Sintered rare earth magnet, method for producing a sintered rare earth magnet, rotor and rotary machine

Abstract

A sintered rare-earth magnet comprises: a main phase satisfying a general formula (Nd, Pr, RH, R)-Fe-BM, where RH is a heavy rare-earth element including Dy and / or Tb, R is one or more rare-earth elements selected excluding Nd, Pr, Dy, and Tb, and M is one or more elements selected from a group consisting of Ga, Al, Cu, and Co, wherein the main phase contains crystal grains based on an Nd₂Fe₁₄B crystal structure; and a subphase. The main phase comprises a core section and a shell section and includes a first main phase satisfying CNd > CPr and a second main phase satisfying CNd <CPr erfüllt, wobei CNd die Konzentration von Nd im Kernabschnitt und CPr die Konzentration von Pr im Kernabschnitt ist. Die Konzentration des schweren Seltenerdelements RH ist im Kernabschnitt der ersten Hauptphase höher als im Kernabschnitt der zweiten Hauptphase.The first and second main phases are supplied mixed. The subphase comprises a first and a second subphase, consisting mainly of an oxide phase represented by (Nd, Pr, RH, La, Sm)-O, with the element M present as a minor component. The concentration of element M is higher in the second subphase than in the first subphase.

Description

Area The present disclosure relates to a sintered rare-earth magnet, which is a permanent magnet obtained by sintering a material containing a rare-earth element, a method for producing a sintered rare-earth magnet, a rotor and a rotary machine. background RTB-based permanent magnets with a tetragonal intermetallic R2T14B compound as the main phase are known. In this compound, R is a rare-earth element, T is a transition metal such as Fe (iron) or Fe partially replaced by cobalt (Co), and B is boron. RTB-based permanent magnets are used in various high-value components, such as industrial motors. In particular, sintered Nd-Fe-B-based magnets, where R is neodymium (Nd), are used in various components due to their excellent magnetic properties. Since industrial motors are often used in high-temperature environments above 100 °C, attempts have also been made to improve coercivity by adding heavy rare-earth elements such as dysprosium (Dy) to sintered Nd-TB-based magnets. In recent years, the production of sintered magnets based on Nd-Fe-B has expanded, thereby increasing the consumption of Nd, Dy, and terbium (Tb), which are heavy rare-earth elements. However, Nd and heavy rare-earth elements are expensive and pose a procurement risk due to their large uneven distribution. For this reason, techniques to reduce the consumption of Nd and heavy rare-earth elements are currently being investigated. Patent document 1 discloses a sintered RTB-based magnet containing main phase grains composed of an R₂T₁₄B crystal, wherein R is one or more rare-earth elements, including a heavy rare-earth element RH, as an essential element, T is one or more transition metal elements, including Fe or including Fe and Co as an essential element, and B is boron. A portion of the main phase grains of the RTB-based sintered magnet comprises a variety of low-rare-earth crystal phases and a variety of non-magnetic, R-rich phases. The low-rare-earth crystal phases are composed of an R₂T₁₄B crystal in which the concentration of the heavy rare-earth element is relatively lower than the concentration of the heavy rare-earth element in the entire main phase grains.The non-magnetic, rhodium-rich phases have an rhodium content of 70 to 100 at%. Furthermore, some of the main phase grains exhibit a core-shell structure with a core section and a shell section surrounding the core section, exhibiting a total concentration of heavy rare-earth elements that is lower than that of the core section. According to the technique described in patent document 1, it is possible to obtain a sintered RTB-based magnet with improved coercivity at low cost. Patent document 2 discloses a method for producing a rare-earth magnet, comprising: a first step of producing a sintered body represented by a composition formula (R11-xR2x)aTMbBcMd and having a structure consisting of a main phase and a grain boundary phase; a second step of producing a rare-earth magnet precursor by hot plastic processing of the sintered body; and a third step of producing a rare-earth magnet by diffusing a melt of an R3-M-modified alloy and penetrating the grain boundary phase of the rare-earth magnet precursor.Here, R1 is one or more rare earth elements, including Y (yttrium), R2 is a rare earth element other than R1, TM is a transition metal, including one or more of Fe, nickel (Ni) and Co, B is boron and M is one or more of titanium (Ti), gallium (Ga), zinc (Zn), silicon (Si), aluminum (Al), niobium (Nb), zirconium (Zr), Ni, Co, manganese (Mn), vanadium (V), tungsten (W), tantalum (Ta), germanium (Ge), copper (Cu), chromium (Cr), hafnium (Hf), molybdenum (Mo), phosphorus (P), carbon (C), magnesium (Mg), mercury (Hg), silver (Ag) and gold (Au). Furthermore, x, a, b, c, and d satisfy the conditions 0.01 ≤ x ≤ 1, 12 ≤ a ≤ 20, b = 100 - acd, 5 ≤ c ≤ 20, and 0 ≤ d ≤ 3, each in at.%. R3 is a rare-earth element, including R1 and R2. Hereinafter, a plastic hot processing applied to a sintered body is referred to as hot forming.According to the technique described in patent document 2, it is possible to reduce the heavy rare earth element and to produce a rare earth magnet that is excellent not only in terms of magnetization but also in terms of coercive force performance, even when the main phase ratio is high. List of cited works Patent literature Patent document 1: Published Japanese patent application no. 2018-174313 (JP 2018-174313 A) Patent document 2: Published Japanese patent application no. 2015-153813 (JP 2015-153813 A) Brief description of the invention Problem to be solved by the invention However, the RTB-based sintered magnet described in Patent Document 1 contains a phase with a heavy rare-earth element in the main phase. This improves the coercivity but cannot provide the residual magnetic flux density required for industrial motors or similar applications, which can lead to a deterioration of magnetic properties due to thermal stress. While the rare-earth magnet produced using the manufacturing process described in Patent Document 2 can reduce the amount of heavy rare-earth elements and improve the coercivity, this process involves hot forming, which reduces the particle size of the main phase and leads to a deterioration of the residual magnetic flux density and the magnetizability of the produced sintered rare-earth magnet. The present disclosure was conceived in view of the foregoing considerations, one objective being to obtain a sintered rare-earth magnet capable of improving the coercive force without reducing the residual magnetic flux density and magnetizability compared to the related prior art. Means to solve the problem To solve the problems described above and the stated task, a sintered rare-earth magnet according to the present disclosure comprises: a main phase satisfying the general formula (Nd, Pr, RH, R)-Fe-BM, where RH is a heavy rare-earth element including Dy and / or Tb, R is one or more rare-earth elements selected excluding Nd, Praseodymium (Pr), Dy, and Tb, and M is one or more elements selected from a group consisting of Ga, Al, Cu, and Co, wherein the main phase contains crystal grains based on an Nd₂Fe₁₄B crystal structure; and a subphase formed between the main phase and the main phase. The main phase includes a core section and a shell section covering the core section. The main phase includes a first main phase satisfying CNd > CPr, and a second main phase satisfying CNd <CPr erfüllt, wobei CNd die Konzentration von Nd im Kernabschnitt und CPr die Konzentration von Pr im Kernabschnitt ist. Die Konzentration des schweren Seltenerdelements RH im Kernabschnitt der ersten Hauptphase ist höher als die Konzentration des schweren Seltenerdelements RH im Kernabschnitt der zweiten Hauptphase. Die erste Hauptphase und die zweite Hauptphase werden gemischt bereitgestellt.The subphase comprises a first and a second subphase, both of which are crystalline and consist mainly of an oxide phase represented by (Nd, Pr, RH, La, Sm)-O, with the element M present as a minor component. The concentration of element M is higher in the second subphase than in the first subphase. Effects of the invention The sintered rare-earth magnet according to the present disclosure can achieve the effect of improving the coercive force without reducing the residual magnetic flux density and the magnetizability compared to the related prior art. Brief description of the drawings Fig. 1 is a diagram schematically illustrating an exemplary sintered structure of a sintered rare-earth magnet according to a first embodiment. Fig. 2 is a diagram schematically illustrating an exemplary sintered structure of a sintered rare-earth magnet according to the second embodiment. Fig. 3 is a diagram illustrating atomic sites in a tetragonal Nd₂Fe₁₄B crystal structure. Fig. 4 is a flowchart illustrating an exemplary process for producing an alloy for a sintered rare-earth magnet according to the third embodiment. Fig. 5 is a flowchart illustrating an exemplary process for producing a sintered rare-earth magnet according to the third embodiment.Figure 6 is a cross-sectional view schematically illustrating an exemplary configuration of a rotor equipped with a sintered rare-earth magnet according to the fourth embodiment. Figure 7 is a cross-sectional view schematically illustrating an exemplary configuration of a rotary machine according to the fifth embodiment. Figure 8 is a diagram obtained by plotting a composite image obtained by analyzing a cross-section of a sintered rare-earth magnet according to Examples 1 to 8 using a field emission electron probe microanalyzer (FE-EPMA). Figure 9 is an elemental map of Nd obtained by analyzing a cross-section of a sintered rare-earth magnet according to Examples 1 to 8 using FE-EPMA.Figure 10 is an elemental map of Pr obtained by analyzing a cross-section of a sintered rare-earth magnet according to Examples 1 to 8 using FE-EPMA. Figure 11 is an elemental map of Tb obtained by analyzing a cross-section of a sintered rare-earth magnet according to Examples 1 to 8 using FE-EPMA. Figure 12 is an elemental map of Co obtained by analyzing a cross-section of a sintered rare-earth magnet according to Examples 1 to 8 using FE-EPMA. Figure 13 is an elemental map of oxygen (O) obtained by analyzing a cross-section of a sintered rare-earth magnet according to Examples 1 to 8 using FE-EPMA. Figure 14 is an elemental map of samarium (Sm) obtained by analyzing a cross-section of a sintered rare-earth magnet according to Examples 1 to 8 using FE-EPMA. Fig.15 is an elemental map of lanthanum (La) obtained by analyzing a cross-section of a sintered rare-earth magnet according to Examples 1 to 8 using FE-EPMA. Description of the embodiments A sintered rare-earth magnet, a method for producing a sintered rare-earth magnet, a rotor and a rotary machine according to the embodiments of the present disclosure are described in detail below with reference to the drawings. First embodiment. Fig. 1 is a diagram schematically illustrating an exemplary sintered structure of a sintered rare-earth magnet according to the first embodiment. The sintered rare-earth magnet 1 according to the first embodiment comprises a main phase 10, which satisfies the general formula (Nd, Pr, RH, R)-Fe-BM and contains crystal grains based on an Nd₂Fe₁₄B crystal structure, and a subphase 20 located between the main phase 10 and the main phase 10. The main phase 10 comprises a core section and a shell section covering the core section. Here, RH is a heavy rare-earth element and is, for example, one or more elements selected from the group consisting of Dy, Tb, Gd (gadolinium), or Ho (holmium), and preferably a heavy rare-earth element including Dy and / or Tb. R is one or more rare-earth elements selected from Nd, Pr, and RH.M is one or more elements selected from the group consisting of Ga, Al, Cu and Co. The shell section has a different composition than the core section and is provided in such a way that it covers the core section. Therefore, in the sintered rare-earth magnet 1 according to the first embodiment, i.e., the sintered rare-earth magnet 1 comprising the main phase 10 and the sub-phase 20, the general formula is expressed by (NdaPrbRcRHd)FeeBfM, where RH is one or more heavy rare-earth elements selected from the group consisting of Dy, Tb, Gd, and Ho, R is a rare-earth element selected excluding Nd, Pr, and RH, and M is one or more elements selected from a group consisting of Ga, Al, Cu, and Co. It is desirable that a, b, c, d, e, f, and g satisfy the following comparative expressions. The main phase 10 has a tetragonal crystal structure R₂Fe₁₄B in which part of the Nd site is replaced by Pr, the heavy rare-earth element RH, and one or more rare-earth elements R, selected to exclude Nd, Pr, and the heavy rare-earth element RH. That is, the main phase 10 has the composition formula (Nd, Pr, RH, R)₂Fe₁₄B. The element M can enter the main phase 10. If the element M is Co or Cu, i.e., a transition element, it is assumed that the element M replaces part of the Fe site in the Nd₂Fe₁₄B crystal structure. In the sintered rare-earth magnet 1 according to the first embodiment, the main phase 10 includes a first main phase 11 in which CNd>CPr holds, and a second main phase 12 in which CNd <CPr gilt, wobei CNd die Konzentration von Nd in den Kernabschnitten 11c und 12c ist und CPr die Konzentration von Pr in den Kernabschnitten 11c und 12c ist, und die erste Hauptphase 11 und die zweite Hauptphase 12 werden gemischt bereitgestellt. Die Konzentration des schweren Seltenerdelements RH im Kernabschnitt 11c der ersten Hauptphase 11 ist höher als die Konzentration des schweren Seltenerdelements RH im Kernabschnitt 12c der zweiten Hauptphase 12. Das heißt, wenn die Konzentration des schweren Seltenerdelements RH im Kernabschnitt 11c der ersten Hauptphase 11 C1RH ist und die Konzentration des schweren Seltenerdelements RH im Kernabschnitt 12c der zweiten Hauptphase 12 C2RH ist, ist C1RH> C2RH is met.The first main phase 11 includes the core section 11c and a shell section 11s, which has a different composition than the core section 11c and covers the core section 11c. The second main phase 12 includes a core section 12c and a shell section 12s, which has a different composition than the core section 12c and covers the core section 12c. Alternatively, for the rare-earth sintered magnet 1 according to the first embodiment, it can be said that the main phase 10 includes a first main phase 11 that satisfies C(Nd,RH)>CPr, and a second main phase 12 that satisfies C(Nd,RH) <CPr erfüllt, wobei C(Nd,RH) die Summe der Konzentration von Nd und der Konzentration des schweren Seltenerdelements RH in den Kernabschnitten 11c und 12c ist, und die erste Hauptphase 11 und die zweite Hauptphase 12 gemischt bereitgestellt werden. This means that the sintered rare-earth magnet 1 has two types of principal phases 10, i.e., the first principal phase 11 and the second principal phase 12, and in particular with respect to the core sections 11c and 12c of the two types of principal phases 10, in the first principal phase 11 the sum of the concentrations of Nd and the heavy rare-earth element RH is higher than the concentration of Pr, and conversely, in the second principal phase 12 the concentration of Pr is higher than the sum of the concentrations of Nd and the heavy rare-earth element RH. As described above, it is by mixing two types of principal phases 10 with core-shell structures that are in anisotropic magnetic field, i.e.,The magnetic anisotropy differs, and the selective presence of the heavy rare-earth element RH in the main phase 10 makes it possible to reduce Nd and the heavy rare-earth element RH, and also to improve the residual magnetic flux density and the coercive force, while simultaneously maintaining good magnetization. Furthermore, the coercive force is significantly improved by the addition of the heavy rare-earth element RH and the element M, which also helps to prevent a deterioration of the magnetic properties due to temperature changes. Here, the concentration difference indicated by "C1RH>C2RH" means that there is a significant difference in the detection intensity of the heavy rare earth element RH in core section 11c of the first main phase 11 and in core section 12c of the second main phase 12 by map analysis using an electron beam microanalysis (EPMA) device. Specifically, the EPMA detection intensity of the concentration of the heavy rare earth element RH in core section 11c of the first main phase 11 is higher than the average detection intensity of the heavy rare earth element RH, and the EPMA detection intensity of the concentration of the heavy rare earth element RH in core section 12c of the second main phase 12 is close to the lower limit of the detection intensity of the heavy rare earth element RH, or the EPMA detection intensity is lower than the average detection intensity of the heavy rare earth element RH.In one example, the heavy rare earth element RH is contained in the core section 11c of the first main phase 11, but hardly in the core section 12c of the second main phase 12. Furthermore, the first main phase 11, which fulfills C(Nd,RH)>CPr, and the second main phase 12, which fulfills C(Nd,RH) <CPr erfüllt“ angegebene Konzentrationsunterschied, dass ein deutlicher Unterschied zwischen der Nachweisintensität von Nd und dem schweren Seltenerdelement RH und der Nachweisintensität von Pr durch die Kartenanalyse unter Verwendung der EPMA besteht. Konkret ist am Beispiel der ersten Hauptphase 11 die EPMA-Nachweisintensität der Konzentration von Nd und der Konzentration des schweren Seltenerdelements RH im Kernabschnitt 11c höher als der Durchschnitt der Nachweisintensität von Nd und des schweren Seltenerdelements RH, und die EPMA-Nachweisintensität der Konzentration von Pr liegt in der Nähe des unteren Grenzwerts der Nachweisintensität von Pr, oder die EPMA-Nachweisintensität der Konzentration von Pr ist niedriger als der Durchschnitt der Nachweisintensität von Pr. In der zweiten Hauptphase 12 ist der