value indicates a value obtained by dividing the supply speed of the molten metal supplied to the chute by the total width of each discharge portion.
- the supply speed per unit contact width is set to be 0.2 kgZmin / cm or more and 5.2 kgZmin / cm or less.
- the supply speed is set to about 0.5 kgZminZcm or more. As a result, it is possible to achieve a processing amount of about 3 kgZmin or more.
- the quenching containing a large amount of the amorphous structure is performed.
- the alloy was produced with high productivity. Since the strip casting method does not use nozzles that significantly increase the manufacturing cost unlike the jet casting method, the cost of the nozzles is unnecessary, and production does not stop due to nozzle blockage accidents.
- the obtained quenched alloy is subjected to a heat treatment for crystallization (hereinafter sometimes referred to as crystallization heat treatment) in a temperature range of about 550 ° C to about 750 ° C.
- crystallization heat treatment a heat treatment for crystallization
- a crystal structure in which a soft magnetic phase composed of one or two of the Fe phase or Fe 3 B type compound and the compound having the R 2 Fe 14 B type crystal structure coexist is 9
- a nanocomposite permanent magnet occupying 0% or more and having an average crystal grain size of 10 nm to 50 nm and having good magnetic properties was obtained.
- FIG. 2 shows a quenching apparatus 1 for producing a quenched alloy by a strip casting method according to an embodiment of the present invention.
- the quenching device 1 is connected to a main chamber 10 whose inside can be brought into a vacuum state or a reduced pressure state in an inert gas atmosphere, and a shirt 28 that can be opened and closed to the main chamber 10. And a sub-chamber 30.
- a melting furnace 12 for melting the alloy raw material Inside the main chamber 10, a melting furnace 12 for melting the alloy raw material, a cooling roll 14 for rapidly cooling and solidifying the molten alloy 3 supplied from the melting furnace 12, and a melting furnace 1
- a chute (tundish) 16 as a molten metal guiding means for guiding the molten metal 3 from 2 to the cooling roll 14, and a collecting means 20 for recovering a thin alloy strip solidified and separated from the cooling roll 14 are provided inside the main chamber 10, a melting furnace 12 for melting the alloy raw material, a cooling roll 14 for rapidly cooling and solidifying the molten alloy 3 supplied from the melting furnace 12, and a melting furnace 1
- a chute (tundish) 16 as a molten metal guiding means for guiding the molten metal 3 from 2 to the cooling roll 14, and a collecting means 20 for recovering a thin alloy strip solidified and separated from the cooling roll 14 are provided. Is provided.
- the melting furnace 12 can supply the molten metal 3 produced by melting the alloy raw material to the shot 16 at a substantially constant supply amount. This supply amount can be arbitrarily adjusted by controlling the operation of tilting the melting furnace 12 or the like.
- the outer peripheral surface of the cooling roll 14 is formed of a material having good heat conductivity such as copper, and has a diameter of 30 cm to 100 cm and a width of 15 cm to 100 cm. .
- the cooling roll 14 can be rotated at a predetermined rotation speed by a driving device (not shown). By controlling the rotation speed, the peripheral speed of the cooling roll 14 can be arbitrarily adjusted.
- the cooling rate by the quench unit 1, by selecting and rotation speed of the cooling roll 1 4 can be controlled in the range of about 1 0 2 KZ sec to about 2 X 1 0 4 K Bruno sec.
- the end 16a of the chute 16 is disposed at a position having a certain angle ⁇ ⁇ ⁇ ⁇ with respect to a line connecting the top of the cooling roll 14 and the center of the roll.
- the molten metal 3 supplied on the chute 16 is supplied from its end 16a to the cooling roll 14 by its own weight.
- the chute 16 is made of ceramics or the like, and temporarily stores the molten metal 3 continuously supplied at a predetermined flow rate from the melting furnace 12 to delay the flow velocity and rectify the flow of the molten metal 3 be able to.
- the flow on the surface of the molten metal in the molten metal 3 supplied to the chutes 16 is selectively dammed. By providing a dam plate that can be stopped, the rectifying effect can be further improved.
- the molten metal 3 can be supplied in a state of being spread to a substantially uniform thickness over a certain width in the body length direction (axial direction) of the cooling roll 14.
- the chute 16 has a function of adjusting the temperature of the molten metal 3 immediately before reaching the cooling roll 14 in addition to the above function. It is desirable that the temperature of the molten metal 3 on the chute 16 be 100 K or more higher than the liquidus temperature. If the temperature of the molten metal 3 is too low, primary crystals, which adversely affect the alloy properties after quenching, are locally nucleated and may remain after solidification.
- the temperature of the molten metal staying on the chute 16 can be controlled by adjusting the temperature of the molten metal at the time of pouring from the melting furnace 12 into the shot 16 and the heat capacity of the chute 16 itself.
- a chute heating facility (not shown) may be provided.
- FIG. 3 shows a shot 16 of the present embodiment.
- the shot 16 of the present embodiment has a plurality of discharge portions 16 provided at a predetermined interval W2 at an end 16a arranged so as to face the outer peripheral surface of the cooling roll 14.
- the width (outlet width) W1 of the discharge portion 16b is preferably set to 0.5 cm to 10.0 cm, and more preferably set to 1.5 cm to 4.0 cm. .
- the tapping width W1 is set to 2 cm.
- the molten metal 3 supplied on the shout 16 contacts the cooling roll 14 along the axial direction A of the cooling roll 14 while having a width substantially equal to the width W1.
- the molten metal 3 contacting the cooling roll 14 with the tapping width W1 moves on the roll peripheral surface (as if being pulled up by the cooling roll 14) as the cooling roll 14 rotates. Is cooled.
- the distance between the end 16a of the chute 16 and the cooling roll 14 is preferably set to 3 mm or less.
- the gap W2 between adjacent discharges is preferably set between 1 cm and 10 cm.
- the form of the chute 16 is not limited to the above-described form, and may have a single discharge portion, or may have a larger tapping width.
- FIG. 2 is referred to again.
- the molten alloy 3 solidified on the outer peripheral surface of the cooling roll 14 is separated into a ribbon-shaped solidified alloy 3 a from the cooling hole 14.
- the exfoliated solidified alloy 3a is crushed and recovered in the recovery device 20.
- the recovery device 20 includes a rotating blade 22 for crushing the ribbon-shaped solidified alloy 3a.
- the rotating blade has a plurality of blades formed of, for example, stainless steel, and is rotated at a speed of about 500 to 100 rpm by a driving device (not shown).
