JP2019161946A - Rotor, rotating electric machine, and vehicle - Google Patents

Abstract

To provide a rotor, a rotating electric machine, and a vehicle, capable of improving torque performance.SOLUTION: A rotor of an embodiment includes a shaft, a housing hole, and a magnet composite. The shaft rotates around a rotation axis. A rotor core is fixed to the shaft. The housing hole is formed in the rotor core. The magnet composite is housed in the housing hole. The magnet composite includes a permanent magnet and a height raising body. The permanent magnet has a plate shape. The height raising body is attached on one surface of the permanent magnet in a direction orthogonal to a rotation axis direction and in a magnetization direction.SELECTED DRAWING: Figure 1

Description

  Embodiments described herein relate generally to a rotor, a rotating electrical machine, and a vehicle.

  For example, a vehicle driving motor mounted on a vehicle (for example, an automobile or a railway vehicle) as a rotating electrical machine can be used. As a vehicle driving motor, there is a permanent magnet synchronous motor (PMSM). The permanent magnet synchronous motor includes a stator around which an armature winding is wound, and a rotor that is rotatably provided to the stator and has a permanent magnet embedded in a rotor core. When a desired voltage is applied to the desired armature winding, a magnetic field is generated in the armature winding. The rotor is rotated by a magnetic attractive force or repulsive force generated between the magnetic field and the permanent magnet.

By the way, when embedding a permanent magnet in a rotor core, embedding a permanent magnet before magnetizing in the rotor core, and then magnetizing the permanent magnet, or embedding a permanent magnet previously magnetized in the rotor core Either of the methods can be adopted. In order to reduce the cost of the rotating electrical machine and ensure the mechanical strength of the rotor core, it is desirable to make the permanent magnet as thin as possible.
However, a permanent magnet generates a demagnetizing field due to the influence of shape permeance and demagnetizes itself. Since the magnitude of the demagnetizing field is proportional to the thickness of the permanent magnet, if the thickness of the permanent magnet is reduced, the permanent magnet is likely to be self-demagnetized. As a result, there is a possibility that the residual magnetic flux density of the magnet is reduced and the torque characteristics of the rotating electrical machine are deteriorated.

JP 2001-251796 A

  The problem to be solved by the present invention is to provide a rotor, a rotating electrical machine, and a vehicle that can improve torque performance.

  The rotor of the embodiment has a shaft, a storage hole, and a magnet complex. The shaft rotates around the rotation axis. The rotor core is fixed to the shaft. The storage hole is formed in the rotor core. The magnet composite is stored in the storage hole. The magnet composite has a permanent magnet and a bulky body. The permanent magnet is plate-shaped. The bulky body is attached to one surface of the magnetization direction in a direction orthogonal to the rotation axis direction of the permanent magnet.

Sectional drawing orthogonal to the rotation axis which shows the rotary electric machine of embodiment. The graph which shows the change of the magnetic flux density of the permanent magnet with the high recoil permeability of embodiment, and a normal Nd magnet. The graph which shows the change of the demagnetization factor with respect to the permeance coefficient of the permanent magnet with high recoil permeability of embodiment, and Nd magnet. It is explanatory drawing which shows the difference of the effect of the composite_body | complex of embodiment and a comparative example, (a) shows a 1st Example, (b) shows a 2nd Example, (c) 1 shows a comparative example, and (d) shows a second comparative example. The table | surface which shows the measurement result of each Example of FIG. 4, and each comparative example. The graph which shows the change of the rotational torque of the rotor of embodiment. The schematic block diagram of the generator in which the rotary electric machine of embodiment was mounted. The schematic block diagram of the railway vehicle carrying the rotary electric machine of embodiment. The schematic block diagram of the motor vehicle carrying the rotary electric machine of embodiment.

  Hereinafter, a rotor, a rotating electrical machine, and a vehicle according to embodiments will be described with reference to the drawings.

FIG. 1 shows the rotating electrical machine 1 and is a cross-sectional view orthogonal to the rotation axis P. Note that the rotor 2 of the rotating electrical machine 1 has eight poles, and FIG. 1 shows only one pole, that is, only a peripheral angle region of 1/8 round.
The rotating electrical machine 1 includes a substantially cylindrical stator 20 and a rotor 2 that is provided on the radially inner side of the stator 20 and is rotatable with respect to the stator 20. In addition, the stator 20 and the rotor 2 are arrange | positioned in the state in which each center axis line was located on the common axis. Hereinafter, the common axis is referred to as the rotation axis P, the direction around the rotation axis P is referred to as the circumferential direction, and the direction orthogonal to the rotation axis P direction and the circumferential direction is referred to as the radial direction.

  The stator 20 has a substantially cylindrical stator core 21. The stator iron core 21 can be formed by laminating a plurality of electromagnetic steel plates or press-molding soft magnetic powder. A plurality (for example, 48 in this embodiment) of teeth 22 projecting toward the rotation axis P and arranged at equal intervals in the circumferential direction are integrally formed on the inner peripheral surface of the stator core 21. The teeth 22 have a substantially rectangular cross section. A slot 23 is formed between adjacent teeth 22. An armature winding 24 is wound around each tooth 22 via these slots 23. By supplying current to the armature winding 24, a predetermined flux linkage is formed in the stator 20 (tooth 22).

  The rotor 2 includes a shaft 3 that extends along the rotation axis P and rotates around the rotation axis P, and a substantially cylindrical rotor core 4 that is externally fixed to the shaft 3. A through hole 5 into which the shaft 3 can be inserted or press-fitted is formed at the radial center of the rotor core 4.

  Here, in the rotor core 4 of the present embodiment, the direction in which the linkage flux formed by the stator 20 easily flows is referred to as the q axis. A direction along a radial direction that is electrically and magnetically orthogonal to the q axis is referred to as a d axis. That is, a positive magnetic position (for example, the N pole of the magnet is brought closer) to an arbitrary circumferential angle position on the outer peripheral surface 4a of the rotor core 4, and one pole (for this embodiment, 45 degrees in mechanical angle) ) Rotation axis when the largest amount of magnetic flux flows when a negative magnetic position (for example, the S pole of the magnet is moved closer) is given to any other angular position that has shifted and the arbitrary position is shifted in the circumferential direction. A direction from P to an arbitrary position is defined as q-axis. A direction along a radial direction that is electrically and magnetically orthogonal to the q axis is defined as a d axis.

That is, one pole portion of the rotor core 4 refers to a region between q axes (a circumferential angle region of 1/8 round). For this reason, the rotor core 4 is comprised by 8 poles. In the rotor core 4 of the present embodiment, the center in the circumferential direction of one pole is the d axis.
In the following description, the d axis is referred to as the pole center E1, and the q axis (both ends in the circumferential direction of the circumferential angle region of 1/8 round) is referred to as the extreme E2.

