JP2016149395A - R-t-b series sintered magnet - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide an R-T-B series sintered magnet excellent in magnetization while maintaining a high coercive force H.SOLUTION: An R-T-B series sintered magnet 10 includes: main phase grains 1, composed of RTB type crystals; and grain boundary phases 3, existing around the main grains composed of RTB type crystals. Inside the main phase grains 1, composed of RTB type crystals, soft magnetic phases 4 are generated.SELECTED DRAWING: Figure 1

Description

The present invention relates to a rare earth permanent magnet, and more particularly to a rare earth magnet with a controlled microstructure of an RTB sintered magnet.

Rare-earth permanent magnets have been used in various fields because of their high magnetic properties. In particular, R-T-B-based sintered magnets (R is a rare earth element and T is one or more elements containing Fe as an essential element). The iron group element (B represents boron) exhibits excellent properties and has been a typical high performance permanent magnet since the invention of 1982.

The rare earth element R is Nd, Pr, Dy, Ho, R-T-B based sintered magnet made of Tb is preferably anisotropic magnetic field _{H a} is as large permanent magnet material. Among these, Nd-Fe-B magnets with rare earth elements R as Nd and transition metal elements T as Fe have a good balance of magnetic properties, and R-T-B systems using other rare earth elements R in terms of resource and corrosion resistance. Because it is superior to sintered magnets, it is widely used in consumer, industrial and transportation equipment.

In recent years, for example, with the spread of environmentally friendly hybrid vehicles (HV) and electric vehicles (EV), permanent magnets having a larger coercive force _HcJ have been demanded. In an R-T-B based sintered magnet, it is known that the coercive force _HcJ is improved by _refining main phase particles (hereinafter referred to as main phase particles) made of R ₂ T ₁₄ B type crystals. It is actively researched. However, when the main phase particles are miniaturized, the magnetization is deteriorated, so that a larger magnetizing magnetic field is required for magnetization (Non-patent Document 1). The RTB-based sintered magnet for motors often employs so-called assembly magnetization that is magnetized after being incorporated in the motor in an unmagnetized state, and is necessary for sufficiently magnetizing practically. It may be difficult to apply a strong magnetic field. A magnet with insufficient magnetization cannot obtain desired magnetic characteristics (particularly, residual magnetic flux density B _r ).

  As an attempt to improve magnetism, for example, Patent Document 1 discloses a method of mixing FeCo powder with raw powder of an RTB-based sintered magnet. Patent Document 2 discloses a method for producing an RTB-based sintered magnet in which a metal element is unevenly distributed at grain boundaries by attaching an organometallic compound to the surface of a magnet particle and performing surface treatment. Yes.

Yasuhiro Une, Hayato Sagawa, Journal of the Japan Institute of Metals, Vol. 76, No. 1, 12 (2012)

JP 2003-217918 A JP2011-216678A

According to the technique disclosed in Patent Document 1, the magnetization is improved by configuring the RTB-based sintered magnet in which the FeCo phase is mixed. However, in this technique, since the FeCo phase has the same size as the main phase particles and segregates as the grain boundary phase, the coercive force _HcJ is inevitably lowered.

In Patent Document 2, although magnetism is improved by an R-T-B system sintered magnet in which metal elements are unevenly distributed at grain boundaries, the average particle size of main phase particles to which this method can be applied is 3 large as .5Myuemu～5.0Myuemu, when the finer the average particle size of main phase grains in order to obtain a high coercivity H _cJ can not improve magnetizability.

The present invention has been made in view of such a situation, and an object of the present invention is to provide an RTB-based sintered magnet having good magnetization while maintaining a high coercive force _HcJ .

In order to solve the above-described problems, the present inventors reduce the coercive force H _cJ by controlling the amount of the soft magnetic phase generated in the main phase particles of the _RTB -based sintered magnet. It has been found that the magnetization can be controlled without any problems.

Here, it is assumed that the soft magnetic material forming the soft magnetic phase has a coercive force _HcJ of 120 Oe or less.

