Patent Application
20210074455
The present disclosure relates to a rare earth magnet and a production method thereof. More specifically, the present disclosure relates to an R—Fe—B-based rare earth magnet (wherein R is a rare earth element) excellent in both the coercive force and the residual magnetization and a production method thereof.
The R—Fe—B-based rare earth magnet includes a main phase and a grain boundary phase present around the main phase. The main phase is a magnetic phase having an R2Fe14B-type crystal structure. High residual magnetization is obtained due to this main phase. However, in the R—Fe—B-based rare earth magnet, magnetization reversal readily occurs between main phases to reduce the coercive force. To solve this problem, in the R—Fe—B-based rare earth magnet, it is common practice to magnetically separate main phases from one another by using a modifier and thereby enhance the coercive force.
Among R—Fe—B-based rare earth magnets, a Nd—Fe—B-based rare earth magnet (neodymium magnet) has an excellent balance between the performance and the cost and is most popular. Accordingly, the Nd—Fe—B-based rare earth magnet has spread rapidly, and the use amount of Nd is sharply increased, leaving the possibility that the use amount of Nd surpasses the production in the future. To cope with this issue, attempts to replace part of Nd by a light rare earth element such as Ce, La, Y and Sc are being made.
For example, Patent Literature 1 discloses a rare earth magnet produced by using, as a precursor, an R—Fe—B-based rare earth magnet containing a light rare earth element and diffusing and infiltrating a modifier containing a rare earth element except for a light rare earth element into the inside of the precursor. Specifically, a rare earth magnet produced by diffusing and infiltrating a Nd—Cu alloy as a modifier into a (Nd, Ce)—Fe—B-based rare earth magnet precursor is disclosed.
At the production of the rare earth magnet disclosed in Patent Literature 1, a rare earth magnet precursor with the main phase being nanocrystallized is used. In addition, the rare earth magnet precursor is previously subjected to hot plastic working before diffusing and infiltrating a modifier, and anisotropy is thereby imparted in the hot plastic working direction even after the diffusion and infiltration of the modifier.
[PTL 1] International Publication WO2014/196605A1
In the R—Fe—B-based rare earth magnet, the coercive force is enhanced by diffusing and infiltrating a modifier into a rare earth magnet precursor. The rare earth magnet precursor includes a main phase and a grain boundary phase present around the main phase, and the modifier diffuses and infiltrates mainly into the grain boundary phase. The modifier contains a rare earth element and a transition metal element. The transition metal element can be alloyed with the rare earth element. Hereinafter, such a transition metal element is sometimes referred to as “alloy element of the modifier”. In the case where, for example, an Nd—Cu alloy is used as the modifier, Nd can be alloyed with Cu, and the melting point of the modifier is thereby reduced. Accordingly, the modifier can be diffused and infiltrated into a rare earth magnet precursor at a relatively low temperature. When the modifier diffuses and infiltrates into a rare earth magnet precursor, the content of an alloy element of the modifier is increased in the grain boundary phase, and this makes it possible to magnetically separate the main phases from one another and enhance the coercive force. However, when the content of an alloy element of the modifier is increased in the grain boundary phase, the volume fraction of the main phase that develops magnetism decreases, and the residual magnetization is reduced.
Various attempts to compensate for the reduction in the residual magnetization are being made. For example, in the production method of a rare earth magnet disclosed in Patent Literature 1, a rare earth magnet precursor with the main phase being nanocrystallized is used so as to enhance in advance the residual magnetization of a rare earth magnet precursor and thereby compensate for the reduction in the residual magnetization after the diffusion and infiltration of a modifier. In addition, as in the production method disclosed in Patent Literature 1, a modifier containing a rare earth element (for example, Nd, etc.) other than a light rare earth element is diffused and infiltrated into a rare earth magnet precursor containing a light rare earth element (for example, Ce, etc.) so as to replace Ce, etc. in the vicinity of the surface layer part of the main phase of the rare earth magnet precursor by Nd, etc., and the residual magnetization of the main phase after the diffusion and infiltration of the modifier is thereby enhanced to compensate for reduction in the residual magnetization.
As the method to compensate for reduction in the residual magnetization, it may be considered to decrease the content of the alloy element of the modifier. However, when the content of the alloy element of the modifier is decreased, the melting point of the modifier increases, and this requires the diffusion and infiltration to be performed at a high temperature. In consequence, coarsening of the nanocrystallized main phase arises as a problem during diffusion and infiltration of the modifier.