The rotor iron core 4 can be formed by laminating a plurality of electromagnetic steel plates or press-molding soft magnetic powder. The rotor core 4 desirably has a magnetic permeability of 10 or more.
The rotor core 4 is provided with two magnet composites 30 for each pole. That is, the two magnet composites 30 are arranged so as to fill the two storage holes 6 formed in the rotor core 4 so as to correspond to the shape of the magnet composite 30. And the magnet composite 30 is being fixed to the accommodation hole 6 with the adhesive agent etc., for example.

The magnet complex 30 includes a plate-like permanent magnet 7 that is rectangular when viewed from the rotation axis P direction, and a bulky body 8 that is attached to one surface 7a in the thickness direction perpendicular to the rotation axis P direction of the permanent magnet 7. .
In the following description, the longitudinal direction of the permanent magnet 7 viewed from the direction of the rotation axis P is simply referred to as the longitudinal direction. The thickness direction of the permanent magnet 7 refers to the short direction of the permanent magnet 7 when viewed from the direction of the rotation axis P.

  The two magnet composites 30 are arranged symmetrically about the pole center E1. In addition, each permanent magnet 7 of each magnet complex 30 has a second end 7c opposite to the first end 7b in the radial direction outside the first end 7b on the pole center E1 side in the longitudinal direction. It is arranged to be located in. Further, the two permanent magnets 7 are arranged so as to be gradually separated from the pole center E1 as going from the first end 7b to the second end 7c. Further, the two permanent magnets 7 are arranged so that the opposite side of the outer peripheral surface 4 a of the rotor core 4 becomes a surface 7 a to which the bulky body 8 is attached.

  In the permanent magnets 7 arranged in this way, the magnetic flux density on the outer peripheral surface 4a side of the rotor core 4 in each permanent magnet 7 is increased, and harmonics of the surface magnetic flux density of the rotor core 4 can be reduced. Further, the magnetic flux of the permanent magnet 7 is easily concentrated on the pole center E1. That is, the magnetization directions of the two permanent magnets 7 arranged in each of the circumferential angle regions of 1/8 turn are the same. That is, for example, it is assumed that the two permanent magnets 7 arranged in each of the circumferential angle regions of 1/8 round are magnetized with N poles on the radially outer surfaces. In this case, the two permanent magnets 7 arranged in the circumferential angle region of another 1/8 round adjacent in the circumferential direction have their radially outer surfaces magnetized to the S pole.

  The bulky body 8 attached to the one surface 7 a of the permanent magnet 7 is made of the same material as the rotor core 4. For example, when the rotor core 4 is formed by laminating electromagnetic steel plates, the bulky body 8 is also formed by laminating electromagnetic steel plates. In this case, the lamination direction of the electromagnetic steel plates in the bulky body 8 may be the rotation axis P direction or the thickness direction of the permanent magnet 7. Further, when the rotor core 4 is formed by pressurizing soft magnetic powder, the bulky body 8 is also formed by pressurizing soft magnetic powder. However, the present invention is not limited to this, and the rotor core 4 may be laminated with electromagnetic steel plates, and the bulky body 8 may be molded by pressurizing soft magnetic powder. The reverse is also possible.

  The rotor core 4 has flux barriers 9 and 10 (first flux barrier 9, so as to be in contact with both longitudinal ends 7 b and 7 c (first end 7 b and second end 7 c) of the permanent magnet 7. A second flux barrier 10) is formed. Each flux barrier 9, 10 is a cavity that penetrates the rotor core 4 in the axial direction. Each flux barrier 9, 10 suppresses leakage of magnetic flux from the longitudinal end portions 7 b, 7 c of the permanent magnet 7 to the rotor core 4.

  The first flux barrier 9 is formed to extend from the first end 7 b of the permanent magnet 7 toward the pole center E <b> 1 and then bend and extend toward the shaft 3. Between the two 1st flux barriers 9, the 1st bridge part 40 located on the pole center E1 is formed. The first bridge portion 40 constitutes the rotor core 4.

  On the other hand, the second flux barrier 10 is formed so as to extend from the second end 7 c of the permanent magnet 7 toward the outer peripheral surface 4 a of the rotor core 4. A second bridge portion 41 constituting a part of the outer peripheral surface 4 a of the rotor core 4 is formed on the radially outer side of the second flux barrier 10.

  In addition, a third flux barrier 11 is formed on the rotor core 4 near the outer peripheral surface 4a on the pole center E1. Further, a fourth flux barrier 12 is formed on the rotor core 4 near the shaft 3 on the extreme E2. These flux barriers 11 and 12 regulate the flow of flux linkage of the stator 20 and the flow of magnetic flux of the permanent magnet 7. Further, by forming the third flux barrier 11 and the fourth flux barrier 12, the rotor core 4 can be reduced in weight.

Next, the magnet complex 30 will be described in more detail with reference to FIGS.
First, the permanent magnet 7 will be described in detail.
The permanent magnet 7 is a permanent magnet having a so-called high recoil permeability.

  Here, an induced voltage (back electromotive voltage) is generated in the armature winding 24 due to a magnetic change caused by the rotation of the rotor 2. In particular, when the rotor 2 rotates at a high speed, a large induced voltage is generated in the armature winding 24, causing an event that the current cannot be supplied to the armature winding 24 and the rotor cannot be rotated at a higher speed. There was a case. Moreover, in order to rotate a permanent magnet synchronous motor, auxiliary machines, such as an inverter, are provided. When an induced voltage exceeding the voltage (control voltage) that can be controlled by an auxiliary machine such as an inverter occurs, there is a possibility that the rotational torque is suddenly reduced or the auxiliary machine is damaged.

For this reason, a technique for reducing the induced voltage at the time of high-speed rotation of the rotor by a control current (field weakening current) has been proposed. However, since the control current does not directly contribute to the output of the permanent magnet synchronous motor, the motor efficiency in the high speed region of the permanent magnet synchronous motor may be reduced.
Therefore, it is conceivable to use a permanent magnet 7 having a high recoil permeability whose magnetization easily changes in response to an external magnetic field (hereinafter referred to as an external magnetic field). By using such a permanent magnet 7, it becomes possible to improve the motor efficiency at the time of high speed rotation, maintaining the motor efficiency at the time of the low speed rotation of the rotary electric machine 1. FIG.

As the permanent magnet 7, for example, an Sm-Co permanent magnet is used. The sm-Co based permanent magnet, for example, the composition _{formula: R p Fe q M r Cu} t Co 100 - p - q - r - s - t ( in the formula, at least one element R selected from rare earth elements , M is at least one element selected from Ti (titanium), Zr (zirconium), and Hf (hafnium), and _p , _q , _r , _s, and _t are each in atomic percent, and 10.8 ≦ p ≦ 11 .6, 25 ≦ q ≦ 40, 0.88 ≦ r ≦ 4.5, 0.88 ≦ t ≦ 13.5). The atomic ratio of the composition formula is an atomic ratio when the total of R, Fe, M, Cu, and Co is 100 atomic%, and the sintered body contains a trace amount of oxygen and carbon.