- the strip-shaped solidified alloy 3 a from which the cooling roll 14 has been peeled off is guided to the rotary blade 22 by the guide member 24. Since the solidified alloy 3a produced in this embodiment using the strip cast method is relatively thick (70! To 250 m), the rotational vibration is larger than that of the relatively thin solid alloy obtained by the jet cast method. It is easy to crush by 22.
- the shape of the solidified alloy 5 crushed by the rotating blades 22 has an aspect ratio closer to 1. Therefore, the crushed solidified alloy 5 can be accommodated in the collection container 26 with a high bulk density.
- the solidified alloy 5 is preferably recovered with a bulk density of at least 1 g / cm 3 . As a result, the efficiency of the collection operation can be improved.
- the recovery container 26 in which a predetermined amount of the crushed and solidified alloy 5 is stored is sent to the sub-champ 30 by a moving means (not shown) such as a belt conveyor.
- a moving means such as a belt conveyor.
- the inside of the sub-chamber 30 is previously kept under the same vacuum as the main chamber 10 or under reduced pressure using an inert gas. Thereby, the vacuum state or the reduced pressure state in the main chamber 10 can be maintained.
- the shirt 28 is closed, and the airtightness of the main chamber 10 is maintained.
- the collection container 26 is covered with a lid 32 by a device (not shown). In this way, the crushed alloy 5 sealed in the collection container 26 is carried out by opening the openable shirt 34.
- the strip casting method does not use a nozzle unlike the jet casting method, and there are no problems such as restrictions on the injection speed due to the nozzle diameter and clogging of the molten metal due to solidification at the nozzle portion, so mass production is possible. Suitable for. Also, since there is no need for a nozzle heating unit or a pressure control mechanism for controlling the melt head pressure, initial equipment investment and running costs can be reduced.
- the strip casting method can reduce the running cost because the shots can be used repeatedly.
- the mouth is rotated at a relatively low speed, and the amount of molten metal coming out is larger than in the jet casting method. Therefore, the thickness of the ribbon can be increased, and the recovery is easy. Become.
- Rare earth element R is an essential element for R 2 Fe 14 B, which is a hard magnetic phase necessary for developing permanent magnet properties.
- R includes one or more of Pr and Nd, Dy, and Tb.
- some other rare earth elements other than these may be substituted. If the composition ratio of R is less than 1 atomic%, the effect of coercive force development is unfavorably small. On the other hand, if the composition ratio of R is 6 atomic% or more, the hard magnetic phase R 2 Fe 14 B is not generated, and the coercive force is significantly reduced. For these reasons, it is preferable that the composition ratio X of the scale is 1 ⁇ x ⁇ 6.
- Q is one or two of B (boron) or C (carbon).
- B is an essential element in iron-based borides such as Fe 3 B which is a soft magnetic phase which is a main phase of the nanocomposite permanent magnet material, and R 2 Fe 14 B which is a hard magnetic phase. If the composition ratio y of B is out of the range of 15 to 30 at%, permanent magnet characteristics are not exhibited. Therefore, the composition ratio y of B is preferably 15 ⁇ y ⁇ 30 at%.
- F e 3 B also also for that contains F e 3 B and hard identification F e 3. 5 B.
- the residual content of the above elements is occupied by Fe, and by replacing a part of Fe with Co, the squareness of the demagnetization curve is improved and the maximum energy product (BH) max can be improved.
- Al, Si, V, C] Mn, Ni, Cu, Ga, Zr, Nb, Mo, Ag, Ta, W, Pt, Au, a kind of Pb or Permanent magnet properties can be improved by substituting two or more types.
- Co and A1 Si, V, Cr, Mn, Ni, Cu, Ga, Zr, Nb, Mo, Ag, Ta, W, P
- the preferable range is 0 ⁇ z ⁇ 7 atomic%. Since a more pronounced effect is obtained when z is 0.5 atomic% or more, a more preferable range is 0.5 ⁇ z ⁇ 7 atomic%.
- a molten alloy having the above-described specific composition is rapidly cooled and solidified by a strip casting method using a rapid cooling device 1 shown in FIG. 2 to produce a ribbon-shaped alloy.
- the supply speed per unit contact width of the molten alloy is 0.2 kg / unit for a cooling roll that rotates at a peripheral speed of 3 mZ seconds or more and less than 2 OmZ seconds under vacuum or reduced pressure in an inert gas atmosphere. Supplied at minZcm or more and 5.2 kg Zm incm or less. In this way, it is possible to produce a quenched alloy having an amorphous structure of 60% by volume or more. By performing crystallization heat treatment on such a raw material alloy having an amorphous structure at a high ratio, good magnetic properties can be obtained.
- a nanocomposite magnet can be manufactured.
- the reason why the peripheral speed of the cooling roll is set to 3 mZ seconds or more and less than 2 OmZ seconds is that if the roll peripheral speed is less than 3 msec, the cooling capacity is insufficient and the non-cooling capacity is not more than 60 vol%. If a quenched alloy containing a crystalline structure cannot be obtained, and if the speed is more than 20 m / sec, it will be difficult to pull up the molten metal by the mouth, and the cooling alloy will be scattered in the form of flakes. For it will be difficult.
- the optimum peripheral speed may vary depending on the structure, material, and molten metal supply speed of the chill roll.
- the peripheral speed of the chill roll is preferably set to 5 mZ sec to 15 m / sec. More preferably, it is set to 6 m / sec to 10 mZ second.
- the reason why the feed rate per unit contact width is set to 5.2 kg / min / cm or less is that if the feed rate exceeds 5.2 kg / min / cm, the specified cooling rate is obtained. This is because a quenched alloy containing 60% by volume or more of amorphous cannot be produced.
- An appropriate range of the feeding speed per unit contact width may vary depending on a roll peripheral speed, a roll structure, and the like, but it is preferably 4.0 kgZminZcm or less, and 3.0 kgZminZcm or less. It is more preferred that:
- the reason why the supply speed per unit contact width is set to 0.2 SkgZm in / cm or more is that if the supply speed is smaller than 0.2 kgZminZcm, the strip casting method uses Enough As a result, the molten metal is not supplied steadily by the flow, and sufficient contact between the roll and the molten metal cannot be obtained. As a result, the molten metal paddle formed on the cooling roll is not stably generated. As a result, a strip-shaped quenched alloy is formed in pieces, resulting in an uneven quenched state. If the quenched state fluctuates in this manner, it becomes impossible to stably obtain a quenched alloy for a nanocomposite containing a predetermined amount of amorphous.
- the melt supply speed be 3 kgZmin or more.