The conventional attempt to compensate for the reduction of the residual magnetization disclosed in Patent Literature 1 has achieved a certain result. However, the demand for performance improvement of rare earth magnets is more increasing, and it is also increasingly likely that the cost of Nd, etc. soars. Under these circumstances, the present inventors have found a problem to be solved that an R—Fe—B-based rare earth magnet excellent in both the coercive force and the residual magnetization is desired also in the case of using a light rare earth element for at least part of the rare earth element.
The rare earth magnet of the present disclosure and the production method thereof have been invented so as to solve the problem above. An object of the present disclosure is to provide an R—Fe—B-based rare earth magnet excellent in both the coercive force and the residual magnetization also in the case of using a light rare earth element for at least part of the rare earth element, and a production method thereof.
The present inventors have made many intensive studies to attain the object above and have accomplished the rare earth magnet of the present disclosure and the production method thereof. The rare earth magnet of the present disclosure and the production method thereof includes the following embodiments.
<1> A rare earth magnet including a main phase and a grain boundary phase present around the main phase, wherein the overall composition is represented, in terms of molar ratio, by the formula: (R2(1-x)R1x)yFe(100-y-w-z-v)CowBzM1y (R3(1-p)M2p)q (wherein R1 is one or more elements selected from the group consisting of Ce, La, Y, and Sc, each of R2 and R3 is one or more elements selected from the group consisting of Nd, Pr, Gd, Tb, Dy, and Ho, M1 is composed of one or more elements selected from the group consisting of Ga, Al, Cu, Au, Ag, Zn, In, and Mn, and unavoidable impurity elements, M2 is composed of a transition metal element which is other than a rare earth element and can be alloyed with R3, and unavoidable impurity elements,
0.1≤x≤1.0,
12.0≤y≤20.0,
5.0≤z≤20.0,
0≤w≤8.0,
0≤v≤2.0,
0.05≤p≤0.40, and
0.1≤q≤15.0),
the main phase has an R2Fe14B-type (wherein R is a rare earth element) crystal structure,
the average particle diameter of the main phase is from 1 to 20 μm,
the main phase has a core portion and a shell portion present around the core portion,
the thickness of the shell portion is from 25 to 150 nm, and
with respect to the core portion, denoting a as the molar ratio of the total content of Ce, La, Y, and Sc relative to the total content of Ce, La, Y, Sc, Nd, Pr, Gd, Tb, Dy, and Ho, and with respect to the shell portion, denoting b as the molar ratio of the total content of Ce, La, Y, and Sc relative to the total content of Ce, La, Y, Sc, Nd, Pr, Gd, Tb, Dy, and Ho, these satisfy 0≤b≤0.30 and 0≤b/a≤0.50.
<2> The rare earth magnet according to item <1>, wherein b satisfies from 0.09 to 0.27 and b/a satisfies from 0.17 to 0.47.
<3> The rare earth magnet according to item <1> or <2>, wherein z is from 5.6 to 20.0.
<4> A method for producing a rare earth magnet, including:
preparing a rare earth magnet precursor which includes a main phase and a grain boundary phase present around the main phase and in which the overall composition is represented, in terms of molar ratio, by the formula: (R2(1-x)R1x)yFe(100-y-w-z-v)CowBzM1y(wherein R1 is one or more elements selected from the group consisting of Ce, La, Y, and Sc, R2 is one or more elements selected from the group consisting of Nd, Pr, Gd, Tb, Dy, and Ho, M1 is composed of one or more elements selected from the group consisting of Ga, Al, Cu, Au, Ag, Zn, In, and Mn, and unavoidable impurity elements, and 0.1≤x≤1.0, 12.0≤y≤20.0, 5.0≤z≤20.0, 0≤w≤8.0, and 0≤v≤2.0 are satisfied), the main phase has an R2Fe14B-type (wherein R is a rare earth element) crystal structure, the average particle diameter of the main phase is from 1 to 20 μm, and the volume fraction of the main phase is from 90 to 97%,
preparing a modifier having a composition represented, in terms of molar ratio, by the formula: R3(1-p)M2p (wherein R3 is one or more elements selected from the group consisting of Nd, Pr, Gd, Tb, Dy, and Ho, M2 is composed of a transition metal element which is other than a rare earth element and can be alloyed with R3, and unavoidable impurity elements, and 0.05≤p≤0.40), and
bringing q parts by mol (0.1≤q≤15.0) of the modifier into contact with 100 parts by mol of the rare earth magnet precursor to diffuse and infiltrate from 3.7 to 10.0 parts by mol of R3 relative to the total of the rare earth magnet precursor and the modifier (100 parts by mol+q parts by mol) at a temperature of not less than the melting point of the modifier and from 750 to 1,000° C.