Fall umgekehrt zur ersten Hauptphase 11. The sintered rare-earth magnet 1 according to the first embodiment satisfies the comparative expressions C1Nd>C2Nd and C1Pr <C2Pr, wobei C1Nd die Nd-Konzentration des Kernabschnitts 11c der ersten Hauptphase 11 ist, C2Nd die Nd-Konzentration des Kernabschnitts 12c der zweiten Hauptphase 12 ist, C1Pr die Pr-Konzentration des Kernabschnitts 11c der ersten Hauptphase 11 ist und C2Pr die Pr-Konzentration des Kernabschnitts 12c der zweiten Hauptphase 12 ist. Das heißt, die Nd-Konzentration ist im Kernabschnitt 11c der ersten Hauptphase 11 höher als im Kernabschnitt 12c der zweiten Hauptphase 12, und umgekehrt ist die Pr-Konzentration im Kernabschnitt 12c der zweiten Hauptphase 12 höher als im Kernabschnitt 11c der ersten Hauptphase 11. Der Konzentrationsunterschied bedeutet hier auch, dass ein Unterschied in der Nachweisintensität von Nd und Pr bei der Kartenanalyse mit der EPMA besteht.In the case of the Nd concentration, this specifically means that the EPMA detection intensity of Nd in core section 11c of the first main phase 11 is higher than the average detection intensity of Nd, and that the EPMA detection intensity of Nd in core section 12c of the second main phase 12 is lower than the average detection intensity of Nd. In the case of the Pr concentration, this means that the EPMA detection intensity of Pr in core section 12c of the second main phase 12 is higher than the average detection intensity of Pr, and that the EPMA detection intensity of Pr in core section 11c of the first main phase 11 is lower than the average detection intensity of Pr. This means that a large amount of Pr is present in core section 12c of the second main phase 12 with a low Nd concentration, and conversely, a large amount of Nd is present in core section 11c of the first main phase 11 with a low Pr concentration.The targeted production of such a structural form results in the sintered rare-earth magnet 1 with excellent magnetic properties. In the rare-earth sintered magnet 1 according to the first embodiment, the first main phases 11, each of which satisfies C(Nd,RH)>CPr, are more abundant than the second main phases 12, each of which satisfies C(Nd,RH) <CPr erfüllt. Mit anderen Worten bedeutet dies, dass die Anzahl der ersten Hauptphasen 11 mit der Zusammensetzungsformel (Nd,RH)2Fe14B größer ist als die Anzahl der zweiten Hauptphasen 12 mit der Zusammensetzungsformel Pr2Fe14B. Dies liegt daran, dass eine Zunahme der ersten Hauptphase 11 mit der Zusammensetzungsformel (Nd,RH)2Fe14B zu besseren magnetischen Eigenschaften und besseren Temperatureigenschaften führt als eine Zunahme der zweiten Hauptphase 12 mit der Zusammensetzungsformel Pr2Fe14B. Darüber hinaus verhindert ein gezieltes Herstellen einer solchen Strukturform auch die Verfeinerung der Kristallkörner als Ganzes, so dass im Vergleich zum Stand der Technik hervorragende magnetische Eigenschaften bei gleichzeitiger Gewährleistung der Magnetisierung erzielt werden können.In the sintered rare-earth magnet 1 according to the first embodiment, the first main phase 11 fulfills the comparative expressions CNd>SNd, CPr, particularly with regard to the shell sections 11s and 12s of the core-shell structures.<SPr und CRH> SRH, and the second main phase 12 fulfills the comparison expressions CNd<SNd, CPr> SPr and CRH <SRH, wobei SNd die Konzentration von Nd in den Schalenabschnitten 11s und 12s ist, SPr die Konzentration von Pr in den Schalenabschnitten 11s und 12s ist, CRH die Konzentration des schweren Seltenerdelements RH in den Kernabschnitten 11c und 12c ist und SRH die Konzentration des schweren Seltenerdelements RH in den Schalenabschnitten 11s und 12s ist. Insbesondere sind im Schalenabschnitt 11s der ersten Hauptphase 11 die Konzentration von Nd und die Konzentration des schweren Seltenerdelements RH niedriger als im Kernabschnitt 11c, aber die Konzentration von Pr ist höher als im Kernabschnitt 11c.In shell section 12s of the second main phase 12, the concentration of Pr is lower than in core section 12c, but the concentration of Nd and the concentration of the heavy rare earth element RH are higher than in core section 12c. In other words, in the sintered rare-earth magnet 1 according to the first embodiment, the first main phase 11 satisfies the comparative expressions C(Nd,RH)>S(Nd,RH) and CPr, particularly with respect to the shell sections 11s and 12s of the core-shell structures. <SPr und die zweite Hauptphase 12 die Vergleichsausdrücke C(Nd,RH)<S(Nd,RH) und CPr> SPr, where S(Nd,RH) is the sum of the concentrations of Nd and the heavy rare-earth element RH in shell sections 11s and 12s, and SPr is the concentration of Pr in shell sections 11s and 12s. Specifically, in shell section 11s of the first main phase 11, the sum of the concentrations of Nd and the heavy rare-earth element RH is lower than in core section 11c, but the concentration of Pr is higher than in core section 11c.In shell section 12s of the second main phase 12, the concentration of Pr is lower than in core section 12c, but the sum of the concentration of Nd and the concentration of the heavy rare earth element RH is higher than in core section 12c. By forming the main phase 10 with the shell section 11s with a high concentration of Pr, as in the first main phase 11, the coercive force can be improved. Furthermore, by forming the main phase 10 with the shell section 12s with a high sum of the concentrations of Nd and the heavy rare-earth element RH, as in the second main phase 12, it is possible to prevent a deterioration of the residual magnetic flux density while maintaining the coercive force. Through selective control to achieve such a structural shape, the sintered rare-earth magnet 1 can exhibit excellent magnetic properties compared to the prior art. Furthermore, the average grain size of the crystal grains of the main phase 10 is preferably 100 µm or less, and particularly preferably 0.5 µm to 50 µm, to improve the magnetic properties. Moreover, adjusting the average grain size to approximately 1 µm to 10 µm results in a grain size that differs from the microstructure produced by hot forming, causing the sintered rare-earth magnet 1 to retain good magnetizability and exhibit excellent magnetic properties compared to the prior art. Subphase 20 comprises a first subphase 21, which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, RH, R)-O, containing the element M as a minor component, and a second subphase 22, which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, RH, R)-O, containing the element M as a minor component. O is oxygen. The crystalline subphase 20 is a general term encompassing the first crystalline subphase 21 and the second crystalline subphase 22. Here, (Nd, Pr, RH, R) signifies that some of Nd and Pr are replaced by the heavy rare-earth element RH and the rare-earth element R, respectively, excluding Nd and Pr. R in the first subphase 21 and R in the second subphase 22 can be the same rare-earth element, partially different rare-earth elements, or different rare-earth elements altogether.It should be noted that the elements of the main components are given in parentheses; therefore, the first subphase 21 and the second subphase 22 may contain a small amount of another component in addition to the components given in parentheses. Subphase 20, i.e., the first subphase 21 and the second subphase 22, contain the element M as a minor component as described above. The concentration of the element M contained in the first subphase 21 and the second subphase 22 is higher in the second subphase 22 than in the first subphase 21. That is, the comparative expression Cs1M <Cs2M ist erfüllt, wobei Cs1M die Konzentration des Elements M in der ersten Unterphase 21 und Cs2M die Konzentration des Elements M in der zweiten Unterphase 22 ist. Here, "the concentration of element M is higher in the second sub-phase 22 than in the first sub-phase 21" means that the detection intensity of element M according to map analysis using EPMA is on average higher in the second sub-phase 22 than in the first sub-phase 21. More precisely, this means that the intensity of element M detected by EPMA in the second sub-phase 22 is higher than the average of the intensities of element M detected by EPMA, and the intensity of element M detected by EPMA in the first sub-phase 21 is lower than the average of the intensities of element M detected by EPMA. In subphase 20, element M is present in high concentration in the second subphase 22, thus forming a non-magnetic phase that magnetically separates the main phases 10, thereby improving the magnetic properties. That is, by establishing a higher concentration of element M in the second subphase 22 than in the first subphase 21, high magnetic properties, particularly high coercivity, can be obtained, and a deterioration of magnetic properties associated with a temperature increase can be prevented. The sintered rare-earth magnet 1 according to the first embodiment comprises: the main phase 10, which satisfies the general formula (Nd, Pr, RH, R)-Fe-BM, wherein RH is a heavy rare-earth element, R is one or more rare-earth elements selected excluding Nd, Pr and the heavy rare-earth element RH, and M is one or more elements selected from a group consisting of Ga, Al, Cu and Co, wherein the main phase contains crystal grains based on an Nd₂Fe₁₄B crystal structure; and the subphase 20, which is located between the main phase 10 and the subphase 10. The main phase 10 comprises the core sections 11c and 12c and the shell sections 11s and 12s, which cover the core sections 11c and 12c.Main phase 10 includes the first main phase 11, which fulfills CNd>CPr, and the second main phase 12, which fulfills CNd <CPr erfüllt, die Konzentration des schweren Seltenerdelements RH in der ersten Hauptphase 11 ist höher als die Konzentration des schweren Seltenerdelements RH in der zweiten Hauptphase 12, und die erste Hauptphase 11 und die zweite Hauptphase 12 werden gemischt bereitgestellt. Die Unterphase 20 beinhaltet die erste Unterphase 21 und die zweite Unterphase 22, die kristallin sind und hauptsächlich aus einer Oxidphase bestehen, die durch (Nd, Pr, RH, R)-O dargestellt wird, wobei das Element M als Nebenbestandteil enthalten ist, und die Konzentration des in der ersten Unterphase 21 und der zweiten Unterphase 22 enthaltenen Elements M ist in der zweiten Unterphase 22 höher als in der ersten Unterphase 21.With such a configuration, it is possible to obtain the sintered rare-earth magnet 1, whose magnetic properties and magnetization are improved compared to the prior art, while reducing the use of Nd and the heavy rare-earth element RH. In particular, it is possible to obtain a sintered rare-earth magnet 1 in which the coercive force can be greatly improved without a significant deterioration of the residual magnetic flux density, and in which the temperature coefficient of the magnetic properties is also improved. The sintered RTB-based magnet described in Patent Document 1 is now compared with the sintered rare-earth magnet 1 according to the first embodiment. The RTB-based sintered magnet described in Patent Document 1 has one or more rare-earth elements, which essentially comprise the heavy rare-earth element RH, and has a type of main phase grain consisting of a core section and a shell section. In Patent Document 1, the heavy rare-earth element RH is contained in all main phase grains of the sintered RTB-based magnet. In contrast, the main phase 10 of the sintered rare-earth magnet 1 according to the first embodiment comprises the first main phase 11 and the second main phase 12, and the concentration of the heavy rare-earth element RH is lower in the second main phase 12 than in the first main phase 11.In one example, the core section 11c of the first main phase 11 contains the heavy rare-earth element RH, while the core section 12c of the second main phase 12 contains hardly any of the heavy rare-earth element RH. That is, the heavy rare-earth elements RH are selectively arranged in the main phase 10. As described above, the sintered rare-earth magnet 1 according to the first embodiment, which includes the main phase 10 with the first main phase 11 and the second main phase 12 with a lower concentration of the heavy rare-earth element RH than the first main phase 11, can reduce the amount of the heavy rare-earth element RH used compared to the RTB-based sintered magnet described in patent document 1, in which the heavy rare-earth element RH must be present in all main phases of only one type.In particular, in a case where the heavy rare earth element RH is scarcely contained in the second main phase 12, the heavy rare earth element RH is selectively arranged, and the amount of the heavy rare earth element RH used can be reduced compared to the RTB-based sintered magnet described in patent document 1. The rare-earth magnet produced using the method described in Patent Document 2 is now compared with the sintered rare-earth magnet 1 according to the first embodiment. To obtain magnetic properties in the rare-earth magnet produced using the technique described in Patent Document 2 that correspond to those of the sintered rare-earth magnet 1 according to the first embodiment, more heavy rare-earth elements RH must be added compared to the sintered rare-earth magnet 1 according to the first embodiment, as will be shown in examples described later. That is, the sintered rare-earth magnet 1 according to the first embodiment can reduce the amount of heavy rare-earth element RH compared to the technique described in Patent Document 2 if one attempts to obtain the same magnetic properties.Alternatively, in a case where the content of the heavy rare earth element RH in the rare earth magnet produced using the technique described in patent document 2 is the same as the content of the heavy rare earth element RH in the sintered rare earth magnet 1 according to the first and second embodiments, the magnetic properties of the rare earth magnet produced using the technique described in patent document 2 are lower than the magnetic properties of the sintered rare earth magnet 1 according to the first and second embodiments. In the sintered rare-earth magnet 1 according to the first embodiment, the first main phase 11 and the second main phase 12 satisfy the comparative expressions C1Nd>C2Nd and C1Pr <C2Pr. Alternativ ist die Anzahl der ersten Hauptphasen 11 größer als die Anzahl der zweiten Hauptphasen 12. Alternativ erfüllt die erste Hauptphase 11 die Vergleichsausdrücke CNd> SNd, CPr<SPr und CRH> SRH, and the second main phase 12 fulfills the comparison expressions CNd<SNd, CPr> SPr and CRH <SRH. Auf diese Weise ist es zudem möglich, einen gesinterten Seltenerdmagneten 1 zu erhalten, bei dem die magnetischen Eigenschaften und die Magnetisierung verbessert werden, während die Verwendung von Nd und dem schweren Seltenerdelement RH reduziert wird. Furthermore, since the main phase 10 contains the heavy rare-earth element RH and the subphase 22 mainly contains the element M, a rare-earth sintered magnet 1 is obtained whose coercivity is significantly improved compared to the prior art. Moreover, as will be shown in examples described later, the sintered rare-earth magnet 1 can be obtained with a better coercivity-temperature coefficient than in the prior art. For this reason, even when a thermal load is applied to the sintered rare-earth magnet 1, the coercivity is greater than in the prior art, and the decrease in coercivity with increasing temperature is also more moderate than in the prior art.This means that, since the coercive force is greatly improved compared to the conventional sintered rare earth magnet, the magnetic properties under thermal stress of the sintered rare earth magnet 1 are also better than those of the conventional sintered rare earth magnet. Second embodiment. In the second embodiment, a case is described in which La and Sm are selected as the rare earth element R in the sintered rare earth magnet 1 according to the first embodiment. Fig. 2 is a diagram schematically illustrating an exemplary sintered structure of a sintered rare-earth magnet according to the second embodiment. Components identical to those of the first embodiment are designated with the same reference numerals, and no further description is provided. The sintered rare-earth magnet 1 according to the second embodiment comprises the main phase 10 and the sub-phase 20. The main phase 10 comprises the first main phase 11 and the second main phase 12 as described in the first embodiment. The sub-phase 20 comprises the first sub-phase 21 and the second sub-phase 22 as described in the first embodiment. In a case where La and Sm are selected as the rare-earth element R, the effect of improving magnetic properties and achieving excellent magnetization compared to the prior art is further enhanced while simultaneously reducing the use of Nd and the heavy rare-earth element RH. In this example, the main phase 10 has the compositional formula (Nd, Pr, RH, La, Sm)₂Fe₁₄B.The reason why the rare-earth element R of the sintered rare-earth magnet 1, which has a tetragonal R₂Fe₁₄B crystal structure, contains rare-earth elements such as La and Sm, is that the calculation of the magnetic interaction energy using a molecular orbital method shows that a composition to which La and Sm are added can produce a sintered rare-earth magnet 1 suitable for practical use, since a deterioration of the magnetic properties associated with a temperature increase can be significantly prevented. Furthermore, by selectively segregating La and Sm even at the grain boundary, which is an example of the subphase 20, it is possible to distribute Nd and Pr relatively diffusely in the main phase 10, leading to improved magnetocrystalline anisotropy of the main phase 10.As a result, a core-shell structure is formed in which a section with high magnetic anisotropy and a section with low magnetic anisotropy are present in the main phase 10, and a state is formed in which the sintered rare-earth magnet 1, in which the first main phase 11, which CNd>CPr, satisfies, and the second main phase 12, which CNd <CPr erfüllt, gemischt bereitgestellt werden, und die Konzentration des schweren Seltenerdelements RH in dem Kernabschnitt 11c der ersten Hauptphase 11 höher ist als die