That is, the present invention is characterized in that the RTB-based sintered magnet includes main phase particles made of R ₂ T ₁₄ B type crystals in which a soft magnetic phase is generated.

According to the present invention, in an RTB-based sintered magnet including main phase particles, the magnetization of fine main phase particles considered to be particularly poor in magnetism is improved. That is, the soft magnetic phase generated inside the main phase particles is easily magnetized in the initial magnetization process, and magnetic domains are generated inside the main phase particles starting from the soft magnetic phase. For this reason, it is presumed that the magnetization of fine main phase particles becomes easy and the magnetization is improved. On the other hand, in the demagnetization process, the main phase particles in which the soft magnetic phase is generated undergo magnetization reversal starting from the soft magnetic phase in a low magnetic field. However, main phase particles in which no soft magnetic phase is generated have no origin of magnetization reversal. Further, since the main phase particles are separated by the grain boundary phase, the propagation of magnetization reversal between the particles is suppressed, and the magnetization reversal does not proceed in the main phase particles in which no soft magnetic phase is generated. As a result, it is presumed that the decrease of the coercive force _HcJ due to the soft magnetic phase is suppressed.

  This soft magnetic phase is widely distributed in the RTB-based sintered magnet, and it is presumed that the finer the main phase particles, the easier the soft magnetic phase is generated inside.

  Preferably, the soft magnetic phase is a soft magnetic material containing one or more of Fe or Co.

According to the present invention, the soft magnetic phase is made of a soft magnetic material containing one or more of Fe or Co, so that R-T-B having better magnetization can be obtained without reducing the coercive force H _cJ. A system sintered magnet can be obtained.

  Preferably, in the RTB-based sintered magnet, the soft magnetic phase of the soft magnetic phase calculated by dividing the sum of the cross-sectional areas of the soft magnetic phase inside the magnet by the sum of the cross-sectional areas inside the magnet. The area ratio is 0.03% or less.

According to the present invention, in the RTB-based sintered magnet, the soft magnetic phase calculated by dividing the total cross-sectional area of the soft magnetic phase inside the magnet by the total cross-sectional area inside the magnet. By setting the area ratio of the magnetic phase to 0.03% or less, it is possible to obtain an RTB-based sintered magnet with further excellent magnetization without reducing the coercive force _HcJ .

  Preferably, in the RTB-based sintered magnet, the soft magnetic phase of the soft magnetic phase calculated by dividing the sum of the cross-sectional areas of the soft magnetic phase inside the magnet by the sum of the cross-sectional areas inside the magnet. The area ratio is 0.0001% or more.

According to the present invention, in the RTB-based sintered magnet, the soft magnetic phase calculated by dividing the total cross-sectional area of the soft magnetic phase inside the magnet by the total cross-sectional area inside the magnet. By setting the area ratio of the magnetic phase to 0.0001% or more, it is possible to obtain an R-T-B based sintered magnet with better magnetization without reducing the coercive force H _cJ .

Preferably, the average particle size of the main phase particles made of the R ₂ T ₁₄ B type crystal is 0.7 to 3.5 μm.

According to the present invention, by setting the average particle size of the main phase particles made of the R ₂ T ₁₄ B type crystal to 0.7 to 3.5 μm, it is possible to further increase the magnetization without reducing the coercive force H _cJ. A good RTB-based sintered magnet can be obtained. If it is 0.7 μm or less, the total number of fine main phase particles composed of R ₂ T ₁₄ B-type crystals increases, and the total number of main phase particles in which the generation of a soft magnetic phase is not confirmed even though it is fine increases. As a result, the effect of improving magnetism is reduced. Further, if it is 3.5 μm or more, the coercive force H _cJ is lowered.

The average particle size of the main phase particles is more preferably 1.0 to 3.5 μm.

  Preferably, the RTB-based sintered magnet contains 0.75 to 1.1 wt% of B.