<5> The method according to item <4>, wherein from 3.6 to 10.4 parts by mol of the modifier is diffused and infiltrated into 100 parts by mol of the rare earth magnet precursor.
<6> The method according to item <4>, wherein from 3.8 to 7.8 parts by mol of R3 is diffused and infiltrated relative to the total of the rare earth magnet precursor and the modifier (100 parts by mol+q parts by mol).
<7> The method according to any one of items <4> to <6>, wherein
z in the formula representing the composition of the rare earth magnet precursor is from 5.6 to 20.0,
the grain boundary phase of the rare earth magnet precursor contains from 0 to 30.0 vol % of a phase having an R1.1Fe4B4-type crystal structure relative to the entire rare earth magnet precursor, and
the composition of the modifier is represented, in terms of molar ratio, by the formula: R3(1-s-t)FesM3t (wherein M3 is composed of a transition metal element which is other than a rare earth element and can be alloyed with R3 and Fe, and unavoidable impurity elements, and 0.05≤s≤0.30, 0≤t≤0.20, and 0.05≤s+t≤0.40 are satisfied).
<8> The method according to any one of items <4> to <7>, wherein the rare earth magnet after diffusing and infiltrating the modifier into the rare earth magnet precursor is further heat-treated for optimization at 450 to 600° C.
<9> The method according to any one of items <4> to <8>, wherein after the diffusion and infiltration, the rare earth magnet precursor and the modifier are cooled at 0.1 to 10° C./min.
<10> The method according to anyone of items <4> to <8>, wherein after the diffusion and infiltration, the rare earth magnet precursor and the modifier are cooled at 0.1 to 1° C./min.
<11> The method according to anyone of items <4> to <10>, wherein the modifier is diffused and infiltrated into the rare earth magnet precursor at a temperature of not less than the melting point of the modifier and from 850 to 1,000° C.
<12> The method according to anyone of items <4> to <10>, wherein the modifier is diffused and infiltrated into the rare earth magnet precursor at a temperature of not less than the melting point of the modifier and from 900 to 1,000° C.
According to the present disclosure, the R—Fe—B-based rare earth magnet in which the average particle diameter of the main phase including a core portion and a shell portion is from 1 to 20 μm, the shell portion has a predetermined thickness, and the concentration of the light rare earth element in the shell portion is in a predetermined range, can be provided. As a result, the R—Fe—B-based rare earth magnet excellent in both the coercive force and the residual magnetization even in the case of using a light rare earth element for at least part of the rare earth element can be provided.
Furthermore, according to the present disclosure, the modifier is diffused and infiltrated into the rare earth magnet precursor at not less than the predetermined temperature, and the production method of the above-described R—Fe—B-based rare earth magnet excellent in both the coercive force and the residual magnetization can thereby be provided.
The embodiments of the rare earth magnet according to the present disclosure and the production method thereof are described in detail below. Incidentally, the embodiments set forth below should not be construed to limit the rare earth magnet according to the present disclosure and the production method thereof.
Although not bound by theory, with respect to the reason why even in the case of using a light rare earth element for at least part of the rare earth element, an R—Fe—B-based rare earth magnet excellent in both the coercive force and the residual magnetization is obtained, the matters found by the present inventors are described using the drawings.
In order to diffuse and infiltrate a modifier into a rare earth magnet precursor, for example, as illustrated in
When the rare earth magnet precursor 50 and the modifier 60 are heated at a temperature of not less than the melting point of the modifier 60 in the state of being put into contact with each other as illustrated in
With the progress of cooling from the state illustrated in
In the case where the modifier is diffused and infiltrated at a high temperature (see,
Even when the same amount of the modifier 60 is diffused and infiltrated into the rare earth magnet precursor 50, the shell portion 14 is thin (see,
The shell portion 14 is part of the main phase 10, and therefore the shell portion 14 has an R2Fe14B-type crystal structure, and a higher residual magnetization is obtained when R is Nd (Nd2Fe14B) than when R is Ce (Ce2Fe4B). In the shell portion 14, at least part of the light rare earth element (for example, Ce, etc.) before diffusion and infiltration is replaced by the rare earth element (for example, Nd of a Nd—Cu alloy) of the modifier. Accordingly, unless the volume fraction of the shell potion 14 in the main phase 10 becomes excessively large, as the shell portion 14 is thicker, the residual magnetization can be more enhanced. Furthermore, in the shell portion 14, as the concentration of the rare earth element (for example, the concentration of Nd of a Nd—Cu alloy) of the modifier is higher, the residual magnetization can be more enhanced. As understood from these, the residual magnetization can be more enhanced when the modifier is diffused and infiltrated at a high temperature than when diffused and infiltrated at a low temperature.