R in the composition formula is an element that increases the magnetic anisotropy of the magnet material. As an example of the element R, one or a plurality of elements selected from rare earths including Y (yttrium) can be used. For example, Sm, Ce (cerium), Nd (neodymium), Pr (praseodymium) or the like can be used, and it is particularly preferable to use Sm.
Further, for example, when a plurality of elements including Sm are used as the element R, the performance of the magnet material can be improved by setting the Sm concentration to 50 atomic% or more of the total elements applicable as the element R. In addition, it is more preferable that 70 atomic% or more, further 90 atomic% or more of the element applicable as the element R is Sm.

  By setting the concentration of an element applicable as the element R to, for example, 10.8 atomic% or more and 12.5 atomic% or less, the coercive force can be increased. When the element concentration applicable as the element R is less than 10.8 atomic%, a large amount of α-Fe is precipitated, so that a sufficient coercive force cannot be obtained. There is a decline. The concentration of the element applicable as the element R is more preferably 11.0 atomic% or more and 11.2 atomic% or less.

  M in the above compositional formula is an element necessary for developing a large coercive force in the composition when the Fe concentration is high. As the element M, for example, one or more elements selected from the group consisting of Ti, Zr, and Hf are used. When the content of the element M is greater than 4.5 atomic%, a heterogeneous phase containing an excessive amount of the element M is likely to be generated, causing a decrease in magnetic properties. Further, when the content of the element M is less than 0.88 atomic%, it is difficult to obtain the effect of increasing the Fe concentration and improving the magnetization. Therefore, the content r of the element M is preferably 1.15 atomic% or more and 3.57 atomic% or less. More preferably, it is greater than 1.49 atom% and not more than 2.24 atom%, and most preferably not less than 1.55 atom% and not more than 2.23 atom%.

The element M preferably contains at least Zr. In particular, the coercive force of the permanent magnet can be increased by using 50 atomic% or more of the element M as Zr. On the other hand, since Hf is expensive in the element M, the amount of Hf used is preferably as small as possible. For example, the content of Hf is preferably less than 20 atomic% of the element M.
Cu (copper) is an element indispensable for the mechanism of high coercive force in a magnet material. The Cu content is preferably, for example, 3.5 atomic% or more and 13.5 atomic% or less. If the content is larger than this, the magnetization is remarkably lowered. On the other hand, if the amount is smaller than this, it is difficult to obtain good magnetic properties. The Cu content t is more preferably 3.9 atomic% or more and 9.0 atomic% or less, and further preferably 4.4 atomic% or more and 5.7 atomic% or less.

  Fe is an element mainly responsible for magnetization. By adding a large amount of Fe, the saturation magnetization of the magnet material can be increased. However, if it is added excessively, it becomes difficult to obtain a desired crystal phase due to precipitation of α-Fe and phase separation, thereby reducing the coercive force. There is also a risk. The Fe content q is preferably 25 atom% or more and 40 atom% or less. The Fe content q is more preferably 28 atom% or more and 36 atom% or less, and most preferably 30 atom% or more and 33 atom% or less.

  Co is an element that plays a role in magnetization and develops a high coercive force. Further, by adding a large amount of Co, a high Curie temperature can be obtained and the heat resistance can be improved. If the amount of Co is small, the above-described effect is lowered. However, if it is added excessively, the proportion of Fe is relatively decreased, and there is a possibility that the magnetization is lowered. Further, 20 atomic% or less of Co is contained in Ni (nickel), V (vanadium), Cr (chromium), Mn (manganese), Al (aluminum), Si (silicon), Ga (gallium), Nb (niobium), Substitution with one or more elements selected from the group consisting of Ta (tantalum) and W (tungsten) makes it possible to increase the coercive force, which is a magnet characteristic.

  Further, the permanent magnet 7 has a two-dimensional metal structure composed of a main phase having a hexagonal Th2Zn17 type crystal phase (2-17 type crystal phase) and a grain boundary phase serving as a boundary between the main phase and the main phase. Further, the main phase is composed of a cell phase having a 2-17 type crystal phase and a Cu rich phase having a hexagonal CaCu5 type crystal phase (1-5 type crystal phase). The Cu-rich phase preferably takes a form that includes one cell phase. The above structure is also called a cell structure. The Cu rich phase also includes a cell wall phase that divides the cell phase.

  Cu-rich phase refers to a phase having a higher Cu concentration than the surroundings. For example, the Cu concentration of the Cu-rich phase is preferably 1.2 times or more the Cu concentration of the Th2Zn17 type crystal phase. The Cu-rich phase exists, for example, in the form of a line or a plate in the cross section including the c-axis in the Th 2 Zn 17 type crystal phase. Although the structure definition of the Cu-rich phase is not particularly defined, a hexagonal CaCu5 type crystal phase (1-5 type crystal phase) and the like can be mentioned as an example. Moreover, the permanent magnet may have a plurality of Cu-rich phases having different phases.

  The domain wall energy of the Cu-rich phase is higher than the domain wall energy of the Th2Zn17 type crystal phase, and this domain wall energy difference becomes a barrier for domain wall movement. Therefore, the Cu-rich phase functions as a pinning site, thereby suppressing domain wall movement between a plurality of cell phases. This is also called a pinning effect. Accordingly, it is more preferable that the Cu rich phase is formed so as to surround the cell phase.

In the Sm—Co magnet containing 25 atomic% or more of Fe, the Cu concentration of the Cu rich phase is preferably 10 atomic% or more and 60 atomic% or less. By increasing the Cu concentration in the Cu-rich phase, better magnetic properties can be obtained. In the composition region where the Fe concentration is high, the Cu concentration in the Cu-rich phase varies. For this reason, it becomes difficult to obtain the pinning effect, and the magnetic characteristics cannot be kept good.
As the domain wall moves out of the pinning site, magnetization reversal occurs and the magnetization decreases. When an external magnetic field is applied, if domain wall movement occurs in a magnetic field lower than the coercive force of the magnet, magnetization is reduced and magnet characteristics are degraded. Therefore, increasing the cell structure region promotes the suppression of the decrease in magnetization.

For observation of the cell structure consisting of Th2Zn17 type crystal phase and Cu rich phase and cell composition analysis, STEM (Scanning Transmission Electron Microscope), STEM-EDX (Scanning Transmission Electron Microscope-Energy Dispersion X) Observation by line spectroscopy: STEM-Energy Dispersive X-ray Spectroscopy).
As pretreatment of the STEM observation sample, first, processing is performed using a focused ion beam (FIB) so that the grain boundary phase enters the field of view. The sample is preferably unmagnetized. As a pretreatment of the sample for measuring the element concentration with STEM-EDX, the inside of the sample is cut out by 1 mm or more to obtain a measurement sample. Further, observation is performed at a magnification of 100,000 with respect to a plane parallel to the easy magnetization axis (c-axis). A mapping image of Cu and element M is taken in the same field of view.