According to the present invention, the RTB-based sintered magnet contains B in an amount of 0.75 to 1.1 wt%, so that R- with better magnetization can be obtained without decreasing the coercive force _HcJ. A TB sintered magnet can be obtained. When B is less than 0.75 wt%, a heterogeneous phase typified by the R ₂ T ₁₇ phase is generated, and a high coercive force H _cJ cannot be obtained. On the other hand, when B exceeds 1.1 wt%, a heterogeneous phase typified by RT ₄ B ₄ phase occurs, and a high coercive force H _cJ cannot be obtained.

As described above, according to the present invention, the RTB-based sintered magnet includes main phase particles in which a soft magnetic phase is generated, so that the soft magnetic phase can be easily formed by an external magnetic field. Since the main phase particles are magnetized along with the magnetization, an RTB-based sintered magnet having good magnetization can be obtained without reducing the coercive force _HcJ .

  The effect of the present invention is achieved by including main phase particles in which a soft magnetic phase is generated in an R-T-B sintered magnet. For example, the rare earth element R is any rare earth element. Even if it is R, the effect of the present invention is not disturbed.

FIG. 1 is a view showing a photograph of a structure containing main phase particles in which a soft magnetic phase is generated in an RTB-based sintered magnet according to an embodiment of the present invention.

Hereinafter, the present invention will be described in detail based on embodiments. In addition, this invention is not limited by the content described in the following embodiment and an Example. In addition, constituent elements in the embodiments and examples described below include those that can be easily assumed by those skilled in the art, those that are substantially the same, and those in a so-called equivalent range. Furthermore, the constituent elements disclosed in the embodiments and examples described below may be appropriately combined or may be appropriately selected and used.

  FIG. 1 is a view showing a photograph of a structure containing main phase particles in which a soft magnetic phase is generated in an RTB-based sintered magnet according to an embodiment of the present invention.

  As shown in FIG. 1, the RTB-based sintered magnet 10 includes a main phase particle 1 in which a soft magnetic phase is generated, a main phase particle 2 in which no soft magnetic phase is generated, and a grain boundary phase 3. including. Furthermore, subphases, such as R rich phase, may be included. A soft magnetic phase 4 is generated inside the main phase particle 1 in which a soft magnetic phase is generated.

In the R-T-B based sintered magnet 10 including the main phase particles 1 and 2, the magnetization of fine main phase particles made of R ₂ T ₁₄ B type crystal, which is considered to have particularly poor magnetization, is improved. That is, the soft magnetic phase 4 generated inside the main phase particle 1 is easily magnetized in the initial magnetization process, and a magnetic domain is generated inside the main phase particle 1 starting from the soft magnetic phase 4. Therefore, it is assumed that the magnetization of the fine main phase particles 1 becomes easy and the magnetization is improved. On the other hand, in the demagnetization process, the main phase particle 1 in which a soft magnetic phase is generated undergoes magnetization reversal starting from the soft magnetic phase 4 in a low magnetic field. However, the main phase particle 2 in which no soft magnetic phase is generated has no origin of magnetization reversal. Further, since the main phase particles 1 and 2 are separated by the grain boundary phase 3, propagation of magnetization reversal between the particles is suppressed, and magnetization reversal proceeds in the main phase particle 2 in which no soft magnetic phase is generated. Absent. As a result, it is presumed that the decrease of the coercive force _HcJ due to the soft magnetic phase is suppressed.

The main phase particles 1 in which the soft magnetic phase 4 is generated are widely distributed in the R-T-B type sintered magnet 10, and further, fine main phase particles made of R ₂ T ₁₄ B type crystals. It is estimated that the soft magnetic phase 4 is more easily generated in the main phase particles.

The RTB-based sintered magnet 10 contains 25 to 35 wt% of rare earth element R. When the amount of R is less than 25 wt%, a phase effective for improving the coercive force H _cJ such as the R rich phase constituting the grain boundary phase 3 is not sufficiently generated, and the coercive force H _cJ is lowered. On the other hand, when the amount of R exceeds 35 wt%, the volume ratio of the R ₂ T ₁₄ B phase, which is the main phase composed of the R ₂ T ₁₄ B type crystal, decreases, and the residual magnetic flux density _Br decreases.