Konzentration des schweren Seltenerdelements RH in dem Kernabschnitt 12c der zweiten Hauptphase 12, problemlos gebildet wird. It should be noted that adding too much La and Sm leads to a decrease in the amount of Nd and Pr, which are elements with a high magnetic anisotropy constant and high magnetic saturation polarization, resulting in a deterioration of the magnetic properties. Therefore, preferably (A+B)>(C+D) is satisfied, where A, B, C, and D are the composition ratios of Nd, Pr, La, and Sm, respectively. Since the sintered rare-earth magnet 1, according to the second embodiment, satisfies R=La, Sm, the subphase 20 comprises the first subphase 21, which is crystalline and consists mainly of an oxide phase represented as (Nd, Pr, RH, La, Sm)-O, containing the element M as a minor component, and the second subphase 22, which is crystalline and consists mainly of an oxide phase represented as (Nd, Pr, RH, La)-O, containing the element M as a minor component. Thus, the concentration of Sm in the first subphase 21 is higher than in the second subphase 22. That is, in the subphase 20 of the sintered rare-earth magnet 1, the first subphase 21 forms an Sm enrichment section with a higher concentration of Sm than the second subphase 22.This not only prevents a deterioration of the magnetic properties at room temperature, but also a deterioration of the magnetic properties when the temperature increases. Furthermore, in the first subphase 21, a high-concentration section (41), i.e., a section with a high concentration of Sm, and a low-concentration section (42), i.e., a section with a low concentration of Sm, may be present. In this case, element M can enter the low-concentration section 42, i.e., a section where the concentration of Sm in the first subphase 21 is lower than in the surrounding area. In this case, the concentration of element M in the low-concentration section 42 is higher than the concentration of element M in the high-concentration section 41. As described in the first embodiment, the concentration of element M in the second subphase 22 is higher than in the first subphase 21. In this way, Sm and element M are segregated into different subphases 20. Because Sm is present in a higher concentration in the first subphase 21, Nd is distributed relatively diffusely in the main phase 10, resulting in improved magnetocrystalline anisotropy of the main phase 10. Furthermore, Sm is also present in the crystal grains of the main phase 10 and thus contributes to improving the residual magnetic flux density, as it is coupled in the same magnetization direction as the ferromagnetic Fe. The element M, present in high concentration in the second subphase 22, forms a non-magnetic phase that magnetically separates the main phases 10 from each other, further improving the magnetic properties.Since Sm and the element M are present in high concentration in the various subphases 20, both the residual magnetic flux density and the coercive force can be improved. Here, "the Sm concentration is higher in the first sub-phase 21 than in the second sub-phase 22" means that the detection intensity of Sm according to map analysis using EPMA is on average higher in the first sub-phase 21 than in the second sub-phase 22. Specifically, this means that the intensity of Sm detected by EPMA in the first sub-phase 21 is higher than the average of the Sm intensities detected by EPMA, and that the intensity of Sm detected by EPMA in the second sub-phase 22 is lower than the average of the Sm intensities detected by EPMA. Crystalline subphase 20 is a general term encompassing crystalline first subphase 21 and crystalline second subphase 22 and lies between main phases 10. Crystalline first subphase 21 is represented by (Nd, Pr, RH, La, Sm)-O, containing the element M as a minor component, and crystalline second subphase 22 is represented by (Nd, Pr, RH, La)-O, containing the element M as a minor component. Here, (Nd, Pr, RH, La, Sm) means that some of the Nd and Pr are replaced by the heavy rare-earth elements RH, La, and Sm. It should be noted that the elements of the main components are given in parentheses; therefore, first subphase 21 and second subphase 22 may contain a small amount of another component in addition to those given in parentheses.In one example, the second subphase 22, represented by (Nd, Pr, RH, La)-O, containing the element M as a minor component, contains an extremely small amount of Sm. In the sintered rare-earth magnet 1 according to the second embodiment, there is a concentration difference of La and Sm between the main phase 10 and the subphase 20, and La and Sm are more segregated in the subphase 20 than in the main phase 10. That is, the sum of the concentrations of La in the first subphase 21 and the second subphase 22 is equal to or greater than the concentration of La in the main phase 10, and the sum of the concentrations of Sm in the first subphase 21 and the second subphase 22 is equal to or greater than the concentration of Sm in the main phase 10. In particular, the concentrations of La and Sm in the subphase 20 are equal to or greater than the concentrations of La and Sm in the main phase 10. Here, the concentration of La in the main phase 10 is the sum of the concentration of La in the first main phase 11 and the concentration of La in the second main phase 12.This means that the sum of the La concentrations in the first subphase 21 and the second subphase 22 is higher than the sum of the La concentrations in the first main phase 11 and the second main phase 12. The Sm concentration in main phase 10 is the sum of the Sm concentration in the first main phase 11 and the Sm concentration in the second main phase 12. That is, the sum of the Sm concentrations in the first subphase 21 and the second subphase 22 is higher than the sum of the Sm concentrations in the first main phase 11 and the second main phase 12. If X represents the concentration of La in the main phase 10, X1 represents the concentration of La in the first subphase 21, X2 represents the concentration of La in the second subphase 22, Y represents the concentration of Sm in the main phase 10, Y1 represents the concentration of Sm in the first subphase 21 and Y2 represents the concentration of Sm in the second subphase 22, then the relationship of the following formula (1) is satisfied. Furthermore, from the point of view of improving the magnetic properties, the relationships of the following formulas (2) and (3) are satisfied with respect to the concentrations of Nd and Pr contained in the main phase 10. In the preceding description, the concentration of La in main phase 10 is the sum of the concentrations of La in the first main phase 11 and the second main phase 12, and the concentration of Sm in main phase 10 is the sum of the concentrations of Sm in the first main phase 11 and the second main phase 12. This shows that both La and Sm are more segregated in subphase 20 than in main phase 10. However, upon local consideration, it is possible that the sum of the concentrations of La and Sm in the first main phase 11 and the second main phase 12, and the sum of the concentrations of La and Sm in the first subphase 21 and the second subphase 22, respectively, do not satisfy the preceding relationship.In particular, the concentration of La in main phase 10 represents the average of the concentrations of La in the first main phase 11 and the second main phase 12, and the concentration of Sm in main phase 10 represents the average of the concentrations of Sm in the first main phase 11 and the second main phase 12. In this case, the concentration of La in subphase 20, i.e., the sum of the concentrations of La in the first subphase 21 and the second subphase 22, represents the average of the concentrations of La in the first subphase 21 and the second subphase 22, and the concentration of Sm in subphase 20, i.e., the sum of the concentrations of Sm in the first subphase 21 and the second subphase 22, represents the average of the concentrations of Sm in the first subphase 21 and the second subphase 22. La is present in high concentrations at the grain boundary during the manufacturing process, particularly during heat treatment, while Nd and Pr are relatively diffusely distributed in the main phase 10. Consequently, in the sintered rare-earth magnet 1 according to the second embodiment, Nd and Pr are not consumed at the grain boundary in the main phase 10, resulting in improved magnetocrystalline anisotropy. Sm is also present in higher concentrations in the subphase 20, particularly in the first subphase 21, than in the main phase 10, with Nd being relatively diffusely distributed in the main phase 10, similar to La, resulting in improved magnetocrystalline anisotropy. Since, as described above, subphase 20 contains the heavy rare earth element RH, the first subphase 21 and the second subphase 22 also contain the heavy rare earth element RH. However, in subphase 20, the concentration of the heavy rare earth element RH is higher in the first subphase 21 than in the second subphase 22. Furthermore, the first subphase 21 contains a high-concentration section 41, where the concentration of Sm is higher than in the surrounding area, and a low-concentration section 42, where the concentration of Sm is lower than in the high-concentration section 41. In subphase 20, which exhibits this property, the distribution of the heavy rare earth element RH differs between the first subphase 21 and the second subphase 22.In the second subphase 22, which has a lower concentration of Sm than the first subphase 21, the heavy rare earth element RH is uniformly distributed throughout the second subphase 22. Conversely, in the first subphase 21, the heavy rare earth element RH is not uniformly distributed, but selectively distributed between the outer contour of the first subphase 21 and the high-concentration section 41, i.e., in the inner perimeter region of the outer contour of the first subphase 21. The inner perimeter region of the outer contour of the first subphase 21 corresponds to the low-concentration region 42. Specifically, the low-concentration region 42 is such that it selectively surrounds the outer contour of the high-concentration region 41, where the concentration of Sm in the first subphase 21 is high, and the heavy rare earth element RH is present in the low-concentration region 42.It follows that the first subphase 21 has the high-concentration section 41, in which Sm is concentrated, and a section containing a heavy rare-earth element, i.e., the low-concentration section 42, in which the heavy rare-earth element RH selectively surrounds the outer contour of the high-concentration section 41. The outer contour of the first subphase 21 is a boundary section between the first subphase 21 and the main phase 10. In this way, the first subphase 21 and the second subphase 22, containing the heavy rare-earth element RH, are located between the main phase 10 and the main phase 10. Therefore, it can be assumed that the heavy rare-earth element RH is deposited in a portion of the surface of the main phase 10 that is in contact with the first subphase 21 and the second subphase 22 containing the heavy rare-earth element RH. That is, similar to the first embodiment, it is also possible in the second embodiment to prevent a decrease in the residual magnetic flux density and simultaneously improve the coercive force of the sintered rare-earth magnet 1. Next, the atomic positions of La and Sm in the tetragonal R₂Fe₁₄B crystal structure are described. Figure 3 is a diagram illustrating atomic positions in a tetragonal Nd₂Fe₁₄B crystal structure. It should be noted that the crystal structure shown in Figure 3 is described in an example in Figure 1 of the reference document 1 listed below. The substitution sites are determined based on the numerical value of the stabilization energy associated with the substitution, calculated using band calculations and molecular field approximations based on the Heisenberg model. (Reference document 1): JF Herbst et al., “Relationships between crystal structure and magnetic properties in Nd2Fe14B”, PHYSICAL REVIEW B. 1984, Vol. 29, No. 7, pp. 4176-4178. First, a method for calculating the stabilization energy of La is described. The stabilization energy of La can be calculated as the energy difference between (Nd₇La₁)Fe₅6B₄ + Nd and Nd₈(Fe₅5La₁)B₄ + Fe using Nd₈Fe₅6B₄ crystal cells. The smaller the energy value, the more stable the substitution of the atom at that position. This means that La is likely to be substituted at an atomic site with the lowest energy among the atomic sites. This calculation assumes that the substitution of the original atom by La does not change the lattice constant in the tetragonal R₂Fe₁₄B crystal structure due to the different atomic radii. Table 1 shows the stabilization energy of La at each substitution site at different ambient temperatures. [Table 1] (Table 1) (Table 1) Nd(f)-136,372-84,943-48,524-40,132-38,132-35,451 Nd(g)-132,613-82,740-47,442-38,211-36,358-34,753 Fe(k1)-135,939-80,596-41,428-32,390-30,237-17,095 Fe(k2)-127,480-75,638-38,948-30,482-28,466-26,719 Fe(j1)-124,248-73,076-38,003-29,754-27,791-26,089 Fe(j2)-117.148-71.400-35.923-28.816-26.917-25.271 Fe(e)-130,814-77,593-39,926-31,235-29,164-27,371 Fe(c)-148,317-87,850-45,055-35,179-32,828-30,789 Unit: eV Table 1 shows that stable substitution sites for La are Nd(f) sites at temperatures of 1000 K and above, and Fe(c) sites at temperatures of 293 K and 500 K. As described later, the raw material of the sintered rare-earth magnet 1 according to the second embodiment is heated and melted at a temperature of 1000 K or above and then rapidly cooled. Therefore, it is assumed that the raw material of the sintered rare-earth magnet 1 is maintained at a temperature of 1000 K or above, i.e., 727 °C or above, and preferably at 1300 K, i.e., 1027 °C. In this case, it is assumed that La is substituted at Nd(f) or Nd(g) sites. It is assumed that La is preferentially substituted at energetically stable Nd(f) sites, but can also be substituted at Nd(g) sites which have a small energy difference between the substitution sites for La.For this reason, Nd(g) positions are also mentioned as candidates for La substitution positions. Furthermore, when the sintered rare-earth magnet 1 is produced using the manufacturing process described later, the temperature at the time of sintering is 1000 K or higher, but the Fe(c) sites described in Table 1 are repeatedly held in an energetically stable temperature zone during the primary, secondary, tertiary, quaternary, and cooling steps, which are described later. In other words, the La substitution at Nd sites of the main phase 10 is maintained in an unstable energy state.This means that in the raw material stage of the sintered rare-earth magnet 1, La is mainly substituted at Nd sites of the main phase 10; however, in the sintered rare-earth magnet 1 produced by the manufacturing process described later, by repeatedly and intentionally holding the sintered rare-earth magnet 1 in a temperature range in an unstable energy state with respect to the Nd sites of the main phase 10, a certain amount of La is selectively released from the Nd sites of the main phase 10, and as a result, La is segregated in the subphase 20. Consequently, the main phase 10 promotes the formation of the characteristic structure, namely the core-shell structure. Next, a method for calculating the stabilization energy in Sm is described. The stabilization energy of Sm can be calculated as the energy difference between (Nd₇Sm₁)Fe₅₆B₄+Nd and Nd₈(Fe₅₅SM₁)B₄+Fe. Similar to La, the lattice constant in the tetragonal R₂Fe₁₄B crystal structure does not change due to atomic substitution. Table 2 shows the stabilization energy of Sm at each substitution site at different ambient temperatures. [Table 2] (Table 2) (Table 2) Nd(f)-164,960-101,695-56,921-46,589-44,128-41,976 Nd(g)-168,180-103,583-57,865-47,315-44,803-42,626 Fe(k1)-136,797-81,098-41,679-32,583-17,350-16,343 Fe(k2)-127,769-75,808-38,482-29,603-28,528-25,696 Fe(j1)- 22,726-73,304-37,783-28,392-26,525-24,681 Fe(j2)-124,483-73,883-38,072-28,483-26,610-24,985 Fe(e)125.93772.52535.30126.63324.45022.782 Fe(c)-155,804-94,457-48,359-37,720-35,187-32,992 Unit: eV Table 2 shows that stable substitution sites for Sm at every temperature are Nd(g) sites, unlike for La. It is also assumed that Sm is preferentially substituted at energetically stable Nd(g) sites, but can also be substituted at Nd(f) sites, which have a small energy difference between the substitution sites for Sm. When the sintered rare-earth magnet 1 is produced using the fabrication process described later, the substitution at Nd(g) sites of the main phase 10 is energetically most stable. However, as described above, holding the magnet in a temperature range where the substitution of La at the Nd sites of the main phase 10 is unstable causes some Sm to be released along with La from the Nd sites of the main phase 10 and segregated in the subphase 20. Consequently, the concentrations of La and Sm differ between the main phase 10 and the subphase 20: the sum of the concentrations of La in the first subphase 21 and the second subphase 22 is equal to or greater than the concentration of La in the main phase 10, and the sum of the concentrations of Sm in the first subphase 21 and the second subphase 22 is equal to or greater than the concentration of Sm in the main phase 10.In particular, the average concentration of La in the first subphase 21 and the second subphase 22 is equal to or greater than the average concentration of La in the first main phase 11 and the second main phase 12, and the average concentration of Sm in the first subphase 21 and the second subphase 22 is equal to or greater than the average concentration of Sm in the first main phase 11 and the second main phase 12. Therefore, it can be said that La and Sm are segregated into subphase 20. Comparing La and Sm, La, when held in an unstable energy state within a temperature range, is much more likely to segregate into subphase 20 from an energetic perspective. In the case of the sintered rare-earth magnet 1, which was produced with nearly equal concentrations of La and Sm, La exhibits a higher segregation ratio to subphase 20 than Sm when comparing La