When the Cu mapping image and the element M mapping image are overlapped, a region having a high Cu concentration corresponds to the Cu rich phase. A region where both the Cu concentration and the element M concentration are high is called a Cu-rich heterogeneous phase.
The cell structure is a main factor that determines the magnitude of the coercive force, and is also one of the factors that determines the recoil permeability. The recoil permeability is an average slope of a demagnetization curve and is defined by the following equation.
Recoil permeability μ = residual magnetic flux density Br / coercive force HcB (1)

  Here, the high recoil permeability means that the magnetization easily changes in response to an applied external magnetic field. The condition that the magnetization reversibly responds to the external magnetic field is that the operating point does not exceed the inflection point (knick) of the demagnetization curve. The operating point is expressed as a function of the magnetic flux density B and the magnetic field H, and indicates a magnetic characteristic when the magnetic material responds to a certain external magnetic field. When the operating point exceeds the nick due to an external magnetic field, the magnetization becomes irreversible. In other words, it will demagnetize and have a different demagnetization curve, and the operating point will move on it. Therefore, the permanent magnet having high recoil permeability is specifically as follows.

FIG. 2 is a graph showing changes in the magnetic flux density when the vertical axis represents the magnetic flux density [T] and the horizontal axis represents the magnetic field [kA / m], and is a permanent Nd magnet and a permanent having a high recoil permeability. Comparison with magnet (high μ magnet).
As shown in FIG. 2, a magnet having a high recoil permeability is preferably a magnet having a high coercive force such that the nick does not appear in the second quadrant and having excellent magnetization response to an external magnetic field. That is, the residual magnetization Br is 1.16 T or more, the coercive force Hcj is 1500 kA / m or more, and the recoil permeability is 1.2 or more. Further, the residual magnetization Br is 1.16 T or more, the coercive force Hcj is 1500 kA / m or more, the coercive force HcB is 700 kA / m or more, and the recoil permeability exceeds 1.1 and is 1.8 or less. Although details of the reason for the set value of the recoil permeability will be described later, the upper limit value of the recoil permeability of the permanent magnet 7 is 1.8 or less due to the upper limit in manufacturing the permanent magnet. However, it is big. Therefore, the recoil permeability of the permanent magnet 7 may not be 1.8 or less.

  Thus, a magnetic material having a responsiveness to magnetization while maintaining the coercive force is required. For the generation of coercive force, the existence of a cell structure is inevitable, but if the square shape remains good, the responsiveness of magnetization to an external magnetic field is impaired. Therefore, the presence of an intragranular heterogeneous phase is important in order to obtain a square shape. The heterogeneous phase consists of the elements M and Cu, and the Cu concentration of the Cu-rich phase, which has been distributed at the grain boundary so far, is distributed within the concentration within the grain boundary. The mold can be held down, that is, the responsiveness of magnetization can be increased.

  Examples of the intragranular heterophase include a Cu-rich phase, a phase composed of Cu and the element M. The intragranular heterogeneous phase here refers to a heterogeneous phase that does not overlap with the grain boundary phase or does not contact the end of the grain boundary phase. The presence / absence of the intragranular heterogeneous phase and the concentration and distribution state were determined by observing the sintered body with SEM (Scanning Electron Microscope), SEM-EDX (Scanning Electron Microscope-Energy Dispersive X-ray Spectroscopy: SEM- It is examined by measurement with an Energy Dispersive X-ray Spectroscope.

  When the presence of an intragranular heterogeneous phase can be confirmed by SEM, the concentration is quantified by the area ratio. For example, it is represented by the occupation ratio of the different phase area with respect to the entire SEM image in one field of view. For example, in an SEM image with a magnification of 3000 times, in a sintered body with a magnetization of 1.20 T, a coercive force of 1800 kA / m, and a recoil permeability of 1.08, the area occupancy of the different phase is 0.1%, In the sintered body having a magnetization of 1.18 T, a coercive force of 1700 kA / m, and a recoil permeability of 1.28, the area occupancy of the different phase was 0.8%. Further, as a result of applying different heat treatment conditions, the area occupancy ratio of the heterogeneous phase of the sintered body having a coercive force of 100 kA / m or less is as large as 3.0%. Thus, there is a correlation between the magnetic characteristics and the heterogeneous concentration, and it can be said that the presence of intragranular heterogeneity is important in order to add high recoil permeability as an essential characteristic while maintaining coercive force and magnetization.

Next, a method for manufacturing the permanent magnet 7 will be described.
The permanent magnet 7 is formed of a sintered body formed by pressure-molding the alloy powder having the above magnetic characteristics.
The alloy powder can be adjusted by, for example, casting a molten metal by an arc melting method or a high frequency melting method, and pulverizing the solid mother alloy. The alloy powder may be adjusted by mixing a plurality of powders having different compositions. Further, the alloy powder may be adjusted using a mechanical alloying method, a mechanical grinding method, a gas atomizing method, a substitution diffusion method, or the like. In the production of an alloy ribbon using the strip cast method, an alloy powder is prepared by producing a flake-like alloy ribbon and then crushing the alloy ribbon.

  For example, a thin ribbon having a thickness of 1 mm or less can be produced by pouring the molten alloy onto a copper cooling roll rotating at a peripheral speed of 0.1 m / second or more and 20 m / second or less and peeling it from the roll surface. When the peripheral speed is less than 0.1 m / sec, the variation in composition increases in the ribbon. On the other hand, when the peripheral speed exceeds 20 m / sec, the crystal grains may be excessively refined and the magnetic characteristics may be deteriorated. For this reason, the peripheral speed of a cooling roll is 0.3 m / sec or more and 15 m / sec or less, More preferably, it is 0.5 m / sec or more and 12 m / sec or less. The average particle diameter of the alloy powder is preferably 2 μm or more and 5 μm or less, and particles having a particle diameter of 2 μm or more and 10 μm or less are preferably 80% or more by volume.

  If necessary, such an alloy powder or an alloy before pulverization may be subjected to a heat treatment for homogenization. The pulverization is carried out using a jet mill or a ball mill. In order to prevent oxidation of the alloy, the pulverization is preferably performed in an inert gas atmosphere in a dry process and in an organic solvent in a wet process.

Next, the pulverized powder is filled with an alloy powder in a mold placed in an electromagnet, and pressure-molded in a magnetic field. By applying a magnetic field, a green compact with the crystal axis oriented is manufactured. A sintered compact is formed by sintering the produced green compact.
Sintering is performed in an inert gas atmosphere such as Ar gas or under vacuum. When sintering is performed in an inert gas atmosphere, it is possible to promote evaporation suppression of an element R such as Sm having a high vapor pressure. This has the effect of making it difficult for compositional deviations to occur. However, in the inert gas atmosphere, there is a possibility that the inert gas remains in the voids existing in the heterogeneous phase or in the green compact, and the density cannot be increased without firing. On the other hand, when sintered under vacuum, although it is possible to suppress the formation of different phases and increase the density of the sintered body, the amount of transpiration of the element R having a high vapor pressure increases, resulting in a composition shift and an alloy suitable as a permanent magnet. It becomes difficult to control the composition.