This RTB-based sintered magnet 10 contains 0.75 to 1.1 wt% of B. When B is less than 0.75 wt%, a high coercive force H _cJ cannot be obtained. On the other hand, even when B exceeds 1.1 wt%, a high coercive force H _cJ cannot be obtained.

The RTB-based sintered magnet 10 can contain 4.0 wt% or less of Co. Co forms the same phase as Fe, but is effective in improving the Curie temperature _Tc and improving the corrosion resistance of the grain boundary phase 3.

  This RTB-based sintered magnet 10 allows the inclusion of other elements. For example, elements such as Zr, Ti, Bi, Sn, Ga, Nb, Ta, Si, V, Ag, Ge, Al, and Cu can be appropriately contained. On the other hand, it is desirable to reduce the content of impurity elements such as O, N, and C as much as possible. In particular, the content of O that lowers the magnetic properties is desirably 5000 ppm or less, more preferably 3000 ppm or less. If the content of O is large, the rare earth oxide phase, which is a nonmagnetic component, increases and the magnetic properties are deteriorated.

  Hereinafter, a suitable example of the manufacturing method of the RTB system sintered magnet in this embodiment is explained.

In the manufacture of the R-T-B system magnet of this embodiment, first, a raw material alloy is prepared so that an R-T-B system sintered magnet having a desired composition can be obtained. The raw material alloy can be produced by a strip casting method or other known melting methods in a vacuum or an inert gas, preferably in an Ar atmosphere.

The raw material alloy is subjected to a pulverization process. The pulverization step includes a first pulverization step, a heat treatment step after the first pulverization step, a second pulverization step, and a third pulverization step. In the first pulverization step, the raw material alloy can be pulverized by hydrogenating the raw material alloy to make it non-uniform and then dehydrogenating and recombining. The dehydrogenation treatment of the raw material alloy is performed for the purpose of reducing hydrogen as an impurity as a rare earth sintered magnet. By recombination as Nd ₂ Fe ₁₄ B by this dehydrogenation treatment, a pulverized Nd ₂ Fe ₁₄ B structure is obtained. The temperature of the hydrogenation and dehydrogenation treatment is 500 to 700 ° C. in the present embodiment. The holding time varies depending on the relationship with the holding temperature, the thickness of the raw material alloy, and the like, but in this embodiment, it is 30 minutes to 4 hours. By appropriately controlling the temperature and holding time of this dehydrogenation treatment, the precipitation of the soft magnetic phase can be controlled. The dehydrogenation process is performed in a vacuum or Ar gas flow. As a result, a first pulverized powder having an average primary particle size of about 0.5 μm is obtained.

Next, in order to take the soft magnetic phase precipitated in the first pulverization step into the main phase particles, the first pulverized powder is put in a crucible and heat-treated at 700 to 800 ° C. for 4 to 12 hours in a vacuum. . The heat treatment process is referred to as a first heat treatment process after the pulverization process. Thereby, the heat-treated powder is obtained after the first pulverization step. Thereby, the pulverized powder grows and the soft magnetic phase is taken into the main phase particles.

  Next, the obtained heat-treated powder after the first pulverization step is subjected to the second pulverization step. The pulverization here is performed by a mechanical method using a ball mill, a stamp mill, a jaw crusher, a brown mill or the like, and is preferably performed in an inert gas atmosphere.

After the second pulverization step, the obtained second pulverized powder is subjected to a third pulverization step to obtain a third pulverized powder. A jet mill is mainly used for the pulverization, and the pulverization is performed so that the average particle diameter is 0.6 to 5 μm, and preferably 0.7 to 3.5 μm. The jet mill releases a high-pressure inert gas from a narrow nozzle to generate a high-speed gas flow, accelerates the pulverized powder by this high-speed gas flow, and collides with the pulverized powder, the target or the container wall. It is a method of generating and pulverizing.

After the third pulverization step, the obtained third pulverized powder is subjected to molding in a magnetic field.