and Sm in the sintered rare-earth magnet 1. Since the sintered rare-earth magnet 1 is repeatedly held within this temperature range, a concentration difference of Sm with a low segregation ratio arises in subphase 20, and the first subphase 21 and the second subphase 22 are formed. This promotes the formation of the core-shell structure in the main phase 10. For the purposes of this article, Nd is described representatively, as shown in Fig. 3, but Nd and Pr are produced as a mixture, as represented by didymium (Di), and therefore the energy levels of Nd and Pr are assumed to be close to each other. The same applies, therefore, to a case where Nd is replaced by Pr. Since both types of Nd and Pr are present in the sintered rare-earth magnet 1, the main phase 10 can be formed with two types of core-shell structures. As described above, the sintered rare-earth magnet 1 according to the second embodiment comprises: the main phase 10, which satisfies the general formula (Nd, Pr, RH, R)-Fe-BM, wherein RH is one or more heavy rare-earth elements selected from the group consisting of Dy, Tb, Gd, and Ho, R is one or more rare-earth elements selected excluding Nd, Pr, and RH, and M is one or more elements selected from a group consisting of Ga, Al, Cu, and Co, wherein the main phase contains crystal grains based on an Nd₂Fe₁₄B crystal structure; and the subphase 20, which is located between the main phase 10 and the main phase 10. The main phase 10 includes the core sections 11c and 12c and the shell sections 11s and 12s, which cover the core sections 11c and 12c.If R = La and Sm, subphase 20 includes the first subphase 21, which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, RH, La, Sm)-O, containing the element M as a minor component, and the second subphase 22, which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, RH, La)-O, containing the element M as a minor component. The concentration of Sm is higher in the first subphase 21 than in the second subphase 22, and the concentration of the element M is higher in the second subphase 22 than in the first subphase 21. That is, in the sintered rare-earth magnet 1, there are two types of main phases 10 and two types of subphases 20, and there is a difference in the concentration of Sm and the concentration of the element M in subphase 20. The first subphase 21 includes the section with high Concentration 41, i.e.An Sm enrichment section, in which Sm is selectively distributed, and Sm, which is present in higher concentrations in the first subphase 21, cause Nd to be relatively diffusely distributed in the main phase 10, leading to improved magnetocrystalline anisotropy of the main phase 10. Furthermore, Sm is also present in the crystal grains of the main phase 10 and thus contributes to improving the residual magnetic flux density, as it is coupled in the same magnetization direction as the ferromagnetic Fe. The element M, which is present in high concentrations in the second subphase 22, forms a non-magnetic phase that magnetically separates the main phases 10 from each other, contributing to improved magnetic properties. Since Sm and the element M are present in high concentrations in the various subphases 20, both the residual magnetic flux density and the coercive force can be improved.As a result, it is possible to provide the sintered rare earth magnet 1 with excellent magnetic properties, such as temperature properties of the magnetic properties, compared to the state of the art. By setting R to La and Sm, the main phase 10 is also in a state in which the first main phase 11, which satisfies C(Nd,RH)>CPr, and the second main phase 12, which satisfies C(Nd,RH) <CPr erfüllt, gemischt bereitgestellt werden. Mit anderen Worten, in dem gesinterten Seltenerdmagneten 1 ist die Hauptphase 10 mit den beiden Arten der ersten Hauptphase 11 und der zweiten Hauptphase 12 vorhanden, und insbesondere in Bezug auf die Kernabschnitte 11c und 12c der beiden Arten von Hauptphasen 10 wird problemlos die Hauptphase 10 mit den beiden Arten von Kern-Schale-Strukturen erzeugt, in denen in der ersten Hauptphase 11 die Konzentration von Nd höher ist als die Konzentration von Pr und umgekehrt in der zweiten Hauptphase 12 die Konzentration von Pr höher ist als die Konzentration von Nd, und die Konzentration des schweren Seltenerdelements RH in der ersten Hauptphase 11 höher ist als die Konzentration des schweren Seltenerdelements RH in der zweiten Hauptphase 12.As a result, the sintered rare earth magnet 1 according to the second embodiment can further enhance the effect of improving the magnetic properties and exhibit excellent magnetization compared to the prior art, while reducing the use of Nd and the heavy rare earth element RH compared to the prior art. Third embodiment. In the third embodiment, a method for producing the sintered rare-earth magnet 1 described in the first and second embodiments is described separately as a method for producing an alloy for a sintered rare-earth magnet, which is the raw material of the sintered rare-earth magnet 1, and as a method for producing the sintered rare-earth magnet 1 using the alloy for a sintered rare-earth magnet. Fig. 4 is a flowchart illustrating an exemplary sequence of a process for producing an alloy for a sintered rare-earth magnet according to the third embodiment. As shown in Fig. 4, the process for producing an alloy for a sintered rare-earth magnet, which is the raw material of the sintered rare-earth magnet 1, includes a melting step (step S1) of heating and melting the raw material of the alloy for a sintered rare-earth magnet, which contains an element forming the sintered rare-earth magnet 1, at a temperature of 1000 K or higher; a primary cooling step (step S2) of cooling the molten raw material on a rotating body to obtain a solidified alloy; and a secondary cooling step (step S3) of further cooling the solidified alloy in a container.In this way, an alloy for a sintered rare-earth magnet can be produced. The individual steps are described below. In melting step S1, the raw material of the alloy for a sintered rare-earth magnet is heated and melted at a temperature of 1000 K or higher in a crucible in an atmosphere containing an inert gas such as argon (Ar) or in a vacuum. Consequently, the alloy for a sintered rare-earth magnet melts to form a molten alloy. The raw material can be Nd, Pr, RH, R, Fe, B, and M. In the production of the sintered rare-earth magnet 1 of the second embodiment, R is La and Sm. Examples of RH include one or more elements of Dy and Tb. Examples of M include one or more elements selected from the group consisting of Ga, Al, Cu, and Co. FeB can be used as the raw material instead of B. Next, in the primary cooling step S2, the molten alloy produced in the melting step is fed into an intermediate container and then onto a single roller, which is a rotating body. Consequently, the molten alloy is rapidly cooled on the single roller rotating in a specific direction, and a solidified alloy, thinner than the raw ingot alloy, is produced from the molten alloy on the single roller. In this example, the single roller is used as a rotating body; however, the present disclosure is not limited to this, and twin rollers, a rotating disk, a rotating cylindrical shape, or the like can also be used for contact with the molten alloy and for the rapid cooling of the molten alloy.From the perspective of efficiently obtaining the thin solidified alloy, the cooling rate in the primary cooling step is preferably in the range of 10 °C / s to 107 °C / s, and even more preferably in the range of 103 °C / s to 104 °C / s. The thickness of the solidified alloy is in the range of 0.03 mm to 10 mm. The molten alloy begins to solidify at the point of contact with the single roller, and crystals grow in a columnar or needle-like pattern in the direction of thickness from the contact surface with the single roller. Subsequently, in the secondary cooling step S3, the thin solidified alloy produced in the primary cooling step is placed in a tray container and cooled. Upon being placed in the tray container, the thin solidified alloy is broken down into scale-like (or flake-like) pieces of alloy for a sintered rare-earth magnet and cooled. Depending on the cooling rate, ribbon-like pieces of alloy for a sintered rare-earth magnet can be obtained, so the present disclosure is not limited to the case of scale-like pieces. To obtain the alloy for a sintered rare-earth magnet with a structure exhibiting favorable temperature characteristics of the magnetic properties, the cooling rate in the secondary cooling step is preferably in the range of 10⁻²°C / s to 10⁵°C / s, and even more preferably in the range of 10⁻¹°C / s to 10²°C / s. The alloy obtained by these steps for a sintered rare-earth magnet has a size in the direction of the minor axis of 3 µm to 10 µm and a size in the direction of the major axis of 10 µm to 300 µm. In the second embodiment, the alloy for a sintered rare-earth magnet has a fine crystal structure containing a (Nd, Pr, RH, La, Sm)-Fe-B crystal phase, with the element M present as a minor component, and the crystalline subphase 20 of an oxide represented by (Nd, Pr, RH, La, Sm)-O, with the element M present as a minor component. In the following, the (Nd, Pr, RH, La, Sm)-Fe-B crystal phase, in which the element M is contained as a minor component, is also referred to as the (Nd, Pr, RH, La, Sm)-Fe-B crystal phase, and the crystalline subphase 20 of the oxide represented by (Nd, Pr, RH, La, Sm)-O, containing the element M as a minor component, is also referred to as the (Nd, Pr, RH, La, Sm)-O phase.The (Nd, Pr, RH, La, Sm)-O phase is a non-magnetic phase consisting of an oxide with a relatively high concentration of rare-earth metals. The thickness of the (Nd, Pr, RH, La, Sm)-O phase is 10 µm or less, corresponding to the grain boundary width. After rapid cooling, the alloy for a sintered rare-earth magnet produced using the above manufacturing process has a more refined structure compared to the alloy for a sintered rare-earth magnet obtained by casting. Next, a method for producing the sintered rare-earth magnet 1 using the alloy for a sintered rare-earth magnet is described. Fig. 5 is a flowchart illustrating an exemplary sequence of a method for producing a sintered rare-earth magnet according to the third embodiment. As shown in Fig.Figure 5 shows that the process for producing the sintered rare-earth magnet 1 comprises a pulverization step (step S21) for pulverizing the alloy for a sintered rare-earth magnet with the (Nd, Pr, RH, La, Sm)-Fe-B crystal phase and the (Nd, Pr, RH, La, Sm)-O phase, a forming step (step S22) for producing a shaped body by forming powder of the pulverized alloy for a sintered rare-earth magnet, a sintering step (step S23) for obtaining a sintered body by sintering the shaped body at a sintering temperature which is a predetermined temperature, an aging step (step S24) for aging the sintered body to improve the magnetic properties such as the coercivity of the rare-earth sintered magnet 1, and a cooling step (step S25) for cooling the sintered body subjected to the aging process. The individual steps are described below. In the pulverization step S21, the alloy for a sintered rare-earth magnet, comprising the (Nd, Pr, RH, La, Sm)-Fe-B crystal phase and the (Nd, Pr, RH, La, Sm)-O phase, which was produced according to the process step in Fig. 4 for an alloy for a sintered rare-earth magnet, is pulverized into alloy powder for a sintered rare-earth magnet with a grain size of 200 µm or less, preferably 0.5 µm to 100 µm and particularly preferably about 1 µm to 10 µm, taking into account the magnetizability. The pulverization of the alloy for a sintered rare-earth magnet is carried out, for example, using an agate mortar, a stamp mill, a jaw crusher, or a jet mill. In particular, to reduce the grain size of the powder, it is advantageous to pulverize the alloy for a sintered rare-earth magnet in an atmosphere containing an inert gas.By pulverizing the alloy for a sintered rare-earth magnet in an atmosphere containing an inert gas, oxygen can be prevented from mixing into the powder. Provided the pulverization atmosphere does not impair the magnetic properties of the magnet, the alloy for a sintered rare-earth magnet can be pulverized in air. In a case where the sintered rare-earth magnet 1 of the first embodiment is produced, La and Sm of the alloy for a sintered rare-earth magnet used in the production of the sintered rare-earth magnet 1 of the second embodiment can be a rare-earth element R other than Nd, Pr, and the heavy rare-earth element RH. That is, the alloy for a sintered rare-earth magnet with the (Nd, Pr, RH, R)-Fe-B crystalline phase and the (Nd, Pr, RH, R)-O phase is pulverized. In forming step S22, the alloy powder for a sintered rare-earth magnet is pressed into a mold under a magnetic field to produce a shaped body. In this example, the applied magnetic field can be 2T. It should be noted that forming cannot be carried out in a magnetic field, i.e., without the application of a magnetic field. In sintering step S23, the molded body produced by compression molding is held at a sintering temperature in the range of 950 °C to 1300 °C, preferably 1000 °C or higher but lower than 1150 °C, for between 0.1 and 10 hours, preferably 1.0 and 6.0 hours, thereby obtaining a sintered body. Sintering preferably takes place in an atmosphere containing an inert gas or in a vacuum to prevent oxidation. Sintering can be carried out under the application of a magnetic field. In the case of Fig. 5, the aging step S24 comprises a primary aging step S24-1, a secondary aging step S24-2, a tertiary aging step S24-3, and a quaternary aging step S24-4. The aging preferably takes place in an atmosphere containing an inert gas or in a vacuum to prevent oxidation. In the primary aging step in step S24-1, the obtained sintered body is held at a primary aging temperature lower than the sintering temperature, in particular a temperature of 700 °C or higher but lower than 950 °C, for 0.1 hours to 10 hours, preferably 0.5 hours to 5 hours. In the secondary aging step in step S24-2, the sintered body held in the primary aging step is held after the primary aging step for 0.1 hours to 10 hours, preferably 1.0 hours to 7 hours, at a secondary aging temperature that is lower than the primary aging temperature, in particular a temperature of 450 °C or higher, but lower than 700 °C. In the tertiary aging step in step S24-3, the sintered body held in the secondary aging step is reheated to the primary aging temperature after the secondary aging step, in particular a temperature of 700 °C or higher, but lower than 950 °C, and held at the primary aging temperature for 0.1 hours to 10 hours, preferably 0.5 hours to 5 hours. In the quaternary aging step in step S24-4, the sintered body held in the tertiary aging step is held again for 0.1 hours to 10 hours, preferably 1.0 hours to 7 hours, at the secondary aging temperature, in particular a temperature of 450 °C or higher, but lower than 700 °C, for 0.1 hours to 10 hours, preferably 1.0 hours to 7 hours. Finally, in the cooling step S25, the sintered body held during the quaternary aging step is kept at a temperature lower than the secondary aging temperature, in particular a temperature of 200 °C or higher but lower than 450 °C, for 0.1 to 5 hours. Afterwards, the sintered rare-earth magnet 1 is finished by cooling to room temperature. Cooling is also preferably carried out in an atmosphere containing an inert gas or in a vacuum to prevent oxidation. As described above, the sintered body is repeatedly kept in an unstable energy state within a temperature range by controlling temperature and time in the sintering, aging, and cooling steps. As a result, the first main phase 11, consisting of CNd>CPr, and the second main phase 12, consisting of CNd <CPr besteht, gemischt, und die Konzentration des schweren Seltenerdelements RH in der ersten Hauptphase 11 kann höher sein als die Konzentration des schweren Seltenerdelements RH in der zweiten Hauptphase 12. Mit anderen Worten weist der gesinterte Seltenerdmagnet 1 zwei Arten von Hauptphasen 10 auf, d. h.the first main phase 11 and the second main phase 12, and in particular with respect to the core sections 11c and 12c of the two types of main phases 10, the production of the sintered rare-earth magnet 1 is characterized in that in the first main phase 11 the sum of the concentration of Nd and the concentration of the heavy rare-earth element RH is higher than the concentration of Pr and conversely in the second main phase 12 the concentration of Pr is higher than the sum of the concentration of Nd and the concentration of the heavy rare-earth element RH. Furthermore, it is possible to produce the sintered rare-earth magnet 1, which includes the first subphase 21, which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, RH, La, Sm)-O, containing the element M as a minor component, and the second subphase 22, which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, RH, La)-O, containing the element M as a minor component, in addition to the first main phase 11 and the second main phase 12 according to the first embodiment, in which the concentration of Sm in the first subphase 21 is higher than in the second subphase 22 and the concentration of the element M in the second subphase 22 is higher than in the first subphase 21.This means that in the aging and cooling steps, the crystalline first subphase 21, consisting mainly of an oxide phase represented by (Nd, Pr, RH, La, Sm)-O, and the crystalline second subphase 22, also consisting mainly of an oxide phase represented by (Nd, Pr, RH, La)-O, are generated from the (Nd, Pr, RH, La, Sm)-O phase according to the concentration of element M. It should be noted that the second subphase 22 may contain a small amount of Sm. Since the concentration of Sm in the first subphase 21 is higher than in the second subphase 22, it can be said that the first subphase 21 forms an Sm enrichment section in subphase 20. Furthermore, in the first subphase 21 there may be a case in which the high concentration section 41 has a high concentration of Sm and the low concentration section 42 has a low concentration of Sm.Therefore, in this case, it can be said