  Moreover, it decomposes | disassembles in heat processing with the moisture content in a sintering furnace, and the water | moisture content adhering to and mixed with a green compact or alloy powder, and an oxygen molecule and a hydrogen molecule are produced. Oxygen molecules combine with the element R, and an oxide of the element R is generated. The oxide of the element R becomes a factor that deteriorates the overall magnet characteristics. On the other hand, hydrogen molecules combine with a small amount of carbon to generate hydrocarbons. This hydrocarbon reacts with the element M, and a carbide of the element M is generated. Therefore, it is important to control the moisture content in the furnace and the moisture adhering to or contained in the alloy powder or the green compact as much as possible.

For the above points, it is effective to perform the sintering process (main sintering process) in an inert gas atmosphere such as Ar gas after performing the pretreatment process (preliminary sintering process) under vacuum. By teaching the sintering process having such a pretreatment process under vacuum and a main sintering process in an inert gas atmosphere, the moisture adhering to or contained in the green compact is reduced, Reduce the formation of oxides and carbides. Further, evaporation of an element R such as Sm having a high vapor pressure can be suppressed. In addition, a sintered body having a high density that is baked by reducing pores existing in the pressed powder is obtained.
In the case of sintering magnetic powder (alloy powder) having an Fe concentration of 25 atomic% or more, it is preferably maintained under vacuum until reaching the main sintering process temperature. By switching to the inert gas atmosphere at the same time as the main sintering temperature is reached, it is possible to suppress transpiration of the element R such as Sm during sintering as much as possible.

Further, the temperature of switching from a vacuum to an inert gas to a temperature T _V-G, when the holding temperature of the sintering process was set to a temperature T _S, it is preferable to satisfy the _{T V-G> T S -61} ℃. When T _{S is} −61 ° C. or lower, the heterogeneous phase remains in the sintered body, causing a decrease in magnet characteristics. Further, it cannot be sufficiently baked, and it becomes difficult to increase the density. Further, it is preferable that T _V−G > T _S −50 ° C., T _V−G ≧ T _S −40 ° C., and T _V−G ≧ T _S −30 ° C. are satisfied.
The degree of vacuum at the time of sintering under vacuum (preliminary sintering step) is preferably 9 × 10 ⁻² Pa or less. When it exceeds 9 × 10 ⁻² Pa, an oxide of element R is excessively formed, which causes deterioration of magnetic characteristics. In addition, the carbide phase of the element M is easily generated excessively. The degree of vacuum in the preliminary sintering step is more preferably 5 × 10 ⁻² Pa or less, and more preferably 1 × 10 ⁻² Pa or less.

  The holding temperature in the main sintering step is preferably 1230 ° C. or lower. This is because when the Fe concentration is high, a melting point drop occurs, so that the evaporation of the element R during sintering is minimized. More preferably, it is 1215 ° C. or lower, further 1205 ° C. or lower, and further preferably 1195 ° C. or lower. By setting the holding time in the main sintering step to 30 minutes or more and 15 hours or less, a high-density sintered body can be obtained. When holding time is less than 30 minutes, it does not burn enough and the density of a sintered compact becomes insufficient. In addition, when the holding time is 15 hours or more, Sm is remarkably evaporated, and it is difficult to obtain good magnetic properties. The holding time is 1 hour or more and 10 hours or less, and more preferably 1 hour or more and 4 hours or less.

  Next, a solution treatment is performed. The solution treatment is a heat treatment for forming a TbCu7 type crystal phase (1-7 type crystal phase) that becomes a precursor of a phase separated structure. The solution treatment requires a holding time of 30 minutes to 24 hours at a temperature of 1100 ° C. to 1190 ° C. During the solution treatment, if the holding temperature is less than 1100 ° C. or more than 1190 ° C., the ratio of the TbCu7-type crystal phase of the sintered body after the solution treatment is small, and there is a high possibility that the magnetic properties will deteriorate. . The holding temperature is preferably 1120 ° C. or higher and 1180 ° C. or lower, and more preferably 1120 ° C. or higher and 1170 ° C. or lower.

  Moreover, when the retention time of the solution treatment is less than 30 minutes, the constituent phases become non-uniform, and the coercive force decreases. Moreover, when the retention time of the solution treatment exceeds 24 hours, the amount of evaporation of the element R in the sintered body increases, and it becomes difficult to obtain good magnetic properties. For this reason, the retention time of the solution treatment is preferably 12 hours or less after 1 hour, and more preferably 1 hour or more and 8 hours or less. Note that the solution treatment in a vacuum or in an inert gas atmosphere such as Ar gas also promotes the suppression of oxidation of the element R in the powder.

  You may perform the heat processing hold | maintained for a fixed time at the intermediate temperature of the holding temperature of both heat processing between the sintering process mentioned above and solution treatment. This process is called high-quality treatment or intermediate heat treatment. The high-quality treatment is a treatment aimed at controlling a metal structure, particularly a macro structure. In the high-quality treatment, for example, it is preferable to have a holding time of 2 hours or more and 12 hours or less at a low temperature of 10 ° C. or higher than the holding temperature in the main sintering step and a high temperature of 10 ° C. or higher than the holding temperature in the solution treatment. . From the viewpoint of the diffusion rate of elements, it is impossible to completely remove the heterogeneous phase generated during sintering only by solution treatment. Also, solution treatment alone may not be sufficient to ensure sufficient grain growth. Therefore, high-quality treatment can be performed to further promote removal of foreign phases and grain growth.

  The holding temperature during the high-quality treatment is preferably, for example, 1140 ° C. or higher and 1190 ° C. or lower. When the temperature is lower than 1140 ° C. or higher than 1190 ° C., the magnetic properties may be deteriorated. In addition, when the retention time of the high-quality treatment is less than 2 hours, the element diffusion becomes insufficient, the removal of the heterogeneous phase is not sufficiently performed, and the effect for improving the magnetic characteristics becomes small. On the other hand, when the holding time exceeds 12 hours, the evaporation amount of the element R increases, and it becomes difficult to obtain good magnetic properties. Note that the heat treatment time in the high-quality treatment is preferably 4 hours or longer and 10 hours or shorter, and more preferably 6 hours or longer and 8 hours or shorter. In order to prevent oxidation, the high-quality treatment is more preferably performed under vacuum or in an inert gas atmosphere such as Ar gas.