- the feed rate per unit contact width must be at least 0.2 kgZminZcm and not more than 5.2 kgZmin / cm as described above. It is necessary to properly select the shape of the shout, the shape of the cooling roll, the peripheral speed, etc. so that the molten metal of 3 kg or more per minute can be processed while satisfying the above conditions.
- the discharge section 1 has a width (hot water width) of 2 cm.
- the roll peripheral speed is 5 mZ seconds to 1 O mZ seconds, supply per unit contact width It was found that the speed is preferably about 0.5 kgZminZcm to 3.0 kgZminZcm.
- the quenching process can be performed at a supply rate of 5 kg min to 15 kg g min. You.
- the thickness and width of the strip-shaped quenched alloy obtained fall within appropriate ranges. It is also important to do so.
- the width of the ribbon-shaped quenched alloy is preferably in the range of 15 mm to 80 mm. Also, if the thickness of the ribbon-shaped alloy is too thin, the bulk density will be low, and it will be difficult to collect it. It is not preferable because sufficient speed cannot be obtained. For this reason, the thickness of the ribbon-shaped alloy is preferably set to be 70 m to 250 m, and more preferably set to be 100 m to 200 m.
- the inert gas atmosphere pressure during the production is too high, the inert gas around the roll may be entrained when the cooling roll is rotating at high speed. Occurs and a stable cooling state cannot be obtained.
- the atmospheric pressure is too low, the thin strip alloy separated from the roll is not rapidly cooled by the inert gas, so that crystallization proceeds and an alloy containing a large amount of amorphous material cannot be produced. In this case, the magnetic properties of the alloy obtained after the crystallization heat treatment are reduced.
- the inert gas pressure is preferably adjusted to 1 to 50 kPa.
- the originally crystalline portion will be coarsened during the heat treatment in the subsequent process, adversely affecting the magnetic properties Therefore, it is not preferable. Therefore, it is important to produce an alloy containing a large amount of amorphous material by the strip casting method. It is advantageous to be able to quantitatively measure the amorphous fraction of the rapidly solidified alloy produced.
- the inventor of the present invention has a simple and accurate method for quantitatively evaluating the amount of the amorphous phase by crushing the strip-shaped alloy after fabrication and determining the calorific value during crystallization by thermal analysis. And decided to use this method.
- the heat generation amount of the Fe 3 B phase which is the main phase
- the magnet powder that has been subjected to the subsequent crystallization heat treatment has good magnetic properties. It was found that it exhibited characteristics.
- the calorific value during main phase crystallization of an alloy considered to be 100% amorphous produced at an excessive cooling rate is measured to be about 45 JZ g
- the calorific value above 28 JZ g is This means that the metal structure has an amorphous structure of substantially 60% by volume or more.
- the present inventor has proposed a simple and accurate method for quantitatively evaluating the amount of an amorphous phase by breaking a forged strip-shaped alloy and measuring its intrinsic coercive force. And decided to use this method.
- the intrinsic coercive force H ( ⁇ More specifically, if the intrinsic coercive force H ⁇ ⁇ of the alloy before the crystallization heat treatment is 10 kA Zm or less, the magnet powder that has undergone the subsequent crystallization heat treatment will be produced. because it has good good magnetic properties, the intrinsic coercive force H c is determined that 1 0 k AZ m or less.
- Each raw material has the composition shown in No. l to No. 11 in Table 1 below.
- the obtained alloy was pulverized and sieved to 150 m or less to produce 20 g of a powder, thereby obtaining an alloy powder for evaluation (sample powder).
- Thermal analysis and magnetic property evaluation were performed using these alloy powders for evaluation.
- the thermal analysis (measurement of crystallization calorific value) was performed using DSC (differential scanning calorimeter), and the heating rate was set at a temperature of 550 ° C (: up to 650 ° C) for 4 mg of powder.
- the magnetic properties were evaluated using a VSM (vibrating sample magnetometer) with a maximum applied magnetic field of 5 mg of powder. 1. Measurements were made at 6 MAZm.
- FIG. 4 shows a thermal analysis curve obtained by thermal analysis of a sample having good magnetic properties after the heat treatment.
- the crystallization exotherm shown in Table 2 was calculated by calculating the area of the first peak.
- the main phase crystallization calorific value determined by thermal analysis exceeded 28 J It can be determined that 60% by volume or more of the sample is amorphous.
- Fig. 5 shows the magnetic hysteresis loop obtained when a sample having good magnetic properties after heat treatment was measured.
- FIG. 6 is an enlarged view of the vicinity of the origin in FIG. For the samples No.
- the coercive force obtained by the magnetic property evaluation is less than 10 kA Zm.
- these samples which are considered to be amorphous by 60% by volume or more after fabrication, show good values of the magnetic properties obtained after the heat treatment for crystallization.
- samples No. 9 to No. 11 shown as comparative examples the crystallization heating value of the main phase is small, and the value of the intrinsic coercive force is large. In the samples shown in these comparative examples, it is presumed that only 30 volume% or less of the amorphous phase is present after the production. For sample No.
- the present invention there is provided a method for producing a raw material alloy for a nanocomposite magnet using a strip casting method.