that the high concentration section 41 of the first subphase 21 forms an Sm enrichment section. Therefore, it is possible to provide the sintered rare earth magnet 1 with excellent magnetizability and excellent magnetic properties compared to the prior art, while simultaneously reducing the use of Nd and the heavy rare earth element RH. In the third embodiment, the alloy for a sintered rare-earth magnet, containing the (Nd, Pr, RH, La, Sm)-Fe-B crystal phase and the (Nd, Pr, RH, La, Sm)-O phase, is pulverized into alloy powder for a sintered rare-earth magnet, which is then shaped. The shaped body is subsequently sintered to form a sintered body, and the sintered body is aged to form the sintered rare-earth magnet 1. In this way, the sintered rare-earth magnet 1 with the structure described in the second embodiment can be produced. Furthermore, since the alloy for a sintered rare-earth magnet is produced after the heavy rare-earth element RH has been brought to a desired concentration, and the sintered rare-earth magnet 1 is produced using the alloy for a sintered rare-earth magnet, the heavy rare-earth element RH readily enters the main phase 10. In the third embodiment, the temperature and time are controlled during the sintering, aging, and cooling steps. In one example, during the first aging step, the resulting sintered body is held at the primary aging temperature, which is lower than the sintering temperature, particularly 700 °C or higher but lower than 950 °C, for 0.1 to 10 hours, preferably 0.5 to 5 hours. During the second aging step, the sintered body is held at the secondary aging temperature, which is lower than the primary aging temperature, particularly 450 °C or higher but lower than 700 °C, for 0.1 to 10 hours, preferably 1.0 to 7 hours.In the tertiary aging step, the sintered body is reheated to the primary aging temperature, in particular to a temperature of 700 °C or higher, but lower than 950 °C, and held at this temperature for 0.1 to 10 hours, preferably 0.5 to 5 hours. In the quaternary aging step, the sintered body is again held at the secondary aging temperature, in particular a temperature of 450 °C or higher, but lower than 700 °C, for 0.1 to 10 hours, preferably 1.0 to 7 hours. In this way, the temperature and time are controlled such that the primary and secondary aging steps are carried out in two separate cycles. This results in a state in which the sintered body is repeatedly held in an unstable energy state within a temperature range.As a result, the first main phase 11, consisting of CNd>CPr, and the second main phase 12, consisting of CNd <CPr besteht, gemischt, und die Konzentration des schweren Seltenerdelements RH in der ersten Hauptphase 11 kann höher sein als die Konzentration des schweren Seltenerdelements RH in der zweiten Hauptphase 12. Mit anderen Worten weist der gesinterte Seltenerdmagnet 1 zwei Arten von Hauptphasen 10 auf, d. h. die erste Hauptphase 11 und die zweite Hauptphase 12, und insbesondere in Bezug auf die Kernabschnitte 11c und 12c der beiden Arten von Hauptphasen 10 kann selektiv das schwere Seltenerdelement 1 hergestellt werden, bei dem in der ersten Hauptphase 11 die Summe der Konzentration von Nd und der Konzentration des schweren Seltenerdelements RH höher ist als die Konzentration von Pr und umgekehrt in der zweiten Hauptphase 12 die Konzentration von Pr höher ist als die Summe der Konzentration von Nd und der Konzentration des schweren Seltenerdelements RH. The preceding manufacturing steps make it possible to selectively produce the sintered rare-earth magnet 1 with a characteristic structure comprising the first subphase 21, which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, RH, La, Sm)-O, containing the element M as a minor component, and the second subphase 22, which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, RH, La)-O, containing the element M as a minor component, wherein the concentration of Sm in the first subphase 21 is higher than in the second subphase 22 and the concentration of the element M in the second subphase 22 is higher than in the first subphase 21.Furthermore, since the concentration of Sm in the first subphase 21 is higher than in the second subphase 22 of subphase 20, it is possible to produce a sintered rare-earth magnet 1 that has a characteristic structure with an Sm enrichment section, i.e., the first subphase 21 where Sm is concentrated. Alternatively, if the high-concentration section 41 with a high concentration of Sm and the low-concentration section 42 with a low concentration of Sm are present in the first subphase 21, the sintered rare-earth magnet 1 can be produced with a characteristic structure that includes the high-concentration section 41 as the Sm enrichment section. In comparison with the RTB-based sintered magnet described in Patent Document 1, the RTB-based sintered magnet described in Patent Document 1 has one or more rare-earth elements, which essentially comprise the heavy rare-earth element RH, and has a type of main phase grain consisting of a core section and a shell section. That is, in Patent Document 1, the heavy rare-earth element RH is contained in all main phase grains. On the other hand, in the main phase 10 of the sintered rare-earth magnet 1 according to the first embodiment, the first main phase 11, in which the heavy rare-earth element RH is contained in the core section 11c, and the second main phase 12, in which the heavy rare-earth element RH is hardly contained in the core section 12c, are mixed. That is, the heavy rare-earth element RH is selectively arranged in the first main phase 11, which is one of the two types of main phases 10.As described above, the sintered rare-earth magnet 1 according to the first embodiment, in which only the first main phase 11, which is one of the two types of main phases 10, needs to contain the heavy rare-earth element RH, can reduce the amount of the heavy rare-earth element RH used compared to the RTB-based sintered magnet described in patent document 1, in which the heavy rare-earth element RH must be present in all main phases of only one type. Furthermore, since the ratio of the volume of the sub-phase 20 to the total volume of the sintered rare-earth magnet 1 is extremely small, the amount of the heavy rare-earth element RH can be reduced compared to the method of patent document 1, even if the heavy rare-earth element RH is diffusely present in the sub-phase 20. Furthermore, in order to achieve magnetic properties for the rare-earth magnet produced using the technique described in Patent Document 2 that correspond to those of the sintered rare-earth magnet 1 according to the first embodiment, as described below, a large quantity of the heavy rare-earth element RH must be added to the rare-earth magnet produced using the technique described in Patent Document 2. That is, the sintered rare-earth magnet 1 according to the first embodiment can reduce the quantity of the heavy rare-earth element RH compared to the technique described in Patent Document 2 if one attempts to obtain the same magnetic properties. The method described in Patent Document 2 involves hot forming, whereas the method for producing the sintered rare-earth magnet 1 according to the third embodiment does not involve hot forming.Therefore, a reduction in the particle size of the main phase 10 is prevented, and the deterioration of the residual magnetic flux density and magnetization can be reduced compared to the rare-earth magnet produced using the technique described in patent document 2. As a result, it is possible to obtain the sintered rare earth magnet 1, which is able to improve the magnetic properties compared to the prior art, while reducing the use of the heavy rare earth element RH compared to the prior art. Fourth embodiment. In the fourth embodiment, a rotor is described that uses the sintered rare-earth magnet 1 according to the first or second embodiment and was manufactured using the manufacturing process according to the third embodiment. Fig. 6 is a cross-sectional view that schematically illustrates an exemplary configuration of a rotor equipped with a sintered rare-earth magnet according to the fourth embodiment. Fig. 6 shows a cross-section in a direction perpendicular to an axis of rotation RA of a rotor 100. The rotor 100 is rotatable about the axis of rotation RA. The rotor 100 comprises a rotor core 101 and the sintered rare-earth magnet 1, which is inserted into a magnet insert hole 102 provided in the rotor core 101 along the circumferential direction of the rotor 100. Fig. 6 illustrates an example in which the four magnet insert holes 102 are provided in the rotor core 101 and the four sintered rare-earth magnets 1 are inserted into the magnet insert holes 102; however, the number of magnet insert holes 102 and the number of sintered rare-earth magnets 1 can be changed according to the design of the rotor 100. The rotor core 101 is formed from a plurality of disk-shaped electromagnetic steel sheets stacked in the axial direction of the axis of rotation RA. The sintered rare-earth magnets 1 are manufactured using the manufacturing process described in the third embodiment. Each of the four sintered rare-earth magnets 1 is inserted into the corresponding magnet insert hole 102. The four sintered rare-earth magnets 1 are magnetized such that the magnetic poles of the sintered rare-earth magnets 1 differ between adjacent sintered rare-earth magnets 1 on the radially outer side of the rotor 100. The rotor 100 according to the fourth embodiment includes the sintered rare-earth magnet 1 according to the first or second embodiment, which improves magnetic properties at room temperature and prevents deterioration of magnetic properties associated with a temperature increase. As described above, the sintered rare-earth magnet 1 according to the first or second embodiment is a sintered rare-earth magnet 1 that is able to reduce the use of the heavy rare-earth element RH compared to the prior art and prevent deterioration of magnetic properties associated with a temperature increase, while maintaining a high residual magnetic flux density and coercivity, thus preventing deterioration of magnetic properties even in a high-temperature environment above 100 °C.This makes it possible to improve magnetic properties and magnetization while simultaneously using cost-effective rare-earth elements instead of Nd and heavy rare-earth elements (RH), which are expensive and pose a procurement risk due to their large distribution inequality. It also stabilizes the operation of the rotor 100 even at high temperatures exceeding 100 °C. Furthermore, since the sintered rare-earth magnet 1 according to the first or second embodiment exhibits excellent magnetizability compared to the prior art, magnetization is possible in an assembled state, with the sintered rare-earth magnet 1 mounted on the rotor 100, thus simplifying handling during the manufacturing process. Moreover, the magnetization process can be implemented with reduced voltage, contributing to energy savings. Fifth embodiment. The fifth embodiment describes a rotary machine equipped with the rotor 100 according to the fourth embodiment. Fig. 7 is a cross-sectional view that schematically illustrates an exemplary configuration of a rotary machine according to the fifth embodiment. Fig. 7 shows a cross-section in a direction perpendicular to an axis of rotation RA of the rotor 100. The rotary machine 120 includes the rotor 100 described in the fourth embodiment, which is rotatable about the axis of rotation RA, and an annular stator 130, which is provided coaxially with and opposite the rotor 100. The stator 130 is formed by stacking a plurality of electromagnetic steel laminations in the axial direction of the axis of rotation RA. Instead of the described configuration of the stator 130, another existing configuration can also be used. Teeth 131 are provided along the inner surface of the stator 130, projecting towards the side of the rotor 100. Windings 132 are provided on the teeth 131. The winding type of the windings 132 can be, in one example, a concentrated winding or a distributed winding.That is, the stator 130 has a ring-shaped structure opposite the rotor 100 and, on an inner surface on one side where the rotor 100 is located, has teeth 131 projecting towards the rotor 100 and windings 132 provided on the teeth 131. The number of magnetic poles of the rotor 100 in the rotating machine 120 should be at least two, i.e., the number of sintered rare-earth magnets 1 should be at least two. Although Fig. 7 shows an example of the rotor 100 of the internal magnet type, the rotor 100 can also be of the surface magnet type, in which the sintered rare-earth magnets 1 are attached to the outer circumference of the rotor with an adhesive. The rotary machine 120 according to the fifth embodiment incorporates the sintered rare-earth magnet 1 according to the first or second embodiment, which can improve magnetic properties at room temperature and prevent deterioration of magnetic properties associated with a temperature increase. As described above, the sintered rare-earth magnet 1 according to the first or second embodiment is a sintered rare-earth magnet 1 that is able to reduce the use of the heavy rare-earth element RH compared to the prior art and prevent deterioration of magnetic properties associated with a temperature increase, while maintaining a high residual magnetic flux density and coercivity, thus preventing deterioration of magnetic properties even in a high-temperature environment above 100 °C.Therefore, it is possible to improve magnetic properties and magnetization while using cost-effective rare earth elements instead of Nd and the heavy rare earth element RH, which are expensive and pose a procurement risk due to high distribution inequality, and to drive the rotor 100 stably and to stabilize the operation of the rotary machine 120 itself in a high temperature environment above 100 °C. [Examples] The sintered rare-earth magnet 1 according to the present disclosure is described in detail below with reference to examples and comparative examples. In Examples 1 to 8, the sintered rare-earth magnet 1 is produced using the method described in the third embodiment, employing samples of a plurality of alloys for a sintered rare-earth magnet that differ in composition, represented by a (Nd, Pr, Tb, La, Sm)-Fe-B crystalline phase, wherein the element M is present as a minor component, and represented by a (Nd, Pr, Tb, La, Sm)-O phase, wherein the element M is present as a minor component. In Examples 1 to 8, the sintered rare-earth magnet 1 is produced using the alloys for a sintered rare-earth magnet that differ in their content of Nd, Pr, Tb, La, and Sm.That is, in Examples 1 to 8, the sintered rare-earth magnet 1 is produced according to the method described in the third embodiment using alloys for a sintered rare-earth magnet, which include a (Nd, Pr, Tb, La, Sm)-Fe-B crystal phase, wherein the element M is present as a minor component, and a (Nd, Pr, Tb, La, Sm)-O phase, wherein the element M is present as a minor component. M is one or more elements selected from the group consisting of Ga, Al, Cu, and Co, with the case being considered here as an example where M is Co. In Comparative Examples 1 to 18, the sintered rare-earth magnet 1 is experimentally produced using R-Fe-BM-based samples of a variety of alloys for a sintered rare-earth magnet, which differ in their composition, by a general method for producing rare-earth magnets as disclosed in Patent Document 1 or Patent Document 2. The samples of the sintered rare-earth magnets 1 according to Comparative Examples 1 to 18 differ with respect to R. In comparative examples 1 to 9, the sintered rare-earth magnet 1 is produced from an alloy for a sintered rare-earth magnet in which R is Nd, or from an alloy for a sintered rare-earth magnet in which R comprises Nd and one or more elements selected from the group consisting of Pr, Tb, La, and Sm, and M comprises one or more elements selected from the group consisting of Ga, Al, Cu, and Co, using the manufacturing process disclosed in patent document 1. A case in which M is Co is used as an example. However, in comparative example 2, (Nd,Tb)-Fe-B does not contain the element M, and in comparative example 3, Nd-Fe-BM contains no rare-earth element R other than Nd. In Comparative Examples 10 to 18, the sintered rare-earth magnet 1 is produced from an alloy for a sintered rare-earth magnet in which R is Nd, or from an alloy for a sintered rare-earth magnet in which R comprises Nd and one or more elements selected from the group consisting of Pr, Tb, La, and Sm, and M comprises one or more elements selected from the group consisting of Ga, Al, Cu, and Co, using the manufacturing process disclosed in Patent Document 2. A case in which M is Co is used as an example. However, in Comparative Example 11, Nd-Fe-BM contains no rare-earth element R other than Nd, and in Comparative Example 12, Nd-Fe-B contains no rare-earth element R other than Nd and no element M. The manufacturing process disclosed in Patent Document 2 includes a step in which a sintered body is subjected to hot forming. Table 3 shows the general formulas of the sintered rare-earth magnets according to examples and comparative examples, the content of the elements comprising R, the results of the analysis of structural forms, and the results of the determination of magnetic properties and magnetizability. Table 3 shows the general formula of the main phase 10 of each sample, i.e., of the sintered rare-earth magnet 1 according to examples 1 to 8 and comparative examples 1 to 18. Next, a method for analyzing the structure of the sintered rare-earth magnet 1 according to Examples 1 to 8 and Comparative Examples 1 to 18 is described. The structural shape of the sintered rare-earth magnet 1 is determined by elemental analysis using a scanning electron microscope (SEM) and EPMA. FE-EPMA (JEOL Ltd., product name: JXA-8530F) is used as both the SEM and EPMA. The conditions for the elemental analysis are as follows: accelerating voltage: 15.0 kV, irradiation current: 2.271e-008A, irradiation time: 130 ms, number of pixels: 512 × 512, magnification: 5000x, number of integrations: one. Next, a method for evaluating the