  Next, an aging treatment is performed on the sintered body. The aging process is a process performed for the purpose of controlling the metal structure and increasing the coercive force of the magnet. Therefore, the metal structure of the magnet is phase-separated into a plurality of phases by aging treatment. The aging treatment temperature for the purpose of improving the coercive force is raised from 700 ° C. to 900 ° C., and the treatment is performed at the holding temperature for 30 minutes to 80 hours. Then, the temperature is lowered at a rate of 0.2 ° C./min to 2.0 ° C./min, gradually cooled to a temperature of 400 ° C. to 650 ° C., and held at an ultimate temperature for 30 minutes to 8 hours. .

  In order to maintain a high coercive force and to form a metal structure having a high recoil permeability, heat treatment conditions different from the aging treatment temperature are required. For example, the holding temperature is set to 900 ° C. or higher in the first holding to appropriately promote the presence of a heterogeneous phase that has been a concern. For example, when kept at 910 ° C. for 40 hours, a heterogeneous phase that has not been seen in the grains until now occurs. Due to the presence of this different phase, a square shape is lowered, and a magnet having a high recoil permeability can be obtained. At a holding temperature of 930 ° C. or higher, the coercive force decreases rapidly, and it is not possible to produce a high recoil permeability magnet having good magnetic properties. The aging treatment holding temperature is preferably 900 ° C. or higher and lower than 930 ° C. The holding time is preferably 30 minutes or longer and 80 hours or shorter. If the holding temperature is less than 900 ° C., the squareness ratio becomes high and the recoil permeability becomes low. On the other hand, when the holding temperature exceeds 930 ° C., the coercive force is rapidly reduced.

  Moreover, the temperature increase rate at the time of reaching the holding temperature in the aging treatment is 5.0 ° C./min or more and 15 ° C./min or less. This is to produce a magnet having sufficient coercive force and recoil permeability with high reproducibility by controlling the heterogeneous concentration and distribution form in the metal structure and reducing variations in magnetic properties. It is preferable that the rate of temperature increase to the holding temperature is 15 ° C./min or more and 35 ° C./min or less. The temperature rising rate affects the diffusion rate and the degree of diffusion of the element, and thus affects the distribution of the forming phase. For example, at a heating rate of 30 ° C./min, a magnet with almost no variation and uniform characteristics can be produced.

At the time of slow cooling from the first holding temperature to the next holding temperature, if the cooling rate is less than 0.2 ° C./min, the thickness of the cell wall phase increases and the magnetization tends to decrease. Moreover, when it exceeds 2.0 degreeC / min, Cu concentration gradient of a cell phase and a cell wall phase cannot fully be applied, but the fall of a coercive force becomes remarkable. The cooling rate during slow cooling is, for example, 0.4 ° C./min or more and 1.5 ° C./min or less, more preferably 0.5 ° C./min or more and 1.3 ° C./min or less. Moreover, when it cools to less than 400 degreeC, a heterogeneous phase will become easy to form. When gradually cooling to a temperature exceeding 650 ° C., the Cu concentration in the Cu-rich phase becomes inappropriate, and a sufficient coercive force may not be obtained. Further, when the holding time in the second holding is less than 30 minutes or more than 8 hours, the heterogeneous phase concentration becomes excessive and sufficient magnetic properties may not be obtained.
A permanent magnet can be manufactured by the above process. In the above manufacturing method, a permanent magnet having high responsiveness to an external magnetic field can be manufactured while maintaining a suitable coercive force and also having high recoil permeability.

Here, the permanent magnet 7 having a high recoil permeability is less likely to be magnetized than an Nd magnet or the like. For this reason, the permanent magnet 7 is magnetized in advance before the permanent magnet 7 is embedded in the rotor core 4, and then the permanent magnet 7 is embedded in the rotor core 4.
Further, the permanent magnet 7 always generates a magnetic field in the opposite direction to the magnetization (hereinafter referred to as a demagnetizing field). Here, when the demagnetizing field is Hd and the demagnetizing factor is N, the demagnetizing field Hd is
Hd = −NJ (2)
It can be expressed as The demagnetizing factor is a numerical value derived from the shape of the magnet. In general, the permeance coefficient: Pc is defined by the following equation without using the demagnetizing factor N, and magnetic field analysis or the like is performed.
Pc = −Bd / Hd (3)

  Here, the larger the cross-sectional area perpendicular to the magnetization direction or the smaller the thickness in the magnetization direction, the larger the demagnetizing field Hd, and the smaller the permeance coefficient Pc. In particular, a permanent magnet having a high recoil permeability is excellent in responsiveness to an external magnetic field, but is demagnetized under the influence of a demagnetizing field due to the influence of shape permeance.

FIG. 3 shows the change of the demagnetization factor with respect to the permeance coefficient when the vertical axis is the demagnetization factor (Bx / Br) and the horizontal axis is the permeance coefficient. It is the graph compared with the Nd magnet.
As shown in FIG. 3, it can be confirmed that the demagnetization factor of the Nd magnet hardly changes depending on the permeance coefficient. On the other hand, the demagnetization factor of a permanent magnet having a high recoil permeability varies greatly depending on the permeance coefficient. In particular, when the permeance coefficient is smaller than 2, it can be confirmed that the demagnetization factor decreases rapidly.

  From the above, in the permanent magnet 7 having a high recoil permeability, it is necessary to reduce and suppress the influence of self-demagnetization due to shape permeance as much as possible. Without increasing the input current by suppressing demagnetization. Torque due to magnet magnetic flux in the rotor core during low-speed operation can be secured. In order to increase the shape permeance coefficient, the bulky body 8 is attached to one surface 7a of the permanent magnet 7 in order to increase the thickness in the magnetization direction (hereinafter referred to as magnet thickness), thereby forming the magnet composite 30. Then, the magnet composite 30 is magnetized. Thereby, the permanent magnet 7 becomes the magnet composite 30 and has a pseudo shape permeance coefficient. And the influence of the demagnetizing field of the permanent magnet 7 becomes small, and the magnetic flux amount reduction by self-demagnetization is suppressed.

Based on FIG. 4, FIG. 5, the shape of the magnet composite 30 is demonstrated concretely, giving an Example and a comparative example.
FIG. 4 is an explanatory diagram of the difference in effect between the magnet composite 30 and the comparative example, where (a) shows the first embodiment of the magnet composite 30 and (b) shows the magnet composite. 30 shows a second example, (c) shows a first comparative example, and (d) shows a second comparative example. FIG. 5 is a table showing the measurement results of the respective examples and comparative examples of FIG. In the following description, the thickness direction corresponds to the thickness direction (short direction) of the permanent magnet 7 as viewed from the direction of the rotation axis P shown in FIG. The magnetization direction of the permanent magnet 7 is the thickness direction (short direction).