- a method for producing a raw material alloy for a nanocomposite magnet using a strip casting method By adopting this for industrial production, it becomes possible to produce a nanocomposite magnet raw material alloy at a lower cost than before. Since the present invention employs an inexpensive strip casting method with a low production cost, the present invention is suitable for mass production, and can provide inexpensively permanent magnet powder having excellent magnetic properties that cannot be achieved with a hard ferrite magnet.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Crystallography & Structural Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Power Engineering (AREA)
- Mechanical Engineering (AREA)
- Nanotechnology (AREA)
- Composite Materials (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Continuous Casting (AREA)
Description
Claims
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2002534022A JP4787459B2 (ja) | 2000-10-06 | 2001-09-25 | ストリップキャスト法を用いたナノコンポジット型永久磁石用原料合金の製造方法 |
US10/381,412 US7004228B2 (en) | 2000-10-06 | 2001-09-25 | Process for producing, through strip casting, raw alloy for nanocomposite type permanent magnet |
AU2001288123A AU2001288123A1 (en) | 2000-10-06 | 2001-09-25 | Process for producing, through strip casting, raw alloy for nanocomposite type permanent magnet |
EP01967835A EP1338359B1 (en) | 2000-10-06 | 2001-09-25 | Process for producing, through strip casting, raw alloy for nanocomposite type permanent magnet |
DE60131561T DE60131561T2 (de) | 2000-10-06 | 2001-09-25 | Verfahren zur herstellung einer rohlegierung durch bandgiessen für dauermagnete aus nanoverbundwerkstoff |
US11/288,710 US7547365B2 (en) | 2000-10-06 | 2005-11-28 | Process for producing, through strip casting, raw alloy for nanocomposite type permanent magnet |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2000307671 | 2000-10-06 | ||
JP2000-307671 | 2000-10-06 |
Related Child Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US10381412 A-371-Of-International | 2001-09-25 | ||
US11/288,710 Division US7547365B2 (en) | 2000-10-06 | 2005-11-28 | Process for producing, through strip casting, raw alloy for nanocomposite type permanent magnet |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2002030595A1 true WO2002030595A1 (fr) | 2002-04-18 |
Family
ID=18788141
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2001/008317 WO2002030595A1 (fr) | 2000-10-06 | 2001-09-25 | Procede de fabrication par coulee de bandes d'un alliage brut pour aimant permanent nanocomposite |
Country Status (7)
Country | Link |
---|---|
US (2) | US7004228B2 (ja) |
EP (2) | EP1880782B1 (ja) |
JP (1) | JP4787459B2 (ja) |
CN (2) | CN100478687C (ja) |
AU (1) | AU2001288123A1 (ja) |
DE (1) | DE60131561T2 (ja) |
WO (1) | WO2002030595A1 (ja) |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2004014582A1 (en) * | 2002-08-08 | 2004-02-19 | Sumitomo Special Metals Co., Ltd. | Method of making rapidly solidified alloy for magnet |
JP2004158842A (ja) * | 2002-10-17 | 2004-06-03 | Neomax Co Ltd | ナノコンポジット磁石およびその製造方法 |
JP2006341294A (ja) * | 2005-06-10 | 2006-12-21 | Ulvac Japan Ltd | 真空溶解鋳造装置の冷却促進機構 |
JP2008231535A (ja) * | 2007-03-22 | 2008-10-02 | Showa Denko Kk | R−t−b系合金及びr−t−b系合金の製造方法、r−t−b系希土類永久磁石用微粉、r−t−b系希土類永久磁石 |
WO2014188596A1 (ja) * | 2013-05-24 | 2014-11-27 | トヨタ自動車株式会社 | 永久磁石原料粉末の製造方法、永久磁石の製造方法および永久磁石素材粉末の検査方法 |
CN108907208A (zh) * | 2018-07-21 | 2018-11-30 | 芜湖君华材料有限公司 | 一种非晶合金磁性粉末生产系统 |
Families Citing this family (40)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2004036602A1 (en) * | 2002-10-17 | 2004-04-29 | Neomax Co., Ltd. | Nanocomposite magnet and method for producing the same |
CN1705761B (zh) * | 2002-10-25 | 2010-05-12 | 昭和电工株式会社 | 包含稀土元素的合金,其生产方法,磁致伸缩器件,以及磁性冷冻剂材料 |
US7371292B2 (en) * | 2002-11-12 | 2008-05-13 | Nissan Motor Co., Ltd. | Nd-Fe-B type anisotropic exchange spring magnet and method of producing the same |
JP4179973B2 (ja) * | 2003-11-18 | 2008-11-12 | Tdk株式会社 | 焼結磁石の製造方法 |
US9022906B1 (en) | 2011-12-22 | 2015-05-05 | Preston Nelson | Top-loading adjustable weight kettlebell system |
TWI268289B (en) * | 2004-05-28 | 2006-12-11 | Tsung-Shune Chin | Ternary and multi-nary iron-based bulk glassy alloys and nanocrystalline alloys |
CN1297994C (zh) * | 2004-11-26 | 2007-01-31 | 中国兵器工业第五二研究所 | 无须磁场处理获取特殊矩形比纳米晶软磁材料的方法 |
WO2006091875A2 (en) * | 2005-02-24 | 2006-08-31 | University Of Virginia Patent Foundation | Amorphous steel composites with enhanced strengths, elastic properties and ductilities |