magnetic properties of the sintered rare-earth magnet 1 according to Examples 1 to 8 and Comparative Examples 1 to 18 is described. The evaluation of the magnetic properties is performed by measuring the coercivity of a variety of samples using a pulse-excitation BH tracer. The maximum magnetic field generated by the BH tracer is equal to or greater than 6 T, at which the sintered rare-earth magnet 1 is fully magnetized. In addition to the pulse-excitation BH tracer, a self-recording DC magnetometer, also called a DC BH tracer, a vibrating sample magnetometer (VSM), a magnetic properties measurement system (MPMS), a physical properties measurement system (PPMS), or the like may be used, provided that a maximum magnetic field of 6 T or more can be generated.The measurement is performed in an atmosphere containing an inert gas such as nitrogen. The magnetic properties of each sample are measured by detecting the magnetization of the sintered rare-earth magnet 1, which is magnetized by an applied magnetic field, using a search coil or magnetic sensor. Magnetic properties are measured using a JH curve or a BH curve, which represents the measured magnetic hysteresis. The magnetic properties of each sample are measured at a first measurement temperature T1 and a second measurement temperature T2, which differ from each other.The temperature coefficient α [% / °C] of the residual magnetic flux density is a value obtained by calculating the ratio of the difference between the residual magnetic flux density at the first measurement temperature T1 and the residual magnetic flux density at the second measurement temperature T2 to the residual magnetic flux density at the first measurement temperature T1 and dividing the ratio by the temperature difference (T2-T1).The temperature coefficient β [% / °C] of the coercive force is a value obtained by calculating the ratio of the difference between the coercive force at the first measurement temperature T1 and the coercive force at the second measurement temperature T2 to the coercive force at the first measurement temperature T1, and by dividing the ratio by the temperature difference (T2-T1). Therefore, the smaller the absolute values ​​|α| and |β| of the temperature coefficients of the magnetic properties are, the more effectively the deterioration of the magnetic properties of the magnet due to a temperature increase is prevented. Furthermore, the measurement of magnetizability is obtained by calculating the magnetization rate based on the ratio between the magnetic flux density measured by the magnetic hysteresis loop applied by any magnetic field and the magnetic flux density measured by the magnetic hysteresis loop applied by a saturated magnetic field, at a constant permeance coefficient. A higher magnetization rate achieved with a lower magnetic field indicates high magnetizability. First, the results of the analysis of the samples according to Examples 1 to 8 and the comparative examples 1 to 18 are described. Fig. 8 is a recording of a composition map obtained by analyzing a cross-section of a sintered rare-earth magnet according to Examples 1 to 8 with FE-EPMA. Figs. 9, 10, 11, 12, 13, 14 to 15 are elemental maps obtained by analyzing a cross-section of a sintered rare-earth magnet according to Examples 1 to 8 with FE-EPMA. Fig. 9 is an element chart of Nd, Fig. 10 is an element chart of Pr, Fig. 11 is an element chart of Tb, Fig. 12 is an element chart of Co, Fig. 13 is an element chart of O, Fig. 14 is an element chart of Sm, and Fig. 15 is an element chart of La. It should be noted that Figs. 9, 10, 11, 12, 13, 14 to 15 are the element charts corresponding to the area shown in Fig. 8.Since the sintered rare-earth magnets 1 according to Examples 1 to 8 all yield similar results, representative examples from Examples 1 to 8 are shown in Figs. 8, 9, 10, 11, 12, 13, 14 to 15. Furthermore, components corresponding to those in Figs. 1 and 2 are designated with the same reference numerals. As illustrated in Figs. 9, 10 to 11, it is confirmed in each sample of Examples 1 to 8 that the main phase 10, which contains crystal grains based on an Nd₂Fe₁₄B crystal structure of the sintered rare-earth magnet 1 satisfying the general formula (Nd, Pr, Tb, R)-Fe-BM, where RH is Tb and R is one or more rare-earth elements selected excluding Nd, Pr, and RH, includes the core sections 11c and 12c and the shell sections 11s and 12s covering the core sections 11c and 12c. Furthermore, it is confirmed that in the main phase 10, the first main phase 11 satisfies CNd > CPr, and the second main phase 12 satisfies CNd <CPr erfüllt, gemischt bereitgestellt sind. Es wird zudem bestätigt, dass, wenn die Konzentration von Tb der ersten Hauptphase 11 C1Tb ist und die Konzentration von Tb der zweiten Hauptphase 12 C2Tb ist, C1Tb> C2Tb is fulfilled. Here, the concentration difference, which is fulfilled by "the first main phase 11, the CNd>CPr, and the second main phase 12, the CNd <CPr erfüllt“ angegeben wird, dass ein deutlicher Unterschied zwischen der Nachweisintensität von Nd und der Nachweisintensität von Pr gemäß Kartenanalyse mittels EPMA besteht. Insbesondere ist am Beispiel der ersten Hauptphase 11 die EPMA-Nachweisintensität der Konzentration von Nd im Kernabschnitt 11c höher als der Durchschnitt und die EPMA-Nachweisintensität der Konzentration von Pr niedriger als der Durchschnitt und liegt in diesem Fall in der Nähe des unteren Grenzwerts. In der zweiten Hauptphase 12 ist der Fall umgekehrt zur ersten Hauptphase 11. In particular, with reference to the map diagram of Nd in Fig. 9 and the map diagram of Pr in Fig. 10 as examples, the average detection value of Nd with EPMA is 89 and the average detection value of Pr is 46. In the case of the first main phase 11, CNd is higher than 89, CPr is around the lower limit, and there is a clear concentration difference. Since the second main phase 12 is also the opposite of the first main phase 11, CPr is higher than 46, CNd is around the lower limit, and there is a clear concentration difference. Here, the concentration difference indicated by "C1Tb>C2Tb" means that there is a significant difference between the detection intensity of Tb in the first main phase 11 and the detection intensity of Tb in the second main phase 12 according to map analysis using EPMA. Specifically, the EPMA detection intensity of the Tb concentration in the first main phase 11 is higher than average, and the EPMA detection intensity of the Tb concentration in the second main phase is lower than average and, in this case, close to the lower limit. In particular, with reference to the diagram of Tb in Fig. 11 as an example, the average of the detection values ​​of Tb with EPMA is 44. In the case of the first main phase 11, CTb is higher than 44, but in the case of the second main phase 12, CTb is around the lower limit, and there is a clear difference in concentration. As illustrated in Figs. 12, 13, 14 to 15, the sintered rare-earth magnet 1, when R = La and / or Sm, comprises the first subphase 21, which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, Tb, La, Sm)-O, containing the element M as a minor component, and the second subphase 22, which is crystalline and has a major component represented by (Nd, Pr, Tb, La)-O, containing the element M as a minor component, in addition to the first main phase 11 and the second main phase 12 in the first embodiment. Furthermore, it is confirmed that the concentration of Sm in the first subphase 21 is higher than in the second subphase 22, and the concentration of Co, i.e., of the element M, is higher in the second subphase 22 than in the first subphase 21. In Table 3, since the sum of the concentration of Nd and the concentration of Tb, the heavy rare earth element RH, is denoted by C(Nd,RH), “○” is entered in the columns of the first main phase 11 and the second main phase 12 for the samples in which the states of the first main phase 11 satisfy C(Nd,RH)>CPr and of the second main phase 12 satisfy C(Nd,RH) <CPr erfüllt, bestätigt werden, und wird „ד in den Spalten der ersten Hauptphase 11 und der zweiten Hauptphase 12 für die Proben eingegeben, in denen solche Zustände nicht bestätigt werden. Der Konzentrationsunterschied mit Ungleichheitszeichen bedeutet, dass ein deutlicher Unterschied zwischen der Nachweisintensität von Nd und Tb und der Nachweisintensität von Pr besteht.As a concrete example, the case of the first main phase 11 shows that the EPMA detection intensity of the concentrations of Nd and Tb is higher than average, and the EPMA detection intensity of the concentration of Pr is lower than average, in this case close to the lower limit. In the second main phase 12, the case is the reverse of the first main phase 11. If only C(Nd,RH) <CPr wie in der zweiten Hauptphase 12 bestätigt wird, wird „○“ nur in der Spalte der zweiten Hauptphase 12 eingegeben, und „ד wird in der Spalte der ersten Hauptphase 11 eingegeben. Furthermore, in Table 3, for samples that have been confirmed to have the first subphase 21, which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, Tb, La, Sm)-O, containing the element M as a minor component, and the second subphase 22, which is crystalline and has a major component represented by (Nd, Pr, Tb, La)-O, containing the element M as a minor component, and for which it has been confirmed that the concentration of M in the second subphase 22 is higher than in the first subphase 21, “○” is entered in each of the columns “M concentration first subphase”. <zweite Unterphase“ in „Unterphase“ des Punktes „Strukturform“ eingegeben, und für Proben, bei denen dies nicht bestätigt wird, wird „ד in jede der Spalten „M-Konzentration erste Unterphase<zweite Unterphase“ in „Unterphase“ des Punktes „Strukturform“ eingegeben.Furthermore, if there is only one subphase 20 or no difference in the concentration of Sm between the subphases 20, the columns "M concentration first subphase" will show the value. <zweite Unterphase“ in „Unterphase“ des Punktes „Strukturform“ „ד eingegeben. Here, the Sm concentration difference between the first sub-phase 21 and the second sub-phase 22 means that the detection intensity of Sm according to map analysis using EPMA is, on average, higher in the first sub-phase 21 than in the second sub-phase 22. Specifically, referring to the Sm map diagram in Fig. 14 as an example, the average Sm detection value with EPMA is 15.0, and the first sub-phase 21 is higher than 15.0, whereas the second sub-phase 22 is lower than 15.0, indicating a detection error due to aggregation. It should be noted that the concentration difference of Co, i.e., element M, between the first sub-phase 21 and the second sub-phase 22 means that the detection intensity of Co in the second sub-phase 22, according to map analysis with EPMA, is, on average, higher than in the first sub-phase 21. Specifically, referring to the Co map diagram in Fig.For example, in 12 the average value of the detection values ​​for Co with EPMA is 31.8, and the second sub-phase 22 is higher than 31.8, whereas the first sub-phase 21 is lower than 31.8, which indicates a detection error due to aggregation. Furthermore, the intensity ratio of the element map obtained by FE-EPMA analysis confirms that the number of first main phases 11 that are C(Nd, RH)>CPr is greater than the number of second main phases 12 that are C(Nd, RH) <CPr sind. Mit Blick auf die Schalenabschnitte 11s und 12s der Kern-Schale-Struktur wird zudem bestätigt, dass die erste Hauptphase 11 die Vergleichsausdrücke CNd> SNd, CPr<SPr und CTb> STb is fulfilled and the second main phase 12 the comparison expressions CNd<SNd, CPr> SPr and CTb <STb erfüllt. Next, the results of the magnetic property measurements in each sample, as shown in Examples 1 to 8 and Comparative Examples 1 to 18, are described. Each sample undergoing magnetic measurement is a block measuring 7 mm in length, 7 mm in width, and 7 mm in height. The first measurement temperature, T1, is 23 °C, and the second measurement temperature, T2, is 200 °C. 23 °C is room temperature. The 200 °C measurement temperature, T2, is a temperature that can occur in the operating environment of automotive and industrial engines. First, the residual magnetic flux density and coercive force in each sample are determined according to Examples 1 to 8 and Comparison Examples 2 to 18 in comparison to Comparison Example 1. If the values ​​of the residual magnetic flux density and coercive force of each sample at 23 °C are within an allowable measurement error of 1% compared to the values ​​of Comparison Example 1, the values ​​are classified as "equivalent". Values ​​that are 1% or more above this are classified as "good", and values ​​that are 1% or more below this are classified as "poor". Next, the temperature coefficient α of the residual magnetic flux density is calculated using the residual magnetic flux density at the first measurement temperature T1 of 23 °C and the residual magnetic flux density at the second measurement temperature T2 of 200 °C. The temperature coefficient β of the coercive force is calculated using the coercive force at the first measurement temperature T1 of 23 °C and the coercive force at the second measurement temperature T2 of 200 °C. The temperature coefficient of the residual magnetic flux density and the temperature coefficient of the coercive force in each sample according to Examples 1 to 8 and Comparison Examples 2 to 18 are determined in comparison to Comparison Example 1.If the values ​​of each sample are within a permissible measurement error of ±1% of the absolute value |α| of the temperature coefficient of the residual magnetic flux density and the absolute value |β| of the temperature coefficient of the coercive force in the sample of comparison example 1, the values ​​are classified as "equivalent". Values ​​1% or more below this value are classified as "good", and values ​​1% or more above this value are classified as "poor". Since the samples classified as "good" have a lower temperature coefficient, it is possible to provide the sintered rare-earth magnet 1 with stable magnetic properties even in high-temperature environments, while simultaneously preventing a deterioration of the magnetic properties associated with a temperature increase. Next, the magnetizability is determined by calculating the magnetization rate from the ratio of the magnetic flux density, which is the intersection of the magnetic hysteresis of the applied magnetic field of 20 kOe and the permeance coefficient Pc, to the magnetic flux density, which is the intersection of the magnetic hysteresis of the applied magnetic field of 80 kOe in the saturation magnetization state and the permeance coefficient Pc. The magnetizability in each sample according to Examples 1 to 8 and Comparison Examples 2 to 18 is determined in comparison to Comparison Example 1. That is, for each sample, values ​​of -1% or more, which are considered measurement errors, are classified as "equivalent or better," and values ​​of -1% or more that are lower are classified as "poor."For samples that are classified as "equivalent or better", it is possible to provide the sintered rare earth magnet 1 with high magnetizability. The results of the determination of the residual magnetic flux density, the coercive force, the temperature coefficient of the residual magnetic flux density, the temperature coefficient of the coercive force and the magnetizability are shown in Table 3. Comparative Example 1 is a sample of the sintered rare-earth magnet 1, which was produced in the form of (Nd, Tb)-Fe-BM using the manufacturing process described in Patent Document 1, employing Nd, Tb, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural form of this sample produced using the above-described method does not confirm a core-shell structure in the main phase 10 due to the absence of Pr, La, and Sm, nor does it confirm that the concentration of Sm in subphase 20 is higher in the first subphase 21 than in the second subphase 22. Furthermore, it is not confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21. Evaluation of the magnetic properties of this sample using the above-described method shows that the residual magnetic flux density Br is 1.25 T and the coercive force HcJ is 1650 kA / m.The temperature coefficients of the residual magnetic flux density and the coercive force are |α| = 0.185% / °C and |β| = 0.455% / °C, respectively. The magnetization rate is 98.6%. These values ​​from comparison example 1 are used as a reference. Comparative Example 2 is a sample of the sintered rare-earth magnet 1, which was produced in the form of (Nd, Tb)-Fe-BM using the manufacturing process described in Patent Document 1, employing Nd, Tb, Fe, and FeB as raw materials. In Comparative Example 2, Co, i.e., the element M, is not added. Observation of the structural form of this sample produced using the above-described method does not confirm a core-shell structure in the main phase 10 due to the absence of Pr, La, and Sm, nor does it confirm that the concentration of Sm in subphase 20 is higher in the first subphase 21 than in the second subphase 22. Furthermore, since Co is not present, it is not confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21.The evaluation of the magnetic properties of this sample using the method described above shows that the residual magnetic flux density is "poor" and the coercivity is "poor" because Co, i.e., the element M, is not present. Furthermore, the temperature coefficient of the residual magnetic flux density is "equivalent," the temperature coefficient of the coercivity is "equivalent," and the magnetizability is "equivalent or better." Comparative Example 3 is a sample of the sintered rare-earth magnet 1, which was produced in the form of Nd-Fe-BM using the manufacturing process described in Patent Document 1, employing Nd, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural form of this sample produced using the above-described method reveals that, due to the absence of Pr, La, and Sm, a core-shell structure in the main phase 10 is not confirmed, nor is it confirmed that the concentration of Sm in subphase 20 is higher in the first subphase 21 than in the second subphase 22. Furthermore, it is not confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21. Evaluation of the