The molding pressure in the magnetic field molding may be in the range of 0.3 to 3 ton / cm ² (30 to 300 MPa). The molding pressure may be constant from the start to the end of molding, may increase or decrease gradually, or may vary irregularly. The lower the molding pressure, the better the crystal orientation of the fine powder.However, if the molding pressure is too low, the strength of the molded product will be insufficient and handling problems will occur. select. The final relative density of the molded body obtained by molding in a magnetic field is usually 40 to 60%.

The applied magnetic field may be about 10 to 20 kOe (800 to 1600 kA / m). The magnetic field to be applied is not limited to a static magnetic field, and may be a pulsed magnetic field. A static magnetic field and a pulsed magnetic field can also be used in combination.

Next, the molded body is sintered in a vacuum or an inert gas atmosphere. The sintering temperature and sintering time need to be adjusted according to various conditions such as composition, grinding method, difference in average particle size and particle size distribution, etc., but in this embodiment, sintering is performed at 850 to 1030 ° C. for 4 to 12 hours. did. If the sintering temperature is lower than 850 ° C., densification is insufficient and sufficient residual magnetic flux density _Br cannot be obtained. On the other hand, if the sintering temperature is higher than 1030 ° C., the grain growth proceeds remarkably, and the coercive force H _cJ particularly decreases.

After sintering, the obtained sintered body can be subjected to an aging treatment. This step is an important step for controlling the coercive force _HcJ . When the aging treatment is performed in two stages, holding for a predetermined time is effective at around 800 ° C. and around 600 ° C. In the case where the aging treatment is performed in one stage, the aging treatment near 600 ° C. is preferably performed. In either case, the effect of increasing the coercive force H _cJ is obtained.

As mentioned above, although the form for implementing this invention suitably was demonstrated, it is not limited to this. For example, the structure of the present invention can also be obtained by mixing two alloys having different rare earth amounts, and performing predetermined molding and sintering. At this time, in order to generate a soft magnetic phase in the main phase particles, at least one alloy has a composition containing a large amount of Fe and Co.

  Hereinafter, although the content of the present invention is explained in detail using an example and a comparative example, the present invention is not limited to the following examples.

As Examples 1 to 9, the composition was 32.5 wt% Nd-1.00 wt% B-0.50 wt% Co-0.06 wt% Cu-0.20 wt% Al-Fe. A raw material metal or alloy was blended so as to be bal, and a raw material alloy thin plate was melted and cast by a strip casting method.

The obtained raw material alloy thin plate was subjected to a first pulverization step, and a first pulverized powder was obtained by performing hydrogenation and dehydrogenation treatment at 500 to 700 ° C. and a holding time of 30 minutes to 4 hours. Thereafter, the first pulverized powder was put in a crucible and heat-treated at 700 to 800 ° C. for 12 hours in a vacuum. Then, after performing the 2nd grinding | pulverization with a stamp mill, the lubricant was added. Next, using a jet mill, third pulverization was performed in a high-pressure nitrogen gas atmosphere to obtain a third pulverized powder.

Subsequently, the produced third pulverized powder was put into a mold and molded in a magnetic field. Specifically, molding was performed at a pressure of 140 MPa in a magnetic field of 15 kOe to obtain a molded body of 20 mm × 18 mm × 13 mm. The magnetic field direction was perpendicular to the pressing direction. The obtained molded body was sintered at 850 to 1030 ° C. for 4 to 12 hours. Thereafter, an aging treatment was performed at 800 ° C. and 600 ° C. for 1 hour to obtain a sintered body.

  Table 1 shows the first pulverization step, the first heat treatment step after the pulverization step, and the sintering conditions in this example.

The initial magnetization curves of the obtained sintered bodies corresponding to Examples 1 to 9 were measured with a BH tracer. In the initial magnetization curve, the ratio of the magnetization value M (1 kOe) at H = 1 kOe to the magnetization value M (20 kOe) at H = 20 kOe, M (1 kOe) / M (20 kOe), is defined as the magnetization rate, and The results are shown in Table 1. The coercive force H _cJ was also measured and the results are shown in Table 1.