RU2389097C1 (ru) * | 2007-02-05 | 2010-05-10 | Сова Денко К.К. | Сплав r-t-b-типа и способ его изготовления, тонкодисперсный порошок для редкоземельного постоянного магнита r-t-b-типа и редкоземельный постоянный магнит r-t-b-типа |
CN100432268C (zh) * | 2007-02-09 | 2008-11-12 | 上海大学 | 一种Fe基大块非晶合金及其制备方法 |
CN100432271C (zh) * | 2007-02-09 | 2008-11-12 | 上海大学 | 一种具有硬磁性的铁基大块非晶合金及其制备方法 |
CN100465323C (zh) * | 2007-07-13 | 2009-03-04 | 上海大学 | 一种纳米晶复合永磁合金及其制备方法 |
CN101888909A (zh) * | 2007-12-13 | 2010-11-17 | 昭和电工株式会社 | R-t-b系合金和r-t-b系合金的制造方法、r-t-b系稀土类永久磁铁用微粉、r-t-b系稀土类永久磁铁 |
CN101509106B (zh) * | 2008-02-20 | 2010-06-30 | 吴更生 | 一种铁基非晶态合金材料及其制备方法 |
KR101922188B1 (ko) * | 2011-08-03 | 2018-11-26 | 가부시키가이샤 산도쿠 | 희토류 소결 자석용 원료 합금 주편 및 그 제조 방법 |
WO2013073513A1 (ja) * | 2011-11-14 | 2013-05-23 | Jfeスチール株式会社 | 金属薄帯の製造方法および製造設備 |
DE112012005566T8 (de) * | 2012-01-04 | 2014-11-13 | National Institute For Materials Science | Seltenerdnanoverbundmagnet |
CN102909329B (zh) * | 2012-11-05 | 2014-05-14 | 江苏锦宏有色金属材料有限公司 | 多喷嘴用非晶合金带分带器 |
CN103805825B (zh) * | 2012-11-08 | 2016-04-06 | 沈阳中北真空科技有限公司 | 稀土永磁合金真空感应熔炼速凝设备 |
CN103077796B (zh) * | 2013-02-06 | 2015-06-17 | 江苏南方永磁科技有限公司 | 一种耐蚀钕铁硼永磁材料及其制备方法 |
BR112015031725A2 (pt) | 2013-06-17 | 2017-07-25 | Urban Mining Tech Company Llc | método para fabricação de um imã permanente de nd-fe-b reciclado |
CN103469118B (zh) * | 2013-07-20 | 2016-01-20 | 南通万宝实业有限公司 | 节能电机的非晶铁合金铁芯及其制备方法 |
US9336932B1 (en) | 2014-08-15 | 2016-05-10 | Urban Mining Company | Grain boundary engineering |
CN105543727B (zh) * | 2015-12-11 | 2017-11-21 | 江西大有科技有限公司 | 应用于防盗传感的非晶合金磁条及其制备方法 |
CN107262688B (zh) * | 2016-04-08 | 2019-04-02 | 沈阳中北真空技术有限公司 | 一种带二次冷却的真空熔炼速凝设备及速凝合金制造方法 |
CN106216698A (zh) * | 2016-09-29 | 2016-12-14 | 柳州增程材料科技有限公司 | 一种3d打印用合金粉末的制备工艺 |
CN106392087A (zh) * | 2016-09-29 | 2017-02-15 | 柳州增程材料科技有限公司 | 一种高强度3d打印金属材料的制备方法 |
CN106270541A (zh) * | 2016-09-29 | 2017-01-04 | 柳州增程材料科技有限公司 | 高强度增材制造材料的加工方法 |
CN106270520A (zh) * | 2016-09-29 | 2017-01-04 | 柳州增程材料科技有限公司 | 高强度高模量3d打印材料的制备方法 |
CN106166616A (zh) * | 2016-09-29 | 2016-11-30 | 柳州增程材料科技有限公司 | 一种3d打印用金属粉末的制备方法 |
CN106216700A (zh) * | 2016-09-30 | 2016-12-14 | 柳州增程材料科技有限公司 | 一种变速箱用铝镁合金粉末的制备工艺 |
CN106392086A (zh) * | 2016-09-30 | 2017-02-15 | 柳州增程材料科技有限公司 | 一种铝镁合金粉末的制备工艺 |
CN107045910B (zh) * | 2017-03-27 | 2019-02-19 | 河北工业大学 | 一种Nd-Fe-B薄带磁体及其制备方法 |
CN107377910B (zh) * | 2017-08-05 | 2019-05-28 | 江苏轩辕特种材料科技有限公司 | 一种铁硅硼合金带材防氧化单辊快淬工艺 |
CN109248994B (zh) * | 2017-08-19 | 2021-05-25 | 福建省长汀金龙稀土有限公司 | 一种薄带的铸造装置及薄带的铸造方法 |
CN108531834B (zh) * | 2018-04-17 | 2019-12-06 | 华中科技大学 | 一种耐磨耐蚀高铬铁基非晶合金及其制备方法 |
CN109014222A (zh) * | 2018-07-19 | 2018-12-18 | 芜湖君华材料有限公司 | 一种非金合金带材收集切碎设备 |
CN108788036A (zh) * | 2018-07-20 | 2018-11-13 | 芜湖君华材料有限公司 | 一种非晶合金材料快淬切碎系统 |
CN113035559B (zh) * | 2021-04-01 | 2022-07-08 | 包头市科锐微磁新材料有限责任公司 | 一种高性能钕铁硼各向同性磁粉的制备方法 |
CN113512685B (zh) * | 2021-04-22 | 2023-03-24 | 北京中磁新材科技有限公司 | Fe基磁性合金及其制备方法 |
Citations (17)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5594151A (en) * | 1979-01-12 | 1980-07-17 | Hitachi Ltd | Method of measuring amorphous state of amorphous ferromagnetic substance |
JPH02179803A (ja) * | 1988-12-28 | 1990-07-12 | Nippon Steel Corp | Nd系永久磁石用フレーク製造用注湯容器 |
JPH02247308A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | Nd合金フレーク製造用冷却ドラムの外周面調整方法及び装置 |
JPH02247310A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | 雰囲気型超急冷装置の防爆安全扉 |
JPH02247306A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | Nd合金注湯ノズルの地金除去装置 |
JPH02247307A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | Nd合金フレーク製造方法 |
JPH02247305A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | Nd合金フレーク製造時の雰囲気圧制御方法 |
JPH02247309A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | 超急冷フレーク用温度測定装置 |
JPH02298003A (ja) * | 1989-05-12 | 1990-12-10 | Fuji Elelctrochem Co Ltd | 希土類永久磁石の製造方法 |
JPH07166206A (ja) * | 1993-12-10 | 1995-06-27 | Sumitomo Special Metals Co Ltd | 永久磁石合金粉末とその製造方法 |
JPH08229641A (ja) * | 1995-02-23 | 1996-09-10 | Sumitomo Special Metals Co Ltd | R−Fe−B系永久磁石用鋳片の製造方法 |
JPH08335506A (ja) * | 1995-04-01 | 1996-12-17 | Sumitomo Special Metals Co Ltd | 高保磁力鉄基永久磁石及びボンド磁石 |
JPH10265915A (ja) * | 1997-03-27 | 1998-10-06 | Sumitomo Special Metals Co Ltd | 微細結晶永久磁石合金及び永久磁石粉末の製造方法 |
EP1104932A2 (en) * | 1999-08-11 | 2001-06-06 | Seiko Epson Corporation | Method of manufacturing magnet material, and bonded magnet |
JP2001226753A (ja) * | 2000-02-10 | 2001-08-21 | Sumitomo Special Metals Co Ltd | 鉄基合金軟磁性材料およびその製造方法 |
JP2001244107A (ja) * | 1999-12-21 | 2001-09-07 | Sumitomo Special Metals Co Ltd | 鉄基合金永久磁石粉末およびその製造方法 |
JP2001254159A (ja) * | 2000-03-10 | 2001-09-18 | Japan Science & Technology Corp | 高ガラス形成能を有する鉄基永久磁石合金 |