Here, as shown in FIGS. 4A and 5, in the first embodiment of the magnet composite 30, the thickness T1 of the permanent magnet 7 is set to 5 mm, and the thickness of the bulky body 8 is set to 6 mm. Further, as shown in FIGS. 4B and 5, in the second embodiment of the magnet composite 30, the thickness T1 of the permanent magnet 7 is 5 mm, and the thickness of the bulky body 8 is 2.5 mm. .
On the other hand, as shown in FIGS. 4C and 5, in the first comparative example, the bulky body 8 is attached only with the permanent magnet 7, and the thickness T <b> 1 of the permanent magnet 7 is 11 mm. . Further, as shown in FIGS. 4D and 5, in the second comparative example, the bulky body 8 is attached only by the permanent magnet 7, and the thickness T <b> 1 of the permanent magnet 7 is 5 mm.

Under the configuration as described above, the amount of magnetic flux: Φ of the first example, the second example, the first comparative example, and the second comparative example was measured. The measurement was performed by applying a gauss meter probe sensor to the easy surface of the magnet and each portion obtained by dividing the easy magnet surface (surface perpendicular to the magnetization direction) into nine equal squares.
As shown in FIG. 5, the measurement result was Φ = 140 [Gauss] in Comparative Example 1, and the result was Φ = 110 [Gauss] in Comparative 2. In other words, it was confirmed that the magnet with a smaller magnet thickness was demagnetized by the influence of the demagnetizing field.

  On the other hand, in Example 1, although it was a magnet of the magnitude | size equivalent to the comparative example 2, the magnetic flux amount: (PHI) became the result equivalent to the comparative example 1. Also in Example 2, although the magnet was the same size as that in Comparative Example 2, the amount of magnetic flux was larger than that in Comparative Example 2. That is, it was confirmed that by attaching the bulky body 8, the influence of the demagnetizing field was suppressed and the amount of magnetic flux was maintained.

Next, the operation of the rotating electrical machine 1 will be described.
When a current is supplied to the armature winding 24 of the stator 20, an interlinkage magnetic flux is formed. A magnetic attractive force or repulsive force is generated between the interlinkage magnetic flux and the magnetic flux generated by the permanent magnet 7 of the rotor 2, and the rotor 2 rotates.
Further, a q-axis magnetic path is formed in the rotor 2 along the longitudinal direction of the permanent magnet 7. On the other hand, almost no magnetic path is formed on the d-axis by the permanent magnet 7, the third flux barrier 11, and the fourth flux barrier 12. For this reason, a direction in which the interlinkage magnetic flux of the stator 20 easily flows and a direction in which the flux hardly flows are formed in the rotor core 4. The reluctance torque generated thereby contributes to the rotation of the rotor 2.

Thus, the rotor 2 is efficiently rotated by the magnetic flux generated by the permanent magnet 7 and the reluctance torque. And the rotational torque of the rotor 2 can be improved.
The bulky body 8 embedded in the rotor core 4 is formed of the same material as the rotor core 4. For this reason, the bulky body 8 does not disturb the magnetic path of the magnetic flux of the permanent magnet 7 and the magnetic path of the interlinkage magnetic flux of the stator 20. Moreover, since the magnetic permeability of the rotor core 4 and the bulky body 8 is 10 or more, the flux linkage of the stator 20 is easy to pass and the rotational torque is easily improved.

FIG. 6 is a graph showing changes in rotational torque when the vertical axis is the rotational torque of the rotor 2 and the horizontal axis is the rotational speed of the rotor 2, and the permanent magnet 7 has a permanent recoil permeability. A comparison is made between the case where a magnet (this embodiment) is used and the case where a conventional permanent magnet (conventional) such as an Nd magnet is used.
As shown in FIG. 6, according to the rotating electrical machine 1 of the present embodiment, the rotational torque of the rotating electrical machine 1 can be improved in both cases of low speed rotation and high speed rotation, as compared with the conventional case.

  As described above, in the above-described embodiment, the housing hole 6 is formed in the rotor core 4, and the magnet complex 30 is provided so as to fill the housing hole 6. The magnet complex 30 includes a permanent magnet 7 and a bulky body 8 attached to one surface 7a of the permanent magnet 7, that is, one surface 7a in the magnetization direction of the permanent magnet 7. For this reason, when the permanent magnet 7 is magnetized, the shape permeance coefficient can be increased in a pseudo manner by magnetizing the magnet composite 30. As a result, the influence of the demagnetizing field of the permanent magnet 7 is reduced, the reduction of the amount of magnetic flux due to self-demagnetization is suppressed, and the magnetic flux of the permanent magnet 7 is compared with the case where the bulky body 8 is not attached to the one surface 7a of the permanent magnet 7. The amount can be increased. Therefore, the rotational torque of the rotating electrical machine 1 can be improved.

The bulky body 8 is formed of the same material as the rotor core 4. For this reason, it can prevent that the bulky body 8 obstructs the magnetic path of the magnetic flux of the permanent magnet 7, and the magnetic path of the interlinkage magnetic flux of the stator 20. Therefore, the rotational torque of the rotating electrical machine 1 can be stably improved.
Furthermore, since the magnetic permeability of the rotor core 4 and the bulky body 8 is 10 or more, the interlinkage magnetic flux of the stator 20 can easily pass and the rotational torque can be further improved.

Moreover, as the permanent magnet 7, a permanent magnet having a high recoil permeability exceeding 1.1 is used. Such a permanent magnet 7 has a particularly remarkable effect that a sufficient amount of magnetic flux can be obtained. Furthermore, the rotational torque of the rotating electrical machine 1 can be improved in both cases of low-speed rotation and high-speed rotation as compared with the conventional case.
Moreover, the magnet composite 30 has a permeance coefficient of 2.0 or more. For this reason, as shown in FIG. 3, it can prevent that the demagnetization rate of the permanent magnet 7 falls remarkably.

  In the above-described embodiment, the case where the same material as the rotor core 4 is used as the bulky body 8 has been described. However, the present invention is not limited to this, and various materials can be used as the bulk body 8. For example, the shape permeance coefficient can be increased even if a resin or the like is used as the bulky body 8. However, when resin is used as the bulky body 8, the magnetic path of the magnetic flux of the permanent magnet 7 and the magnetic path of the interlinkage magnetic flux of the stator 20 may be obstructed. Design is required.

  In the above-described embodiment, the magnet composite 30 is magnetized in advance before the magnet composite 30 is embedded in the rotor core 4, and then the magnet composite 30 is embedded in the rotor core 4. did. However, the present invention is not limited to this, and the magnet composite 30 may be magnetized after the magnet composite 30 is embedded in the rotor core 4. Even in this case, since an interface is formed between the rotor core 4 and the magnet composite 30, the amount of magnetic flux of the permanent magnet 7 compared with the case where the permanent magnet 7 is magnetized alone. Can be increased.