Regarding the diffusion infiltration temperature, the “low temperature” means a diffusion infiltration temperature at which when the main phase of the rare earth magnet precursor is nanocrystallized, coarsening of the main phase can be substantially avoided. Here, the “nanocrystallized” means that the average particle diameter of the main phase is 1 nm or more and less than 1,000 nm. On the other hand, the “high temperature” means a diffusion infiltration temperature at which when a magnetic rare earth magnet obtained by pressureless sintering is used as a rare earth magnet precursor, coarsening of the main phase can be substantially avoided. The average particle diameter of the main phase of the rare earth magnet obtained by pressureless sintering is from 1 to 20 μm. Details of the diffusion infiltration temperature are described later.
The rare earth magnet of the present disclosure is obtained by diffusing and infiltrating the modifier at a “high temperature”, and therefore it is difficult to use a rare earth magnet precursor having a nanocrystallized main phase (hereinafter, sometimes referred to as “nanocrystalline rare earth magnet precursor”). At the production of the rare earth magnet of the present disclosure, a rare earth magnet precursor with the main phase having an average particle size of 1 to 20 μm (hereinafter, sometimes referred to as “microcrystalline rare earth magnet precursor”) is used. Therefore, in the rare earth magnet of the present disclosure and the production method thereof, the effect of enhancement of residual magnetization due to nanocrystallization of the main phase can hardly be enjoyed. However, the present inventors have found that the residual magnetization can be more enhanced when the modifier is diffused and infiltrated at a “high temperature” into a microcrystalline rare earth magnet precursor, than when the modifier is diffused and infiltrated at a “low temperature” into a nanocrystalline rare earth magnet precursor. As a result, the present inventors have reached the finding that even when a light rare earth element is used for at least part of the rare earth element, an R—Fe—B-based rare earth magnet excellent in both the coercive force and the residual magnetization is obtained.
In addition, with the progress of cooling from the state illustrated in
The configuration requirements of the rare earth magnet according to the present disclosure and the production method thereof, based on these findings, are described below.
First, the configuration requirements of the rare earth magnet according to the present disclosure are described. As illustrated in
The overall composition of the rare earth magnet 100 of the present disclosure is described. The overall composition of the rare earth magnet 100 of the present disclosure means a composition combining all main phases 10 and grain boundary phases 20 in
The overall composition in terms of molar ratio of the rare earth magnet 100 of the present disclosure is represented by the formula: (R2(1-x)R1x)yFe(100-y-w-z-v)CowBzM1v.(R3(1-p)M2p)q. In the formula, (R2(1-x)Rx)yFe(100-y-w-z-v)CowBzM1v represents a composition derived from a rare earth magnet precursor, and (R3(1-p)M2p)q represents a composition derived from a modifier.
The rare earth magnet 100 of the present disclosure is obtained by diffusing and infiltrating a modifier having a composition represented by the formula: R3(1-p)M2p into the inside of a rare earth magnet precursor having a composition represented by the formula: (R2(1-x)R1x)yFe(100-y-w-z-v)CowBzM1v. When q parts by mol of a modifier is diffused and infiltrated into the inside of 100 parts by mol of a rare earth magnet precursor, the volume of the rare earth magnet after diffusing and infiltrating the modifier into the rare earth magnet precursor is (100+q) parts by mol. The formula above shows this, and since the total of R1 and R2 is y parts by mol, Fe is (100-y-w-z-v) parts by mol, Co is w parts by mol, B is z parts by mol, and M1 is v parts by mol, the total of these is y parts by mol+(100-y-w-z-v) parts by mol+w parts by mol+z parts by mol+v parts by mol=100 parts by mol. The total of R3 and M2 is p parts by mol.
In the formula above, R2(1-x)R1x means that in terms or molar ratio, (1-x)R2 and xR1 are present relative to the total of R2 and R3. Similarly, in the formula above, R3(1-p)M2p means that in terms of molar ratio, (1-p)R3 and pM3 are present relative to the total of R3 and M3.
In the formula above, R1 is one or more elements selected from the group consisting of Ce, La, Y, and Sc. Ce is cerium, La is lanthanum, Y is yttrium, and Sc is scandium. Each of R2 and R3 is one or more elements selected from the group consisting of Nd, Pr, Gd, Tb, Dy, and Ho. Nd is neodymium, Pr is praseodymium, Gd is gadolinium, Tb is terbium, Dy is dysprosium, and Ho is holmium. Fe is iron, Co is cobalt, and B is boron. M1 is composed of one or more elements selected from the group consisting of Ga, Al, Cu, Au, Ag, Zn, In, and Mn, and unavoidable impurity elements. Ga is gallium, Al is aluminum, Cu is copper, Au is gold, Ag is silver, Zn is zinc, In is indium, and Mn is manganese. M2 is composed of a transition metal element which is other than a rare earth element and can be alloyed with R3, and unavoidable impurity elements.