  The soft magnetic phase present in the main phase particles can be analyzed by the following method. As a specific example, a case of a soft magnetic material containing Fe having a body-centered cubic structure will be described.

The sintered bodies after the measurement corresponding to Examples 1 to 9 were subjected to thermal demagnetization, and then embedded in an epoxy resin, and these were polished to obtain polished cross sections of the respective sintered bodies. The polished surface is observed using a scanning electron microscope (SEM), and the other phases such as the main phase composed of R ₂ T ₁₄ B type crystal and the grain boundary phase are confirmed by the reflected electron composition image (COMPO). did. Furthermore, from energy dispersive X-ray spectroscopy (EDX), a phase in which the Fe concentration in the main phase particles of each sintered body is relatively higher than the main phase composed of R ₂ T ₁₄ B type crystals (Fe rich phase). Confirmed that was generated. Furthermore, when the sintered body was processed into a thin piece and observed with a high-resolution transmission electron microscope (TEM), it was confirmed that the Fe-rich phase was an Fe compound having a body-centered cubic structure. Furthermore, from the analysis of the magnetic flux distribution by electron holography of this compound, it was confirmed that the Fe compound having this body-centered cubic structure is a soft magnetic phase mainly composed of Fe.

Using a scanning electron microscope (SEM), observe the polished cross section of each sintered body over 10 fields of view, and the number of soft magnetic phases mainly in the diameter of 30 nm or more present in the main phase particles. Was measured. The results are shown in Table 1. In Table 1, since there is a difference in the number of main phase particles observed in each sintered body, the amount of the soft magnetic phase containing Fe as a main component was the amount per 1000 μm ^{2 of the} observed cross section. In addition, the area ratio of the soft magnetic phase mainly composed of Fe, which is calculated by dividing the total cross-sectional area of the soft magnetic phase mainly composed of Fe by the sum of the observed cross-sectional areas, is also shown. It is shown in 1.

Furthermore, using a scanning electron microscope (SEM), the polished cross section of each sintered body was observed in 5 fields or more, and the average particle diameter of the main phase particles was measured by image processing. The results are shown in Table 1.

As Example 10, the composition was 31.5 wt% Nd-0.75 wt% B-1.00 wt% Co-0.60 wt% Cu-0.30 wt% Al-1.00 wt% Ga-0.30 wt% Zr-Fe. . A raw material metal or alloy was blended so as to be bal, and a raw material alloy thin plate was melted and cast by a strip casting method.

Then, the 1st, 2nd, 3rd pulverized powder was obtained by the method similar to Examples 1-9, and also the sintered compact was produced. Thereafter, the magnetization rate, the coercive force H _cJ , the number of soft magnetic phases in the main phase particles, the area ratio of the soft magnetic phase, and the average particle size of the main phase particles were measured in the same manner as in Examples 1 to 9. did. The results are shown in Table 1.

As Example 11, the composition was 23.7 wt% Nd-7.00 wt% Pr-0.10 wt% Dy-0.87 wt% B-1.50 wt% Co-1.00 wt% Cu-0.10 wt% Al-0. 50 wt% Ga-0.20 wt% Zr-Fe. A raw material metal or alloy was blended so as to be bal, and a raw material alloy thin plate was melted and cast by a strip casting method.

Then, the 1st, 2nd, 3rd pulverized powder was obtained by the method similar to Examples 1-9, and also the sintered compact was produced. Thereafter, the magnetization rate, the coercive force H _cJ , the number of soft magnetic phases in the main phase particles, the area ratio of the soft magnetic phase, and the average particle size of the main phase particles were measured in the same manner as in Examples 1 to 9. did. The results are shown in Table 1.

As Example 12, the composition was 29.3 wt% Nd-0.20 wt% Dy-0.95 wt% B-3.00 wt% Co-0.30 wt% Cu-0.60 wt% Al-0.30 wt% Ga-0. 60 wt% Zr-Fe. A raw material metal or alloy was blended so as to be bal, and a raw material alloy thin plate was melted and cast by a strip casting method.