In the above-described embodiment, the magnet composite 30 is arranged such that the opposite side of the outer peripheral surface 4a of the rotor core 4 of the permanent magnet 7 is the one surface 7a to which the bulky body 8 is attached. explained. However, the present invention is not limited to this, and the magnet composite 30 is placed in the rotor core 4 so that the one surface 7 a to which the bulky body 8 of the permanent magnet 7 is attached faces the outer peripheral surface 4 a side of the rotor core 4. You may arrange.
In the above-described embodiment, the case where the short direction of the permanent magnet 7 is the thickness direction and the thickness direction is the magnetization direction has been described. However, the present invention is not limited to this, and the longitudinal direction of the permanent magnet 7 may be the magnetization direction. In this case, the bulky body 8 is provided at either one of the longitudinal end portions 7a and 7b.

  Moreover, the rotary electric machine 1 in the above-mentioned embodiment may be mounted in the following generators 100, for example.

FIG. 7 is a schematic configuration diagram of the generator 100.
That is, as shown in FIG. 7, the generator 100 includes the rotating electrical machine 1. The rotor 2 is connected via a turbine 101 provided at one end of the generator 100 and a shaft 102. This shaft 102 is connected to the shaft 3 of the rotor 2. The turbine 101 is rotated by a fluid supplied from the outside, for example.
Note that the shaft 102 can be rotated by transmitting dynamic rotation such as regenerative energy of an automobile in place of the turbine 101 rotated by a fluid.

Further, the shaft 102 is in contact with a commutator (not shown) disposed on the opposite side of the turbine 101 from the rotor 2. Then, the electromotive force generated by the rotation of the rotor 2 is boosted to the system voltage and transmitted as the output of the generator 100 via the phase separation bus and the main transformer (not shown).
The generator 100 may be either a normal generator or a variable magnetic flux generator. The rotor 2 is charged by static electricity from the turbine 101 or an axial current accompanying power generation. For this reason, the generator 100 includes a brush 103 for discharging the charge of the rotor 2.

  Moreover, the rotary electric machine 1 in the above-described embodiment may be mounted on, for example, the following railway vehicle (an example of a vehicle) 200.

FIG. 8 is a schematic configuration diagram of a railway vehicle 200 used for railway traffic.
As shown in FIG. 8, the rotating electrical machine 1 is mounted on the railway vehicle 200. The rotating electrical machine 1 may be used as, for example, an electric motor (motor) that outputs driving force by using electric power supplied from an overhead wire or electric power supplied from a secondary battery mounted on the railway vehicle 200. . Moreover, the rotary electric machine 1 may be used as a generator (generator) that converts kinetic energy into electric power and supplies electric power to various loads in the railway vehicle 200, for example. Thus, by using the highly efficient rotating electrical machine 1, the railway vehicle can be run with energy saving.

  Moreover, the rotary electric machine 1 in the above-described embodiment may be mounted on, for example, the following automobile (another example of a vehicle) 300.

FIG. 9 is a schematic configuration diagram of a vehicle 300 such as a hybrid vehicle or an electric vehicle.
As shown in FIG. 9, when the rotating electrical machine 1 is mounted on the automobile 300, the rotating electrical machine 1 is an electric motor that outputs the driving force of the automobile 300 or a generator that converts kinetic energy when the automobile 300 travels into electric power. May also be used.

  The rotating electrical machine 1 described above may be mounted on, for example, industrial equipment (industrial motor), air conditioning equipment (air conditioner / water heater compressor motor), wind power generator, or elevator (winding machine). .

  According to at least one embodiment described above, the housing hole 6 is formed in the rotor core 4, and the magnet complex 30 is provided so as to fill the housing hole 6. The magnet complex 30 includes a permanent magnet 7 and a bulky body 8 attached to one surface 7 a of the permanent magnet 7. For this reason, when the permanent magnet 7 is magnetized, the shape permeance coefficient can be increased in a pseudo manner by magnetizing the magnet composite 30. As a result, the influence of the demagnetizing field of the permanent magnet 7 is reduced, the reduction of the amount of magnetic flux due to self-demagnetization is suppressed, and the magnetic flux of the permanent magnet 7 is compared with the case where the bulky body 8 is not attached to the one surface 7a of the permanent magnet 7. The amount can be increased. Therefore, the rotational torque of the rotating electrical machine 1 can be improved.

The bulky body 8 is formed of the same material as the rotor core 4. For this reason, it can prevent that the bulky body 8 obstructs the magnetic path of the magnetic flux of the permanent magnet 7, and the magnetic path of the interlinkage magnetic flux of the stator 20. Therefore, the rotational torque of the rotating electrical machine 1 can be stably improved.
Furthermore, since the magnetic permeability of the rotor core 4 and the bulky body 8 is 10 or more, the interlinkage magnetic flux of the stator 20 can easily pass and the rotational torque can be further improved.

Moreover, as the permanent magnet 7, a permanent magnet having a high recoil permeability exceeding 1.1 is used. Such a permanent magnet 7 has a particularly remarkable effect that a sufficient amount of magnetic flux can be obtained. Furthermore, the rotational torque of the rotating electrical machine 1 can be improved in both cases of low-speed rotation and high-speed rotation as compared with the conventional case.
Moreover, the magnet composite 30 has a permeance coefficient of 2.0 or more. For this reason, as shown in FIG. 3, it can prevent that the demagnetization rate of the permanent magnet 7 falls remarkably.

  Although several embodiments of the present invention have been described, these embodiments are presented by way of example and are not intended to limit the scope of the invention. These embodiments can be implemented in various other forms, and various omissions, replacements, and changes can be made without departing from the spirit of the invention. These embodiments and their modifications are included in the scope and gist of the invention, and are also included in the invention described in the claims and the equivalents thereof.

DESCRIPTION OF SYMBOLS 1 ... Rotary electric machine, 2 ... Rotor, 3 ... Shaft, 4 ... Rotor iron core, 6 ... Storage hole, 7 ... Permanent magnet, 8 ... Bulk body, 20 ... Stator, 24 ... Armature winding, 30 ... Magnet complex, 100 ... generator, 200 ... railway vehicle (vehicle), 300 ... automobile (vehicle), P ... rotation axis

Claims (7)

A shaft that rotates about the axis of rotation;
A rotor core fixed to the shaft;
A storage hole formed in the rotor core;
A magnet composite housed in the housing hole;
With
The magnet complex is
A plate-like permanent magnet;
A bulky body attached to one surface of the magnetization direction in a direction perpendicular to the rotational axis direction of the permanent magnet;
Rotor consisting of The rotor according to claim 1, wherein the bulky body is formed of the same material as the rotor core. The rotor according to claim 2, wherein the rotor core and the bulky body have a magnetic permeability of 10 or more. The rotor according to any one of claims 1 to 3, wherein the permanent magnet has a recoil permeability exceeding 1.1. The rotor according to any one of claims 1 to 4, wherein the magnet complex has a permeance coefficient of 2.0 or more. The rotor according to any one of claims 1 to 5,
A stator around which an armature winding is wound to apply a rotational force to the rotor;
Rotating electric machine with A vehicle comprising the rotating electrical machine according to claim 6.

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