In the present description, the rare earth element consists of 17 elements of Sc, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu. Among these, Sc, Y, La, and Ce are light rare earth elements. Pr, Nd, Pm, Sm, Eu, and Gd are medium rare earth elements. Tb, Dy, Ho, Er, Tm, Yb, and Lu are heavy rare earth elements. Incidentally, in general, the rarity of the heavy rare earth element is high, and the rarity of the light rare earth element is low. The rarity of the medium rare earth element is between the heavy rare earth element and the light rare earth element.
The constituent elements of the rare earth magnet of the present disclosure, represented by the formula above, is described below.
R1 is an essential component for the rare earth magnet of the present disclosure. As described above, R1 is one or more elements selected from the group consisting of Ce, La, Y, and Sc and belongs to the light rare earth element. R1 is an element constituting the main phase (R2Fe14B phase). At least part of R1 in the vicinity of the surface layer part of the main phase is replaced by R3 in the modifier, and the main phase can thereby have a core portion and a shell portion.
As described above, R2 is one or more elements selected from the group consisting of Nd, Pr, Gd, Tb, Dy, and Ho and belongs to the rare earth element other than the light rare earth element. Nd, Pr, and Gd belong to the medium rare earth element, and Tb, Dy, and Ho belong to the heavy rare earth element. In other words, R2 belongs to the medium rare earth element and/or the heavy rare earth element. In the rare earth magnet of the present disclosure, in view of the balance between the performance and cost, it is preferable to increase the contents of Nd and Pr, and it is more preferable to increase the content of Nd. In the case where Nd and Pr are caused to coexist as R1, didymium may be used. R2 is an element constituting the main phase (R2Fe14B phase).
<Molar Ratios of R1 and R2>
In the rare earth magnet of the present disclosure, R1 and R2 are elements derived from a rare earth magnet precursor. Relative to the total of R1 and R2, in terms of molar ratio, xR1 is present, and (1-x)R2 is present, wherein 0.1≤x≤1.0.
As illustrated in
In the R2Fe14B phase (main phase), the anisotropic magnetic field (coercive force) and the residual magnetization are higher when the rare earth element other than the light rare earth element is contained as R in a larger amount than the light rare earth element. R1 (light rare earth element) and R2 (rare earth element other than light rare earth element) are derived from the rare earth magnet precursor. By diffusing and infiltrating the modifier into the rare earth magnet precursor, in the portion near the surface layer part of the main phase 10, at least part of R1 (light rare earth element) of the rare earth magnet precursor is replaced by R3 (rare earth element other than light rare earth element) of the modifier, whereby a shell portion 14 is formed. In the case where the main phase has a core portion 12 and a shell portion 14, the anisotropic magnetic field (coercive force) and residual magnetic field of the rare earth magnet as a whole can be efficiently enhanced by enhancing the anisotropic magnetic field (coercive force) and residual magnetization in the shell portion 14 than in the core portion 12. This implies that even when all are an inexpensive R1 (light rare earth element) in the core portion 12, it is sufficient if R1 (light rare earth element) is replaced by R3 (rare earth element other than light rare earth element) in the shell portion 14.
<Total Content Ratio of R1 and R2>
In the formula above, the total content ratio of R1 and R2 is represented by y and satisfies 12.0≤y≤20.0. Here, the value of y is a content ratio relative to the rare earth magnet precursor and corresponds to at %.
When y is 12.0 or more, in the rare earth magnet precursor, a large amount of αFe phase cannot be present, and a sufficient amount of main phase (R2Fe14B phase) can be obtained. From this viewpoint, y may be 12.4 or more, 12.8 or more, or 13.2 or more. On the other hand, when y is 20.0 or less, the grain boundary phase cannot be excessive. From this viewpoint, y may be 19.0 or less, 18.0 or less, or 17.0 or less.