Family Cites Families (59)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5946008A (ja) | 1982-08-21 | 1984-03-15 | Sumitomo Special Metals Co Ltd | 永久磁石 |
CA1316375C (en) | 1982-08-21 | 1993-04-20 | Masato Sagawa | Magnetic materials and permanent magnets |
US5174362A (en) * | 1982-09-03 | 1992-12-29 | General Motors Corporation | High-energy product rare earth-iron magnet alloys |
US4851058A (en) | 1982-09-03 | 1989-07-25 | General Motors Corporation | High energy product rare earth-iron magnet alloys |
EP0108474B2 (en) | 1982-09-03 | 1995-06-21 | General Motors Corporation | RE-TM-B alloys, method for their production and permanent magnets containing such alloys |
JPS609852A (ja) | 1983-06-24 | 1985-01-18 | ゼネラル・モ−タ−ズ・コ−ポレ−シヨン | 高エネルギ−積の稀土類−鉄磁石合金 |
JPS61140350A (ja) | 1984-12-13 | 1986-06-27 | Toyota Central Res & Dev Lab Inc | 金属薄帯の製造装置 |
JP2727505B2 (ja) | 1986-04-15 | 1998-03-11 | ティーディーケイ株式会社 | 永久磁石およびその製造方法 |
DE3779481T2 (de) | 1986-04-15 | 1992-12-24 | Tdk Corp | Dauermagnet und verfahren zu seiner herstellung. |
JP2727506B2 (ja) | 1986-04-15 | 1998-03-11 | ティーディーケイ株式会社 | 永久磁石およびその製造方法 |
DE3777523D1 (de) | 1986-10-10 | 1992-04-23 | Philips Nv | Magnetisches material aus eisen, bor und seltenerdmetall. |
JPS647501U (ja) | 1987-07-03 | 1989-01-17 | ||
JPS647502U (ja) | 1987-07-03 | 1989-01-17 | ||
US5022939A (en) | 1987-07-30 | 1991-06-11 | Tdk Corporation | Permanent magnets |
JPH01103805A (ja) | 1987-07-30 | 1989-04-20 | Tdk Corp | 永久磁石 |
JPH01100242A (ja) | 1987-10-13 | 1989-04-18 | Tdk Corp | 永久磁石材料 |
JPH02247A (ja) | 1987-12-07 | 1990-01-05 | Heinz Bereuter | 少なくとも一部がパーフルオロアミノカルボン酸及び/又はパーフルオロアミドカルボン酸の新規塩類又はアミン類、及びその利用 |
US4919732A (en) * | 1988-07-25 | 1990-04-24 | Kubota Ltd. | Iron-neodymium-boron permanent magnet alloys which contain dispersed phases and have been prepared using a rapid solidification process |
EP0362812B1 (en) * | 1988-10-04 | 1996-01-24 | Hitachi Metals, Ltd. | Bonded isotropic R-Fe-B-magnet and method for making it |
JPH0831385B2 (ja) | 1990-03-09 | 1996-03-27 | 富士電気化学株式会社 | 異方性希土類永久磁石の製造方法 |
JPH0831386B2 (ja) | 1990-03-09 | 1996-03-27 | 富士電気化学株式会社 | 異方性希土類永久磁石の製造方法 |
JP3502107B2 (ja) | 1991-08-29 | 2004-03-02 | Tdk株式会社 | 永久磁石材料の製造方法 |
ATE158669T1 (de) | 1993-06-14 | 1997-10-15 | Santoku Metal Ind | Verfahren zur herstellung eines dauermagneten aus seltenerdmetall, bor und eisen |
JP3304175B2 (ja) | 1993-10-20 | 2002-07-22 | エフ・ディ−・ケイ株式会社 | 希土類急冷粉体の製造方法、希土類急冷粉体、ボンド磁石の製造方法、およびボンド磁石 |
JP3311907B2 (ja) | 1994-10-06 | 2002-08-05 | 増本 健 | 永久磁石材料、永久磁石及び永久磁石の製造方法 |
JP3777199B2 (ja) | 1994-12-09 | 2006-05-24 | 株式会社Neomax | 高性能R−Fe−B系永久磁石材料の製造方法 |
US5666635A (en) | 1994-10-07 | 1997-09-09 | Sumitomo Special Metals Co., Ltd. | Fabrication methods for R-Fe-B permanent magnets |
JP3845461B2 (ja) * | 1995-04-06 | 2006-11-15 | 株式会社Neomax | ボンド磁石用永久磁石合金粉末の製造方法及びその装置 |
US5800635A (en) * | 1995-06-15 | 1998-09-01 | Alliedsignal Inc. | Method of achieving a controlled step change in the magnetization loop of amorphous alloys |
JP3201944B2 (ja) | 1995-12-04 | 2001-08-27 | 株式会社三徳 | 希土類金属含有合金の製造システム |
JPH09155513A (ja) | 1995-12-04 | 1997-06-17 | Santoku Kinzoku Kogyo Kk | ストリップキャスト用タンディッシュ |
US6022424A (en) | 1996-04-09 | 2000-02-08 | Lockheed Martin Idaho Technologies Company | Atomization methods for forming magnet powders |
US5725792A (en) | 1996-04-10 | 1998-03-10 | Magnequench International, Inc. | Bonded magnet with low losses and easy saturation |
JPH1088294A (ja) | 1996-09-12 | 1998-04-07 | Alps Electric Co Ltd | 硬磁性材料 |
KR100340383B1 (ko) | 1997-02-14 | 2002-06-12 | 오카모토 유지 | 미세 결정 조직을 갖는 박판 자석 |
EP0867897B1 (en) * | 1997-03-25 | 2003-11-26 | Alps Electric Co., Ltd. | Fe based hard magnetic alloy having super-cooled liquid region |
JPH10317109A (ja) | 1997-05-22 | 1998-12-02 | Sumitomo Special Metals Co Ltd | 薄肉永久磁石の製造方法 |
US5905424A (en) | 1997-08-04 | 1999-05-18 | Magnequench International, Inc. | Bonded magnet made from gas atomized powders of rare earth alloy |
JPH1171646A (ja) * | 1997-08-29 | 1999-03-16 | Alps Electric Co Ltd | スピーカ |
EP0898287B1 (en) * | 1997-08-22 | 2003-05-21 | Alps Electric Co., Ltd. | Hard magnetic alloy having supercooled liquid region, sintered product thereof and applications |
US6332933B1 (en) | 1997-10-22 | 2001-12-25 | Santoku Corporation | Iron-rare earth-boron-refractory metal magnetic nanocomposites |
US6183572B1 (en) | 1997-12-30 | 2001-02-06 | Magnequench International, Inc. | Isotropic rare earth material of high intrinsic induction |
JPH11323509A (ja) | 1998-05-15 | 1999-11-26 | Alps Electric Co Ltd | 硬磁性合金圧密成形体およびその製造方法 |
JP3981788B2 (ja) | 1998-06-24 | 2007-09-26 | 株式会社アルバック | 希土類元素含有合金の鋳造装置および製造方法 |