Then, the 1st, 2nd, 3rd pulverized powder was obtained by the method similar to Examples 1-9, and also the sintered compact was produced. Thereafter, the magnetization rate, the coercive force H _cJ , the number of soft magnetic phases in the main phase particles, the area ratio of the soft magnetic phase, and the average particle size of the main phase particles were measured in the same manner as in Examples 1 to 9. did. The results are shown in Table 1.

As Example 13, the composition was 25.5 wt% Nd-8.00 wt% Pr-1.10 wt% B-0.30 wt% Co-0.15 wt% Cu-0.40 wt% Al-0.15 wt% Ga-1. .00 wt% Zr-Fe. A raw material metal or alloy was blended so as to be bal, and a raw material alloy thin plate was melted and cast by a strip casting method.

Then, the 1st, 2nd, 3rd pulverized powder was obtained by the method similar to Examples 1-9, and also the sintered compact was produced. Thereafter, the magnetization rate, the coercive force H _cJ , the number of soft magnetic phases in the main phase particles, the area ratio of the soft magnetic phase, and the average particle size of the main phase particles were measured in the same manner as in Examples 1 to 9. did. The results are shown in Table 1.

  As Example 14, a metal or alloy as a raw material was blended so as to have the same composition as in Examples 1 to 9, and a raw material alloy thin plate was melted and cast by a strip casting method.

  The obtained raw material alloy sheet was first pulverized, occluded hydrogen at room temperature, then dehydrogenated with Ar + hydrogen gas flow at 650 ° C., and the coarse pulverization in which the soft magnetic phase was generated on the outer periphery of the main phase particles I got a powder. Thereafter, the heat treatment step after the first pulverization step was not performed, and the second pulverization step and the third pulverization step were performed in the same manner as in Examples 1 to 9 to obtain a third pulverized powder.

Thereafter, a sintered body was produced in the same manner as in Examples 1 to 9, and the magnetization rate, the coercive force H _cJ , the number of soft magnetic phases in the main phase particles, the area ratio of the soft magnetic phase, and the main phase particles The average particle size was measured. The results are shown in Table 1.

Comparative example

As Comparative Examples 1 to 3, metals or alloys as raw materials were blended so as to have the same composition as in Examples 1 to 9, and the raw material alloy thin plates were melted and cast by a strip casting method.

The obtained raw material alloy thin plate was subjected to second pulverization by a stamp mill without performing the first pulverization and heat treatment. Further, a third pulverized powder was obtained in the same manner as in Examples 1-9.

Thereafter, a sintered body was produced in the same manner as in Examples 1 to 9, and the magnetization rate, the coercive force H _cJ , the number of soft magnetic phases in the main phase particles, the area ratio of the soft magnetic phase, and the main phase particles The average particle size was measured. The results are shown in Table 1.

As Comparative Example 4, a metal or alloy as a raw material was blended so as to have the same composition as in Examples 1 to 9, and a raw material alloy thin plate was melted and cast by a strip casting method.

First, second, and third pulverized powders were obtained in the same manner as in Examples 1 to 9, except that the obtained raw material alloy thin plate had a retention time of 12 hours for hydrogenation and dehydration treatment. .

Thereafter, a sintered body was produced in the same manner as in Examples 1 to 9, and the magnetization rate, the coercive force H _cJ , the number of soft magnetic phases in the main phase particles, the area ratio of the soft magnetic phase, and the main phase particles The average particle size was measured. The results are shown in Table 1.

  As Comparative Example 5, a metal or alloy as a raw material was blended so as to have the same composition as in Examples 1 to 9, and a raw material alloy thin plate was melted and cast by a strip casting method.

  The obtained raw material alloy thin plate was subjected to second pulverization by a stamp mill without performing the first pulverization and heat treatment.

  Then, Fe fine powder produced by the water atomization method was added so that the second pulverized powder: Fe fine powder = 98: 2 by weight ratio. Thereafter, a third pulverized powder was obtained in the same manner as in the example.