B constitutes the main phase 10 (R2Fe14B phase) as illustrated in
The content ratio of B is represented by z in the formula above. The value of z is a content ratio relative to a rare earth magnet precursor and corresponds to at %. When z is 20.0 or less, a rare earth magnet where the main phase 10 and the grain boundary phase 20 are properly present can be obtained. From this viewpoint, z may be 18.0 or less, 16.0 or less, 14.0 or less, 12.0 or less, 10.0 or less, or 8.0 or less. On the other hand, when z is 5.0 or more, generation of a large amount of a phase having Th2Zn17 and/or Th2Ni17-type crystal structures hardly occurs, as a result, the formation of R2Fe14B is less inhibited. In addition, when z is 5.6 or more, the R1.1Fe4B4 phase is likely to be produced as the triple point 22 in the grain boundary phase 20. From this viewpoint, z may be 5.8 or more, 6.0 or more, 6.2 or more, 6.4 or more, 6.6 or more, 6.8 or more, or 7.0 or more. When many R1.1Fe4B4 phases are formed as the triple point 22 in the grain boundary phase 20 and a Fe-containing modifier is diffused and infiltrated, R1.1Fe4B4 is changed to R2Fe14B phase due to Fe of the modifier, and the volume fraction of the main phase increases, as a result, the residual magnetization is further enhanced.
Co is an element capable of being replaced by Fe in the main phase and the grain boundary phase. In the present description, when Fe is referred to, this means that part of Fe can be replaced by Co. For example, part of Fe of the R2Fe14B phase is replaced by Co to form a R2(Fe, Co)14B phase. In addition, for example, part of Fe of the R1.1Fe4B4 phase in the grain boundary phase is replaced by Co to form R1.1(Fe, Co)4B4.
The R2Fe14B phase is changed to R2(Fe, Co)14B phase due to replacing of part of Fe by Co, and in turn, the Curie point of the rare earth magnet of the present disclosure increases. In addition, when a Fe-containing modifier is diffused and infiltrated, the R1.1(Fe, Co)4B4 phase changes to R2(Fe, Co)14B phase, and therefore the Curie point of the rare earth magnet of the present disclosure increases. In the case of not desiring the increase of the Curie point, Co may not be contained, and it is not mandatory to contain Co.
In the formula above, the content ratio of Co is represented by w. The value of w is a content ratio relative to the rare earth magnet precursor and corresponds to at %. When w is 0.5 or more, an increase of the Curie point is substantially recognized. From the viewpoint of increasing the Curie point, w may be 1.0 or more, 2.0 or more, 3.0 or more, or 4.0 or more. On the other hand, since Co is expensive, from the economical viewpoint, w may be 30.0 or less, 25.0 or less, 20.0 or less, 10.0 or less, 8.0 or less, 7.0 or less, or 6.0 or less.
M1 can be contained to an extent of not impairing the properties of the rare earth magnet of the present disclosure. M1 may contain unavoidable impurity elements. In the present description, the unavoidable impurity elements indicates impurity elements that is inevitably contained or causes a significant rise in the production cost for avoiding its inclusion, such as impurity elements contained in raw materials of the rare earth magnet or impurity elements having mixed in the production step. The impurity elements, etc. that mixes in the production step encompasses an element that is contained to an extent of not affecting the magnetic properties for the reason of production convenience, and the unavoidable impurity elements encompasses an element that is an element other than the rare earth element selected as R1 and R2 and inevitably mixes for the above-described reasons.
The element that can be contained to an extent of not impairing the effects of the rare earth magnet of the present disclosure and the production method thereof includes Ga, Al, Cu, Au, Ag, Zn, In, and Mn. As long as the amount in which these elements are present is not more than the upper limit of the content of M1, the elements have substantially no influence on the magnetic properties. Accordingly, the elements above may be treated as equivalent to unavoidable impurity elements. Furthermore, besides these elements, unavoidable impurity elements can be contained as M1,
In the formula above, the content ratio of M1 is represented by v. The value of v is a content ratio relative to the rare earth magnet precursor and corresponds to at %. When the value of v is 2.0 or less, the magnetic properties of the present disclosure are not impaired. From this viewpoint, v may be 1.5 or less, 1.0 or less, or 0.5 or less.
Ga, Al, Cu, Au, Ag, Zn, In, Mn, and unavoidable impurity elements, as M1, cannot be made zero, and therefore, even if the lower limit of v is 0.05, 0.1, or 0.2, there is no practical problem.
Fe is the remainder excluding hereinbefore-described R1, R2, Co, B, and M1, and the content ratio of Fe is represented by (100-y-w-z-v). When y, w, z, and v are in the ranges described above, as illustrated in
R3 is an element derived from the modifier. As illustrated in
R3 is one or more elements selected from the group consisting of Nd, Pr, Gd, Tb, Dy, and Ho and is a rare earth element (a medium rare earth element and a heavy rare earth element) other than the light rare earth element. As described above, at least part of R1 (light rare-earth element) in the vicinity of the surface layer part of the main phase 10 is replaced by R3 (a rare earth element other than the light rare earth element) of the modifier 60, and the concentration of the rare earth element other than the light rare earth element in the shell portion 14 increases. As a result, the anisotropic magnetic field (coercive force) and residual magnetization of the rare earth magnet 100 of the present disclosure are enhanced.