JP3901875B2 (ja) | 1998-06-24 | 2007-04-04 | 株式会社アルバック | タンディッシュ、およびそのタンディッシュを用いた希土類元素含有合金の製造方法と、そのタンディッシュを備えた希土類元素含有合金の製造装置 |
CN1265401C (zh) | 1998-07-13 | 2006-07-19 | 株式会社三德 | 制造纳米复合磁性材料的方法以及制造粘结磁体的方法 |
CN1198292C (zh) * | 1998-10-30 | 2005-04-20 | 株式会社三德 | Sm(Co,Fe,Cu,Zr,C)组合物及其制造方法 |
US6302972B1 (en) | 1998-12-07 | 2001-10-16 | Sumitomo Special Metals Co., Ltd | Nanocomposite magnet material and method for producing nanocomposite magnet |
JP3604308B2 (ja) * | 1998-12-07 | 2004-12-22 | 株式会社Neomax | ナノコンポジット磁石用原料合金、その粉末および製造方法、ならびにナノコンポジット磁石粉末および磁石の製造方法 |
US6302939B1 (en) | 1999-02-01 | 2001-10-16 | Magnequench International, Inc. | Rare earth permanent magnet and method for making same |
US6524399B1 (en) | 1999-03-05 | 2003-02-25 | Pioneer Metals And Technology, Inc. | Magnetic material |
JP3712595B2 (ja) * | 1999-06-08 | 2005-11-02 | 信越化学工業株式会社 | 永久磁石用合金薄帯および焼結永久磁石 |
DE60031914T8 (de) | 1999-06-11 | 2007-10-31 | Seiko Epson Corp. | Magnetpulver und isotroper Verbundmagnet |
KR100562681B1 (ko) * | 2000-05-24 | 2006-03-23 | 가부시키가이샤 네오맥스 | 복수의 강자성상을 포함하는 영구자석 및 그 제조방법 |
JP2002080921A (ja) * | 2000-09-07 | 2002-03-22 | Sumitomo Special Metals Co Ltd | 鉄基希土類合金磁石用原料合金およびその製造方法 |
US6790296B2 (en) * | 2000-11-13 | 2004-09-14 | Neomax Co., Ltd. | Nanocomposite magnet and method for producing same |
CN1220989C (zh) * | 2001-02-07 | 2005-09-28 | 株式会社新王磁材 | 制造铁基稀土磁体用合金材料的方法 |
JP4023138B2 (ja) * | 2001-02-07 | 2007-12-19 | 日立金属株式会社 | 鉄基希土類合金粉末および鉄基希土類合金粉末を含むコンパウンドならびにそれを用いた永久磁石 |
WO2004036602A1 (en) * | 2002-10-17 | 2004-04-29 | Neomax Co., Ltd. | Nanocomposite magnet and method for producing the same |
-
2001
- 2001-09-25 DE DE60131561T patent/DE60131561T2/de not_active Expired - Lifetime
- 2001-09-25 EP EP07015643.5A patent/EP1880782B1/en not_active Expired - Lifetime
- 2001-09-25 US US10/381,412 patent/US7004228B2/en not_active Expired - Lifetime
- 2001-09-25 CN CNB2005100511775A patent/CN100478687C/zh not_active Expired - Fee Related
- 2001-09-25 EP EP01967835A patent/EP1338359B1/en not_active Expired - Lifetime
- 2001-09-25 JP JP2002534022A patent/JP4787459B2/ja not_active Expired - Fee Related
- 2001-09-25 AU AU2001288123A patent/AU2001288123A1/en not_active Abandoned
- 2001-09-25 CN CNB018121764A patent/CN1228158C/zh not_active Expired - Fee Related
- 2001-09-25 WO PCT/JP2001/008317 patent/WO2002030595A1/ja active IP Right Grant
-
2005
- 2005-11-28 US US11/288,710 patent/US7547365B2/en not_active Expired - Fee Related
Patent Citations (17)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5594151A (en) * | 1979-01-12 | 1980-07-17 | Hitachi Ltd | Method of measuring amorphous state of amorphous ferromagnetic substance |
JPH02179803A (ja) * | 1988-12-28 | 1990-07-12 | Nippon Steel Corp | Nd系永久磁石用フレーク製造用注湯容器 |
JPH02247308A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | Nd合金フレーク製造用冷却ドラムの外周面調整方法及び装置 |
JPH02247310A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | 雰囲気型超急冷装置の防爆安全扉 |
JPH02247306A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | Nd合金注湯ノズルの地金除去装置 |
JPH02247307A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | Nd合金フレーク製造方法 |
JPH02247305A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | Nd合金フレーク製造時の雰囲気圧制御方法 |
JPH02247309A (ja) * | 1989-03-17 | 1990-10-03 | Nippon Steel Corp | 超急冷フレーク用温度測定装置 |
JPH02298003A (ja) * | 1989-05-12 | 1990-12-10 | Fuji Elelctrochem Co Ltd | 希土類永久磁石の製造方法 |
JPH07166206A (ja) * | 1993-12-10 | 1995-06-27 | Sumitomo Special Metals Co Ltd | 永久磁石合金粉末とその製造方法 |
JPH08229641A (ja) * | 1995-02-23 | 1996-09-10 | Sumitomo Special Metals Co Ltd | R−Fe−B系永久磁石用鋳片の製造方法 |
JPH08335506A (ja) * | 1995-04-01 | 1996-12-17 | Sumitomo Special Metals Co Ltd | 高保磁力鉄基永久磁石及びボンド磁石 |
JPH10265915A (ja) * | 1997-03-27 | 1998-10-06 | Sumitomo Special Metals Co Ltd | 微細結晶永久磁石合金及び永久磁石粉末の製造方法 |
EP1104932A2 (en) * | 1999-08-11 | 2001-06-06 | Seiko Epson Corporation | Method of manufacturing magnet material, and bonded magnet |
JP2001244107A (ja) * | 1999-12-21 | 2001-09-07 | Sumitomo Special Metals Co Ltd | 鉄基合金永久磁石粉末およびその製造方法 |
JP2001226753A (ja) * | 2000-02-10 | 2001-08-21 | Sumitomo Special Metals Co Ltd | 鉄基合金軟磁性材料およびその製造方法 |
JP2001254159A (ja) * | 2000-03-10 | 2001-09-18 | Japan Science & Technology Corp | 高ガラス形成能を有する鉄基永久磁石合金 |
Non-Patent Citations (1)
Title |
---|
See also references of EP1338359A4 * |
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2004014582A1 (en) * | 2002-08-08 | 2004-02-19 | Sumitomo Special Metals Co., Ltd. | Method of making rapidly solidified alloy for magnet |
EP1647343A2 (en) * | 2002-08-08 | 2006-04-19 | Neomax Co., Ltd. | Method of making rapidly solidified alloy for magnet |