Thereafter, a sintered body was produced in the same manner as in Examples 1 to 9, and the magnetization rate, the coercive force H _cJ , the number of soft magnetic phases in the main phase particles, the area ratio of the soft magnetic phase, and the main phase particles The average particle size was measured. The results are shown in Table 1.

From Table 1, in any of the examples, the presence of the soft magnetic phase in the main phase particles shows a magnetization rate of 98.2% or more while the coercive force H _cJ is as good as _15.8 kOe or more. It can be seen that the magnetization is improved.

In Examples 2 to 14, the area ratio of the soft magnetic phase in the observation visual field is 0.03% or less. In this case, although the coercive force _HcJ is as good as _15.8 kOe or higher, it shows a high magnetization rate of 98.6% or higher.

Further, in Examples 2 to 4 and 6 to 14, the area ratio of the soft magnetic phase in the observation visual field is 0.0001% or more. In this case, although the coercive force _HcJ is as good as _15.8 kOe or higher, a high magnetization rate of 98.9% or higher is shown.

In Examples 8 to 9, in addition to the soft magnetic phase mainly composed of Fe, a soft magnetic phase mainly composed of Co and a soft magnetic phase that is a FeCo mixture were confirmed. However, although the coercive force H _cJ is as good as _16.2 kOe or more, it shows a magnetization rate of 99.0% or more, and it can be seen that the magnetization is improved.

In Example 1, the average particle size of the main phase particles is 0.7 μm or less. In this case, the coercive force H _cJ is 17.7 kOe, which is equal to or greater than that of the other examples, but the magnetization rate is 98.2%, which is smaller than that of the other examples.

In Example 7, the average particle size of the main phase particles is 3.5 μm or more. In this case, the magnetization rate is 99.5%, which is equal to or greater than that of the other examples, but the coercive force _HcJ is 15.8 kOe, which is smaller than the other examples.

On the other hand, in Comparative Examples 1 to 4, no soft magnetic phase was confirmed in the main phase particles. For this reason, although the coercive force _HcJ is equal to or greater than that of the example, the magnetization rate is 93.4 to 94.8%, which is smaller than any of the examples.

In Comparative Example 5, the soft magnetic phase was not confirmed in the main phase particles, and when the polished cross section of the sintered body was observed with a scanning electron microscope (SEM), Fe was present in the grain boundary phase. It was. For this reason, the magnetization rate is similar to that of the example, but the coercive force H _cJ is as small as _13.9 kOe.

Since the _RTB -based sintered magnet according to the present invention exhibits good magnetization while maintaining a high coercive force _HcJ , they can be widely used for motors for automobiles and the like.

DESCRIPTION OF SYMBOLS 1 ... Main phase particle | grains 2 with which soft magnetic phase was produced | generated ... Main phase particle 3 with which soft magnetic phase was not produced | generated ... Grain boundary phase 4 ... Soft magnetic phase 10 ... R- TB sintered magnet

Claims (5)

An RTB-based sintered magnet, comprising main phase particles made of an R ₂ T ₁₄ B-type crystal in which a soft magnetic phase is generated.   The RTB-based sintered magnet according to claim 1, wherein the soft magnetic phase is a soft magnetic material containing one or more of Fe or Co. In the RTB-based sintered magnet, the area ratio of the soft magnetic phase calculated by dividing the sum of the cross-sectional areas of the soft magnetic phase inside the magnet by the sum of the cross-sectional areas inside the magnet is The RTB-based sintered magnet according to claim 1, wherein the content is 0.03% or less. In the RTB-based sintered magnet, the area ratio of the soft magnetic phase calculated by dividing the sum of the cross-sectional areas of the soft magnetic phase inside the magnet by the sum of the cross-sectional areas inside the magnet is The RTB-based sintered magnet according to claim 3, which is 0.0001% or more. The average particle diameter of the main phase particles composed of the R ₂ T ₁₄ B-type crystal is 0.7 to 3.5 μm, and R-T-B according to claim 1, Sintered magnet.

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