M2 is composed of a transition metal element which is other than a rare earth element and can be alloyed with R3, and unavoidable impurity elements. Typically, M2 is composed of an alloy element which reduce the melting point of R3(1-p)M2p to be lower than the melting point of R3, and unavoidable impurity elements. M2 includes, for example, one or more elements selected from Cu, Al, Co, and Fe, and unavoidable impurity elements. M2 is preferably one or more elements selected from Cu, Al, and Fe. Furthermore, as described above, compared with the case where M2 does not contain Fe (see,
<Molar Ratio of R3 and M2>
R3 and M2 form an alloy having a composition represented, in terms of molar ratio, by the formula: R3(1-p)M2p, and the modifier contains this alloy, wherein p satisfies 0.05≤p≤0.40.
When p is 0.05 or more, a melt of the modifier 60 can be diffused and infiltrate into the inside of the rare earth magnet precursor 50 at a temperature where coarsening of the main phase 10 of the rare earth magnet precursor 50 can be avoided. From this viewpoint, p is preferably 0.07 or more, more preferably 0.09 or more. On the other hand, when p is 0.40 or less, the content of M2 remaining in the grain boundary phase 20 of the rare earth magnet 100 of the present disclosure after diffusing and infiltrating the modifier 60 into the rare earth magnet precursor 50 is reduced, and this contributes to the enhancement of residual magnetization. From this viewpoint, p may be 0.35 or less, 0.30 or less, 0.25 or less, 0.20 or less, or 0.15 or less.
M2 may or may not contain Fe, but, as described above, M2 preferably contains Fe. In the case where M2 contains Fe, for the sake of convenience, M2 other than Fe may be rewritten as M3, and R3(1-p)M2p in the formula above may be rewritten as R3(1-s-t)FesM3t. At this time, M3 is composed of a transition metal element other than a rare earth element and Fe which can be with R3, and unavoidable impurity elements, and 0.05≤s≤0.30, 0≤t≤0.20, and 0.05≤s+t≤0.40 are satisfied. s and t are described in detail in “«Production Method»”.
Typically, M3 is composed of an alloy element, which reduce the melting point of R3(1-s-t)FesM3t to be lower than the melting points of R3 and Fe, and unavoidable impurity elements. M3 includes, for example, one or more elements selected from Cu, Al, Ga and Co.
<Molar Ratios of Element Derived from Rare Earth Magnet Precursor and Element Derived from Modifier>
In the formula above, the ratio of the modifier 60 relative to 100 parts by mol of the rare earth magnet precursor 50 is q parts by mol. More specifically, when q parts by mol of the modifier 60 is diffused and infiltrated into 100 parts by mol of the rare earth magnet precursor 50, this gives 100 parts by mol+q parts by mol of the rare earth magnet 100 of the present disclosure. Accordingly, assuming the total content of the elements derived from the rare earth magnet precursor is 100 parts by mol, q is the molar ratio of the content of the element derived from the modifier. In other words, the rare earth magnet 100 of the present disclosure is (100+q) at % relative to 100 at % of the rare earth magnet precursor 50.
When q is 0.1 or more, at least part of R1 (light rare earth element) of the main phase 10 of the rare earth magnet precursor 50 can be replaced by R3 (a rare earth element other than a light rare earth element) of the modifier 60 and in turn, the shell portion 14 can be formed. As a result, the anisotropic magnetic field (coercive force) and residual magnetization of the rare earth magnet 100 of the present disclosure can be enhanced. From this viewpoint, q may be 0.5 or more, 1.0 or more, 1.5 or more, 2.0 or more, 2.5 or more, 3.0 or more, or 3.6 or more. On the other hand, when q is 15.0 or less, the content of M2 remaining in the grain boundary phase 20 of the rare earth magnet 100 of the present disclosure is reduced, and this contributes to the enhancement of residual magnetization. From this viewpoint, q may be 14.0 or less, 13.0 or less, 12.0 or less, 11.0 or less, 10.4 or less, 10.0 or less, 9.5 or less, 9.0 or less, 8.5 or less, 8.0 or less, 7.5 or less, 7.0 or less, or 6.5 or less.