magnetic properties of this sample using the above-described method shows that the residual magnetic flux density is "good," which is better than in Comparative Example 1, and the coercive force is "poor," i.e.,significantly lower than in comparative example 1, since Tb, i.e., the heavy rare-earth element RH, is not contained in the main phase 10. Furthermore, the temperature coefficient of the residual magnetic flux density is "equivalent," the temperature coefficient of the coercive force is "equivalent," and the magnetizability is "equivalent or better." Comparative Example 4 is a sample of the sintered rare-earth magnet 1, which was produced in the form of (Nd, Pr)-Fe-BM using the manufacturing process described in patent document 1, employing Nd, Pr, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural form of this sample produced using the aforementioned process confirms the presence of the main phase 10, in which Nd and Pr are mixed, due to the addition of Pr; however, a core-shell structure is not formed. Furthermore, due to the absence of La and Sm, it is not confirmed that the concentration of Sm in subphase 20 is higher in the first subphase 21 than in the second subphase 22. Similarly, it is not confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21.The evaluation of the magnetic properties of this sample using the method described above shows that no improvement in coercivity can be achieved compared to a case containing Tb, even though Tb (i.e., the heavy rare-earth element RH) is not present and Pr is present instead. Therefore, the residual magnetic flux density is "good," i.e., better than in Comparative Example 1, and the coercivity is "poor," i.e., lower than in Comparative Example 1. Furthermore, the addition of Pr worsens the temperature coefficient of the coercivity, which is characteristic of Pr, to "poor." Since the manufacturing process does not involve hot forming, the magnetizability is "equivalent or better." It should be noted that the temperature coefficient of the residual magnetic flux density is "equivalent."This result reflects the fact that the magnetic anisotropy of the main phase 10 is increased and the coercive force is improved by the addition of Pr, but the structural shape in the main phase 10 and the subphase 20 is not optimal. Comparative Example 5 is a sample of the sintered rare-earth magnet 1, which was produced in the form of (Nd, Pr, Tb)-Fe-BM using the manufacturing process described in patent document 1, employing Nd, Pr, Tb, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural form of this sample produced using the aforementioned process confirms the presence of the main phase 10, in which Nd and Pr are mixed; however, a core-shell structure is not formed. Furthermore, due to the absence of La and Sm, it is not confirmed that the concentration of Sm in subphase 20 is higher in the first subphase 21 than in the second subphase 22. Similarly, it is not confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21.The evaluation of the magnetic properties of this sample using the method described above shows that the residual magnetic flux density and the coercive force are improved by the inclusion of Pr and Tb, i.e., the heavy rare-earth element RH, and that the residual magnetic flux density is "equivalent" and the coercive force is "good." However, the temperature coefficient of the coercive force, which is characteristic of Pr, has deteriorated and is "poor." Since the manufacturing process does not involve hot forming, the magnetizability is "equivalent or better." It should be noted that the temperature coefficient of the residual magnetic flux density is "equivalent." This result reflects the fact that while the magnetic anisotropy of the main phase 10 is increased and the coercive force is improved by the addition of Tb, Pr, and Co, the structural shape in the main phase 10 and the subphase 20 is not optimal. Comparative Example 6 is a sample of the sintered rare-earth magnet 1, which was produced in the form of (Nd, La, Sm)-Fe-BM using the manufacturing process described in patent document 1, employing Nd, La, Sm, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural form of this sample produced using the aforementioned process reveals that a core-shell structure is not confirmed in the main phase 10 due to the absence of Pr. Furthermore, the addition of La and Sm segregates the concentration of Sm in a subphase 20 along with the segregation of La, but the second subphase 22 does not exist. It cannot be confirmed that the concentration of Sm in the first subphase 21 is higher than in the second subphase 22, nor can it be confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21.The evaluation of the magnetic properties of this sample using the method described above shows that, due to the absence of Tb, i.e., the heavy rare-earth element RH, the residual magnetic flux density is "good," but the coercivity is significantly lower than in comparison example 1 and therefore "poor." With the addition of La and Sm, and their presence in the main phase 10 or subphase 20, the temperature coefficient of the residual magnetic flux density and the temperature coefficient of the coercivity are "good." Since the manufacturing process does not involve hot forming, the magnetizability is "equivalent or better."This result reflects the fact that the presence of La and Sm in the main phase 10 or the sub-phase 20 leads to a good result in the temperature coefficient of the coercive force, but the magnetic properties at room temperature are not improved and the structural shape in the main phase 10 and the sub-phase 20 is not optimal. Comparative Example 7 is a sample of the sintered rare-earth magnet 1, produced in the form of (Nd, La, Sm)-Fe-BM using the manufacturing process described in Patent Document 1 and employing Nd, La, Sm, Fe, FeB, and Co, i.e., the element M, as raw materials. The compositional ratio of Nd, La, and Sm differs from that of Comparative Example 6. Observation of the structural form of this sample produced using the aforementioned process confirms that a core-shell structure is not present in the main phase 10 due to the absence of Pr. Furthermore, the addition of La and Sm segregates the concentration of Sm in a subphase 20 along with the segregation of La, but the second subphase 22 does not exist.Furthermore, it cannot be confirmed that the concentration of Sm in the first subphase 21 is higher than in the second subphase 22, nor can it be confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21. Evaluation of the magnetic properties of this sample using the method described above shows that, despite adjusting the addition amounts of La and Sm, there is no significant change compared to Comparative Example 6. That is, since Tb, i.e., the heavy rare-earth element RH, is not present, the residual magnetic flux density is "good," but the coercivity is significantly lower than in Comparative Example 1 and therefore "poor." The temperature coefficient of the residual magnetic flux density is "good," and the temperature coefficient of the coercivity is "good." Since the manufacturing process does not involve hot forming, the magnetizability is "equivalent or better."The result of comparative example 7 reflects the fact that the addition of La and Sm leads to a good result in the temperature coefficient of the magnetic properties, but the magnetic properties at room temperature are not improved because Tb, i.e. the heavy rare earth element RH, is not added to the base material, and the structural shape in the main phase 10 and the sub-phase 20 is not optimal: changing the composition ratio of Nd, La, Sm leads to almost the same result as in comparative example 6. Comparative example 8 is a sample of the sintered rare-earth magnet 1, which was produced in the form of (Nd, Pr, La, Sm)-Fe-BM using the manufacturing process described in patent document 1, employing Nd, Pr, La, Sm, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural form of this sample produced using the aforementioned process confirms the presence of the main phase 10, in which Nd and Pr are mixed, due to the addition of Pr; however, a core-shell structure is not formed. Furthermore, the addition of La and Sm segregates the concentration of Sm in a subphase 20 along with the segregation of La, but the second subphase 22 does not exist.Furthermore, it cannot be confirmed that the concentration of Sm in the first subphase 21 is higher than in the second subphase 22, nor can it be confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21. Evaluation of the magnetic properties of this sample using the method described above shows that, due to the absence of Tb, i.e., the heavy rare-earth element RH, the residual magnetic flux density is "good," but the coercive force is "poor," since the addition of La, Sm, and Pr does not improve the coercive force as it does in the case of the addition of Tb. Although the temperature coefficient of the residual magnetic flux density and the temperature coefficient of the coercive force should be "good," only the temperature coefficient of the coercive force is reduced to "equivalent" by the addition of Pr, as the temperature coefficient of the coercive force, which is characteristic of Pr, is degraded.Since the manufacturing process does not involve hot forming, the magnetizability is "equivalent or better". Comparative example 9 is a sample of the sintered rare-earth magnet 1, which was produced in the form of (Nd, Pr, Tb, La, Sm)-Fe-BM using the manufacturing process described in patent document 1 and employing Nd, Pr, Tb, La, Sm, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural form of this sample produced using the aforementioned process confirms the presence of the main phase 10, in which Nd and Pr are mixed, due to the addition of Pr; however, a core-shell structure is not formed. Furthermore, the addition of La and Sm segregates the concentration of Sm in a subphase 20 along with the segregation of La, but the second subphase 22 does not exist.Furthermore, it cannot be confirmed that the concentration of Sm in the first subphase 21 is higher than in the second subphase 22, and it cannot be confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21. The evaluation of the magnetic properties of this sample using the method described above shows that the addition of Tb, i.e., the heavy rare-earth element RH, greatly improves the coercive force compared to reference example 8 and is therefore "good," but since the structure of the main phase 10 and the subphase 20 cannot be controlled, the residual magnetic flux density is significantly reduced and therefore "poor."The temperature coefficient of the residual magnetic flux density and the temperature coefficient of the coercive force correspond to those of comparison example 8: The temperature coefficient of the residual magnetic flux density is "good" and the temperature coefficient of the coercive force is "equivalent". Since the manufacturing process does not involve hot forming, the magnetizability is "equivalent or better". Comparative example 10 is a sample of the sintered rare-earth magnet 1, produced in the form of (Nd, Tb)-Fe-BM using the manufacturing process described in patent document 2, including hot forming, with Nd, Tb, Fe, FeB, and Co, i.e., element M, as raw materials. Observation of the structural form of this sample produced using the above-described process does not confirm a core-shell structure in the main phase 10 due to the absence of Pr, La, and Sm, nor does it confirm that the concentration of Sm in subphase 20 is higher in the first subphase 21 than in the second subphase 22. Furthermore, it is not confirmed that the concentration of Co is higher in the second subphase 22 than in the first subphase 21. However, the refinement of the structure, which is a characteristic of a magnet produced by hot forming, is confirmed.Furthermore, the evaluation of the magnetic properties of this sample using the method described above shows that the coercive force is "good" and the temperature coefficient of the coercive force is "equivalent," which is attributable to the refinement of the magnetic powder by hot forming. Since the magnetic moments are less likely to align, the residual magnetic flux density and the magnetizability are reduced to "poor." The temperature coefficient of the residual magnetic flux density is "equivalent." This result reflects the decrease in the residual magnetic flux density and the deterioration in magnetizability due to the less likely alignment of the magnetic moments, despite the improvement in the absolute value of the coercive force and the temperature coefficient of the coercive force that accompanies the refinement of the magnetic powder by hot forming. Comparative example 11 is a sample of the sintered rare-earth magnet 1, which was produced in the form of Nd-Fe-BM using the manufacturing process described in patent document 2, including hot forming, with Nd, Fe, FeB, and Co, i.e., element M, as raw materials. Observation of the structural form of this sample produced using the above-described process does not confirm a core-shell structure in the main phase 10 due to the absence of Pr, La, and Sm, nor does it confirm that the concentration of Sm in subphase 20 is higher in the first subphase 21 than in the second subphase 22. Furthermore, it is not confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21. However, the refinement of the structure, which is a characteristic of a magnet produced by hot forming, is confirmed.The evaluation of the magnetic properties of this sample using the method described above shows that, due to the refinement of the magnetic powder, the coercivity is "good" and the temperature coefficient of the coercivity is "equivalent." However, the magnetizability is "poor" because the magnetic moments are less likely to align. Since no Tb is present, a significant deterioration of the residual magnetic flux density is prevented, and its level is comparable to that of Comparison Example 1, so the residual magnetic flux density is "equivalent." The temperature coefficient of the residual magnetic flux density is "equivalent." This result reflects the deterioration in magnetizability because the magnetic moments are less likely to align, despite the improvement in coercivity that accompanies the refinement of the magnetic powder by hot forming. Comparative Example 12 is a sample of the sintered rare-earth magnet 1, produced in the form of Nd-Fe-B using the manufacturing process described in Patent Document 2, including hot forming, with Nd, Fe, and FeB as raw materials. In Comparative Example 12, Co, i.e., the element M, is not added. Observation of the structural form of this sample produced using the above-described process does not confirm a core-shell structure in the main phase 10 due to the absence of Pr, La, and Sm, nor does it confirm that the concentration of Sm in subphase 20 is higher in the first subphase 21 than in the second subphase 22. Furthermore, since Co is not present, it is not confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21. However, the refinement of the structure, which is a characteristic of a magnet produced by hot forming, is confirmed.The evaluation of the magnetic properties of this sample using the method described above shows that the residual magnetic flux density is "poor," the coercive force is "good," the temperature coefficient of the residual magnetic flux density is "equivalent," the temperature coefficient of the coercive force is "equivalent," and the magnetizability is "poor." This result reflects the decrease in the residual magnetic flux density and the deterioration of the magnetizability because the magnetic moments are less likely to align, even though the coercive force is improved and the temperature coefficient of the residual magnetic flux density and the temperature coefficient of the coercive force are equivalent in conjunction with the refinement of the magnetic powder by hot forming. Comparative Example 13 is a sample of the sintered rare-earth magnet 1, produced in the form of (Nd, Pr)-Fe-BM using the manufacturing process described in patent document 2, including hot forming, with Nd, Pr, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural shape of this sample produced using the above-described process confirms the core-shell structure through hot forming in addition to the addition of Pr. The core-shell structure is confirmed only in one type of main phase 10 with a high concentration of Pr in the core section. Furthermore, due to the absence of La and Sm, it is not confirmed that the concentration of Sm in subphase 20 is higher in the first subphase 21 than in the second subphase 22. Similarly, it is not confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21.Evaluation of the magnetic properties of this sample using the method described above shows that, due to the refinement of the magnetic powder, the coercivity is "good" and the temperature coefficient of the coercivity is "equivalent". Since the magnetic moments are less likely to align, the residual magnetic flux density and magnetizability are "poor". The temperature coefficient of the residual magnetic flux density is "equivalent". This indicates that the coercivity is significantly improved to the level of sintered rare-earth magnet 1 containing Tb due to the formation of the core-shell structure with a high concentration of Pr in the core section, while the other properties reflect the structural refinement achieved through hot forming. Comparative Example 14 is a sample of the sintered rare-earth magnet 1, produced in the form of (Nd, Pr, Tb)-Fe-BM using the manufacturing process described in patent document 2, including hot forming, with Nd, Pr, Tb, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural shape of this sample produced using the above-described process confirms the core-shell structure through hot forming in addition to the addition of Pr. The core-shell structure is confirmed only in one type of main phase 10 with a high concentration of Pr in the core section. Furthermore, due to the absence of La and Sm, it is not confirmed that the concentration of Sm in subphase 20 is higher in the first subphase 21 than in the