EP1647343A3 (en) * | 2002-08-08 | 2006-04-26 | Neomax Co., Ltd. | Method of making rapidly solidified alloy for magnet |
JP2004158842A (ja) * | 2002-10-17 | 2004-06-03 | Neomax Co Ltd | ナノコンポジット磁石およびその製造方法 |
JP2006341294A (ja) * | 2005-06-10 | 2006-12-21 | Ulvac Japan Ltd | 真空溶解鋳造装置の冷却促進機構 |
JP4603426B2 (ja) * | 2005-06-10 | 2010-12-22 | 株式会社アルバック | 真空溶解鋳造装置の冷却促進機構 |
JP2008231535A (ja) * | 2007-03-22 | 2008-10-02 | Showa Denko Kk | R−t−b系合金及びr−t−b系合金の製造方法、r−t−b系希土類永久磁石用微粉、r−t−b系希土類永久磁石 |
WO2014188596A1 (ja) * | 2013-05-24 | 2014-11-27 | トヨタ自動車株式会社 | 永久磁石原料粉末の製造方法、永久磁石の製造方法および永久磁石素材粉末の検査方法 |
JP5983872B2 (ja) * | 2013-05-24 | 2016-09-06 | トヨタ自動車株式会社 | 永久磁石原料粉末の製造方法、永久磁石の製造方法および永久磁石素材粉末の検査方法 |
US10464132B2 (en) | 2013-05-24 | 2019-11-05 | Toyota Jidosha Kabushiki Kaisha | Permanent magnet source powder fabrication method, permanent magnet fabrication method, and permanent magnet raw material powder inspection method |
CN108907208A (zh) * | 2018-07-21 | 2018-11-30 | 芜湖君华材料有限公司 | 一种非晶合金磁性粉末生产系统 |
Also Published As
Publication number | Publication date |
---|---|
EP1338359B1 (en) | 2007-11-21 |
US7004228B2 (en) | 2006-02-28 |
DE60131561T2 (de) | 2008-03-06 |
CN100478687C (zh) | 2009-04-15 |
CN1657936A (zh) | 2005-08-24 |
EP1338359A4 (en) | 2006-06-07 |
CN1440317A (zh) | 2003-09-03 |
EP1880782B1 (en) | 2015-01-07 |
EP1338359A1 (en) | 2003-08-27 |
JPWO2002030595A1 (ja) | 2004-02-19 |
EP1880782A3 (en) | 2013-04-17 |
US20060081308A1 (en) | 2006-04-20 |
EP1880782A2 (en) | 2008-01-23 |
US7547365B2 (en) | 2009-06-16 |
CN1228158C (zh) | 2005-11-23 |
DE60131561D1 (de) | 2008-01-03 |
US20030183305A1 (en) | 2003-10-02 |
AU2001288123A1 (en) | 2002-04-22 |
JP4787459B2 (ja) | 2011-10-05 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2002030595A1 (fr) | Procede de fabrication par coulee de bandes d'un alliage brut pour aimant permanent nanocomposite | |
US6695929B2 (en) | Method of making material alloy for iron-based rare earth magnet | |
JP3602120B2 (ja) | ナノコンポジット磁石用急冷合金の製造方法 | |
US7261781B2 (en) | Nanocomposite magnet | |
US7208097B2 (en) | Iron-based rare earth alloy nanocomposite magnet and method for producing the same | |
JP3365625B2 (ja) | ナノコンポジット磁石粉末および磁石の製造方法 | |
JP2001226753A (ja) | 鉄基合金軟磁性材料およびその製造方法 | |
US7958929B2 (en) | Apparatus for producing alloy and rare earth element alloy | |
JP3604308B2 (ja) | ナノコンポジット磁石用原料合金、その粉末および製造方法、ならびにナノコンポジット磁石粉末および磁石の製造方法 | |
JP4120253B2 (ja) | ナノコンポジット磁石用急冷合金およびその製造方法 | |
JP4332982B2 (ja) | 鉄基合金磁石の製造方法 | |
JP3583105B2 (ja) | 鉄基希土類磁石原料合金の製造方法 | |
JP2003158005A (ja) | ナノコンポジット磁石およびその製造方法 | |
JP2003286548A (ja) | ナノコンポジット磁石用急冷合金およびその製造方法 | |
JP4374633B2 (ja) | ナノコンポジット磁石用原料合金の製造方法、ならびにナノコンポジット磁石粉末および磁石の製造方法 | |
JP4168643B2 (ja) | ボンド磁石用コンパウンドおよびその製造方法 | |
JP2004339527A (ja) | 熱間成形型ナノコンポジット磁石の製造方法 | |
JP3810639B2 (ja) | 急冷合金の製造方法および希土類磁石の製造方法 | |
JP2002003979A (ja) | ナノコンポジット磁石用原料合金の製造方法、ならびにナノコンポジット磁石粉末および磁石の製造方法 | |
JP2004263232A5 (ja) | ||
JP3625821B6 (ja) | ナノコンポジット磁石およびその製造方法 | |
JP3625821B2 (ja) | ナノコンポジット磁石およびその製造方法 | |
JP2014087812A (ja) | 希土類磁石合金薄帯の製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AK | Designated states |
Kind code of ref document: A1 Designated state(s): AE AG AL AM AT AU AZ BA BB BG BR BY BZ CA CH CN CO CR CU CZ DE DK DM DZ EC EE ES FI GB GD GE GH GM HR HU ID IL IN IS JP KE KG KP KR KZ LC LK LR LS LT LU LV MA MD MG MK MN MW MX MZ NO NZ PH PL PT RO RU SD SE SG SI SK SL TJ TM TR TT TZ UA UG US UZ VN YU ZA ZW |
|
AL | Designated countries for regional patents |
Kind code of ref document: A1 Designated state(s): GH GM KE LS MW MZ SD SL SZ TZ UG ZW AM AZ BY KG KZ MD RU TJ TM AT BE CH CY DE DK ES FI FR GB GR IE IT LU MC NL PT SE TR BF BJ CF CG CI CM GA GN GQ GW ML MR NE SN TD TG |
|
DFPE | Request for preliminary examination filed prior to expiration of 19th month from priority date (pct application filed before 20040101) | ||
121 | Ep: the epo has been informed by wipo that ep was designated in this application | ||
WWE | Wipo information: entry into national phase |
Ref document number: 018121764 Country of ref document: CN |
|
WWE | Wipo information: entry into national phase |
Ref document number: 10381412 Country of ref document: US |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2001967835 Country of ref document: EP |
|
REG | Reference to national code |
Ref country code: DE Ref legal event code: 8642 |
|
WWP | Wipo information: published in national office |
Ref document number: 2001967835 Country of ref document: EP |
|
WWG | Wipo information: grant in national office |
Ref document number: 2001967835 Country of ref document: EP |