second subphase 22. Similarly, it is not confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21.The evaluation of the magnetic properties of this sample using the method described above also shows that, due to the refinement of the magnetic powder, the coercivity is "good" and the temperature coefficient of the coercivity is "equivalent". Since the magnetic moments are less likely to be aligned, the residual magnetic flux density and the magnetizability are "poor". The temperature coefficient of the residual magnetic flux density is "equivalent". This suggests that the coercivity is significantly improved by substituting Tb with high magnetocrystalline anisotropy for a portion of the Nd, in addition to its production by hot forming, while the other properties reflect the refinement of the structure by hot forming. Comparative Example 15 is a sample of the sintered rare-earth magnet 1, produced in the form of (Nd, La, Sm)-Fe-BM using the manufacturing process described in patent document 2, including hot forming, with Nd, La, Sm, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural shape of this sample produced using the above-described process does not confirm a core-shell structure in the main phase 10 due to the absence of Pr. Furthermore, the addition of La and Sm segregates the concentration of Sm in a subphase 20 along with the segregation of La, but the second subphase 22 does not exist. It also cannot be confirmed that the concentration of Sm in the first subphase 21 is higher than in the second subphase 22, nor can it be confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21.Furthermore, the evaluation of the magnetic properties of this sample using the method described above shows that the coercive force and the temperature coefficient of the coercive force are "good" due to the refinement of the magnetic powder. Since the magnetic moments are less likely to align, the residual magnetic flux density and the magnetizability are "poor." The temperature coefficient of the residual magnetic flux density is "good." This result reflects the fact that the presence of La and Sm in the main phase 10 or the subphase 20 leads to a good result for the temperature coefficient of the magnetic properties, but the residual magnetic flux density and the magnetizability at room temperature are not improved because the magnetic moments are less likely to align and the structural shape in the main phase 10 and the subphase 20 is not optimal. Comparative Example 16 is a sample of the sintered rare-earth magnet 1, produced in the form of (Nd, La, Sm)-Fe-BM using the manufacturing process described in Patent Document 2, including hot forming, and using Nd, La, Sm, Fe, FeB, and Co, i.e., the element M, as raw materials. The compositional ratio of Nd, La, and Sm in Comparative Example 16 differs from that of Comparative Example 15. Observation of the structural form of this sample produced using the process described above confirms that a core-shell structure is not present in the main phase 10 due to the absence of Pr. Furthermore, the addition of La and Sm segregates the concentration of Sm in a subphase 20 along with the segregation of La, but the second subphase 22 does not exist.Furthermore, it cannot be confirmed that the concentration of Sm in the first subphase 21 is higher than in the second subphase 22, nor can it be confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21. Moreover, the evaluation of the magnetic properties of this sample using the method described above shows that the coercive force and the temperature coefficient of the coercive force are "good" due to the refinement of the magnetic powder. Since the magnetic moments are less likely to align, the residual magnetic flux density and the magnetizability are "poor." The temperature coefficient of the residual magnetic flux density is "good."This result reflects the fact that the presence of La and Sm in the main phase 10 or the subphase 20 leads to a good result for the temperature coefficient of the magnetic properties, but the residual magnetic flux density and the magnetizability at room temperature are not improved, since the magnetic moments are less likely to be aligned and the structural shape in the main phase 10 and the subphase 20 is not optimal. Changing the composition ratio of Nd, La, Sm leads to almost the same result as in comparative example 15. Comparative Example 17 is a sample of the sintered rare-earth magnet 1, which was produced in the form of (Nd, Pr, La, Sm)-Fe-BM using the manufacturing process described in patent document 2, including hot forming, and using Nd, Pr, La, Sm, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural shape of this sample produced using the aforementioned process confirms the core-shell structure, which is further confirmed by hot forming in addition to the addition of Pr. The core-shell structure is confirmed only in one type of the main phase 10 with a high concentration of Pr in the core section. Furthermore, the addition of La and Sm segregates the concentration of Sm in a subphase 20 along with the segregation of La, but the second subphase 22 does not exist.Furthermore, it cannot be confirmed that the concentration of Sm in the first subphase 21 is higher than in the second subphase 22, nor can it be confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21. Moreover, the evaluation of the magnetic properties of this sample using the method described above shows that the coercive force and the temperature coefficient of the coercive force are "good" due to the refinement of the magnetic powder. Since the magnetic moments are less likely to align, the residual magnetic flux density and the magnetizability are "poor." The temperature coefficient of the residual magnetic flux density is "good."This result reflects the fact that the residual magnetic flux density and the magnetizability at room temperature are not improved and the structural shape in the main phase 10 and the subphase 20 is not optimal, since the magnetic moments are less likely to be aligned, although the coercive force is significantly improved to the level of the sintered rare-earth magnet 1 to which Tb is added, by the formation of the core-shell structure in which the concentration of Pr in the core section is high and the temperature coefficient of the magnetic properties, in particular the temperature coefficient of the coercive force, is good due to the presence of La and Sm in the main phase 10 or the subphase 20. Comparative example 18 is a sample of the sintered rare-earth magnet 1, which was produced in the form of (Nd, Pr, Tb, La, Sm)-Fe-BM using the manufacturing process described in patent document 2, including hot forming, and using Nd, Pr, Tb, La, Sm, Fe, FeB, and Co, i.e., the element M, as raw materials. Observation of the structural shape of this sample produced using the aforementioned process confirms the core-shell structure, which is further confirmed by hot forming in addition to the addition of Pr. The core-shell structure is confirmed only in one type of the main phase 10 with a high concentration of Pr in the core section. Furthermore, the addition of La and Sm segregates the concentration of Sm in a subphase 20 along with the segregation of La, but the second subphase 22 does not exist.Furthermore, it cannot be confirmed that the concentration of Sm in the first subphase 21 is higher than in the second subphase 22, nor can it be confirmed that the concentration of Co in the second subphase 22 is higher than in the first subphase 21. Moreover, the evaluation of the magnetic properties of this sample using the method described above shows that the coercive force and the temperature coefficient of the coercive force are "good" due to the refinement of the magnetic powder. Since the magnetic moments are less likely to be aligned, the residual magnetic flux density and the magnetizability are "poor." The temperature coefficient of the residual magnetic flux density is "good."This result reflects the fact that the residual magnetic flux density and the magnetizability at room temperature are not improved, and the structural shape in the main phase 10 and the subphase 20 is not optimal because the magnetic moments are less likely to be aligned, although the coercivity is significantly improved by the formation of the core-shell structure, in which the concentration of Pr in the core section is high, and by the addition of Tb, and the temperature coefficient of the magnetic properties, especially the temperature coefficient of the coercivity, is good due to the presence of La and Sm in the main phase 10 or the subphase 20. The samples of Examples 1 to 8 are the sintered rare-earth magnet 1, which comprises: the main phase 10, satisfying the general formula (Nd, Pr, Tb, R)-Fe-BM, where the heavy rare-earth element RH is Tb, R is one or more rare-earth elements selected excluding Nd, Pr, and Tb, and M is one or more elements selected from a group consisting of Ga, Al, Cu, and Co, wherein the main phase contains crystal grains based on an Nd₂Fe₁₄B crystal structure; and the subphase 20, which is located between the main phase 10 and the subphase 20. The main phase 10 comprises the core sections 11c and 12c and the shell sections 11s and 12s, which cover the core sections 11c and 12c. Main phase 10 includes the first main phase 11, which fulfills CNd>CPr, and the second main phase 12, which fulfills CNd <cpr erfüllt, die konzentration von tb, d. h. dem schweren seltenerdelement rh, in der ersten hauptphase 11 ist höher als tb zweiten 12, und erste zweite 12 werden gemischt bereitgestellt. der gesinterte seltenerdmagnet 1 beispiele bis 8 erfüllt r="La" sm, zusätzlich zu umfasst unterphase 20 21, kristallin hauptsächlich aus einer oxidphase besteht, durch (nd, pr, la, sm)-o dargestellt wird, wobei das element m nebenbestandteil enthalten ist, 22, la)-o sm 21 22 des elements 21. zudem wird abschnitt mit hoher 41 gebildet, ein sm-anreicherungsabschnitt ist. die evaluierung magnetischen eigenschaften probe gemäß den beispielen vorstehend beschriebenen verfahren zeigt, dass magnetische restflussdichte „gut", koerzitivkraft temperaturkoeffizient „gut" magnetisierbarkeit „gleichwertig oder besser" somit haben diese gesinterten seltenerdmagnete im vergleich zum stand technik hervorragende eine ausgezeichnete magnetisierung, während gleichzeitig verwendung nd rh reduziert teuer sind aufgrund starken verteilungsungleichheit beschaffungsrisiko darstellen.As can also be seen from Table 3, the content of Tb, i.e., the heavy rare-earth element RH, in the samples of Examples 1 to 8 is lower than in the samples of Comparative Examples 1, 2, 5, 9, 10, 14, and 18, yet better magnetic properties are achieved than in the samples of Comparative Examples 1 to 18. In particular, when attempting to achieve magnetic properties in the samples of Comparative Examples 10, 14, and 18, which were produced using the manufacturing process of Patent Document 2, that correspond to those of the samples of Examples 1 to 8, it is necessary that Tb be included in addition. Thus, the sintered rare-earth magnet 1 according to the first and second embodiments also has the effect of reducing the amount of the heavy rare-earth element RH used compared to the technology of Patent Document 2.Alternatively, in a case where the content of the heavy rare-earth element RH in the rare-earth magnet produced by the manufacturing process of patent document 2 is the same as the content of the heavy rare-earth element RH in the sintered rare-earth magnet 1 according to the first and second embodiments, the magnetic properties of the rare-earth magnet produced by the manufacturing process of patent document 2 are lower than the magnetic properties of the sintered rare-earth magnet 1 according to the first and second embodiments. Furthermore, Table 3 shows that the samples of Examples 1 to 8, compared with the samples of Comparative Examples 1, 2, 5, and 9 produced by the manufacturing process of patent document 1, can improve the magnetic properties while reducing the content of Tb, i.e., the heavy rare-earth element RH. The configurations described in the aforementioned embodiments are examples. These embodiments can be combined with other known methods and with each other, and some of the configurations can be omitted or modified in a way that does not deviate from the basic concept. Reference symbol list 1 Sintered rare-earth magnet; 10 Main phase; 11 First main phase; 11c, 12c Core section; 11s, 12s Shell section; 12 Second main phase; 20 Sub-phase; 21 First sub-phase; 22 Second sub-phase; 41 High concentration section; 42 Low concentration section; 100 Rotor; 101 Rotor core; 102 Magnet insert hole; 120 Rotating machine; 130 Stator; 131 Teeth; 132 Winding. QUOTES INCLUDED IN THE DESCRIPTION This list of documents cited by the applicant was automatically generated and is included solely for the reader's convenience. The list is not part of the German patent or utility model application. The DPMA accepts no liability for any errors or omissions. Cited patent literature JP 2018-174313

[0005] JP 2018-174313 A

[0005] JP 2015-153813

[0005] JP 2015-153813 A

[0005] Cited non-patent literature JF Herbst et al., “Relationships between crystal structure and magnetic properties in Nd2Fe14B”, PHYSICAL REVIEW B. 1984, Vol. 29, No. 7, pp. 4176-4178

[0051] < / cpr>

Claims

Sintered rare-earth magnet comprising: a main phase satisfying a general formula (Nd, Pr, RH, R)-Fe-BM, wherein RH is a heavy rare-earth element including Dy and / or Tb, R is one or more rare-earth elements selected excluding Nd, Pr, Dy and Tb, and M is one or more elements selected from a group consisting of Ga, Al, Cu and Co, wherein the main phase contains crystal grains based on an Nd₂Fe₁₄B crystal structure; and a subphase formed between the main phase and the main phase, wherein the main phase includes a core section and a shell section covering the core section, the main phase includes a first main phase satisfying CNd > CPr, and a second main phase satisfying CNd <CPr erfüllt, wobei CNd eine Konzentration von Nd im Kernabschnitt und CPr eine Konzentration von Pr im Kernabschnitt ist,a concentration of the heavy rare earth element RH in the core section of the first main phase is higher than a concentration of the heavy rare earth element RH in the core section of the second main phase, the first main phase and the second main phase are provided mixed, the subphase includes a first subphase and a second subphase which are crystalline and consist mainly of an oxide phase represented by (Nd, Pr, RH, La, Sm)-O, containing the element M as a minor component, and a concentration of the element M in the second subphase is higher than in the first subphase. Sintered rare-earth magnet according to claim 1, wherein, in a case where the sintered rare-earth magnet is analyzed using an electron beam microanalysis device, with respect to a concentration of element M in the first subphase, a detection intensity of element M with the electron beam microanalysis device is lower than an average of detection intensities of element M, and with respect to a concentration of element M in the second subphase, a detection intensity of element M with the electron beam microanalysis device is higher than the average of detection intensities of element M. Sintered rare-earth magnet according to claim 1, wherein a number of the first main phases is greater than a number of the second main phases. Sintered rare-earth magnet according to claim 1, wherein the first main phase has the comparative expressions CNd>SNd, CPr<SPr und CRH> SRH is fulfilled and the second main phase the comparison expressions CNd<SNd, CPr> SPr and CRH <srh erfüllt,wobei snd eine konzentration von nd im schalenabschnitt, spr pr crh des schweren seltenerdelements rh kernabschnitt der hauptphase und srh schalenabschnitt ist.Sintered rare-earth magnet according to claim 1, wherein if R is La and / or Sm, the subphase comprises a first subphase which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, RH, La, Sm)-O, wherein the element M is included as a minor component, and a second subphase which is crystalline and consists mainly of an oxide phase represented by (Nd, Pr, RH, La)-O, wherein the element M is included as a minor component, and a concentration of Sm in the first subphase is higher than in the second subphase. A method for producing the sintered rare-earth magnet according to any one of claims 1 to 5, wherein the method comprises: a melting step for melting a raw material of an alloy for a sintered rare-earth magnet containing an element forming the sintered rare-earth magnet; a primary cooling step for cooling the raw material melted in the melting step to obtain a solidified alloy; a second cooling step for further cooling the solidified alloy to obtain an alloy for a sintered rare-earth magnet; a pulverization step for pulverizing the alloy for a sintered rare-earth magnet satisfying (Nd, Pr, RH, R)-Fe-BM; a forming step for producing a shaped body by forming powder from the alloy for a sintered rare-earth magnet that was pulverized in the pulverization step;a sintering step to obtain a sintered body by sintering the molded body at a predetermined sintering temperature; a primary aging step to maintain the sintered body at a primary aging temperature lower than the sintering temperature; a secondary aging step to maintain the sintered body held in the primary aging step at a secondary aging temperature lower than the primary aging temperature; a tertiary aging step to again maintain the sintered body held in the secondary aging step at the primary aging temperature; a quaternary aging step to again maintain the sintered body held in the tertiary aging step at the secondary aging temperature; and a cooling step to cool the sintered body held in the quaternary aging step. Rotor comprising: a rotor core; and the sintered rare-earth magnet according to any one of claims 1 to 5, which is provided in the rotor core. Rotary machine comprising: the rotor according to claim 7; and an annular stator opposite the rotor, comprising on an inner surface on a side on which the rotor is arranged windings provided on teeth projecting towards the rotor.< / srh>

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