The rare earth magnet 100 of the present disclosure includes a main phase 10 and a grain boundary phase 20. The main phase 10 has a core portion 12 and a shell portion 14. The main phase 10 and the grain boundary phase 20 are described below. With respect to the main phase 10, the core portion 12 and the shell portion 14 are also described.
The main phase 10 has a R2Fe14B-type crystal structure. R is a rare earth element. The reason why the crystal structure is expressed as R2Fe14B “-type” is because in the main phase 10 (in the crystal structure), elements other than R, Fe and B can be contained in a substitution-type and/or interstitial-type manner. For example, in the main phase 10, part of Fe may be replaced by Co, or in the main phase 10, part of any one element of R, Fe and B may be replaced by M1. Alternatively, for example, M1 may be present as an interstitial-type element in the main phase 10.
The average particle diameter of the main phase 10 is from 1 to 20 μm. In the case where the average particle diameter of the main phase 10 is 1 μm or more, even when a modifier is diffused and infiltrated at a high temperature, coarsening of the main phase 10 can be substantially avoided. From this viewpoint, the average particle diameter of the main phase may be 1.1 μm or more, 1.2 μm or more, 1.3 μm or more, 1.4 μm or more, 1.5 μm or more, 1.6 μm or more, 1.7 μm or more, 1.8 μm or more, 1.9 μm or more, 2.0 μm or more, 2.2 μm or more, or 2.4 μm or more. When the average particle diameter of the main phase 10 is 20 μm or less, a phenomenon that desired residual magnetization and/or coercive force cannot be obtained due to the particle diameter of the main phase 10 does not occur. From this viewpoint, the average particle diameter of the main phase 10 may be 18 μm or less, 16 μm or less, 14 μm or less, 12 μm or less, 10 μm or less, 9 μm or less, 8 μm or less, 7 μm or less, 6 μm or less, 5 μm or less, or 4 μm or less.
The “average particle diameter” is an average of maximum lengths of the main phases 10. The “average of maximum lengths” means an average of maximum lengths of respective main phases 10 present in a certain area after defining the certain area in a scanning electron microscope image or a transmission electron microscope image. For example, when the cross section of the main phase 10 is elliptical, the length of the major axis is the maximum length. For example, when the cross section of the main phase 10 is quadrangular, the length of a longer diagonal line is the maximum length. In addition, since the main phase 10 of the rare earth magnet 100 of the present disclosure has a core portion 12 and a shell portion 14, the maximum length of the main phase 10 is a maximum length including the shell portion 14. For example, as illustrated in
As illustrated in
The anisotropic magnetic field (coercive force) and the residual magnetization of the rare earth magnet 100 as a whole of the present disclosure can be increased by more increasing the anisotropic magnetic field (coercive force) and residual magnetization in the shell portion 14 than in the core portion 12. In addition, a rare earth element (for example, Nd, etc.) of the modifier other than a light rare earth element is diffused and infiltrated into the shell portion 14, and this is advantageous for enhancing the anisotropic magnetic field (coercive force) and the residual magnetization. Accordingly, as long as the volume fraction of the shell portion 14 in the main phase 10 does not become excessive, the shell portion 14 preferably has a larger thickness. When the thickness of the shell portion 14 is 25 nm or more, the rare earth magnet 100 of the present disclosure can have desired anisotropic magnetic field (coercive force) and residual magnetization. From this viewpoint, the thickness of the shell portion 14 may be 30 nm or more, 35 nm or more, 40 nm or more, 45 nm or more, 50 nm or more, 55 nm or more, 60 nm or more, 65 nm or more, 70 nm or more, 75 nm or more, 80 nm or more, 85 nm or more, or 90 nm or more. On the other hand, when the thickness of the shell portion 14 is 150 nm or less, the volume fraction of the shell portion 14 in the main phase is kept from becoming excessively large. From this viewpoint, the thickness of the shell portion 14 may be 140 nm or less, 130 nm or less, 120 nm or less, 125 nm or less, 120 nm or less, 115 nm or less, 110 nm or less, 105 nm or less, 100 nm or less, or 95 nm or less.
The thickness of the shell portion 14 means the distance between the outer circumference of the core portion 12 and the inner circumference of the shell portion 14. With respect to the method for measuring the thickness of the shell portion 14, after a certain area is defined, the distance above is measured in each of main phases 10 present in the certain area by using a scanning electron microscope or a transmission electron microscope, and the thickness is determined by averaging respective distances.
In order to more increase the anisotropic magnetic field (coercive force) and residual magnetization in the shell portion 14 than in the core portion 12, the concentration of the light rare earth element is more reduced (the concentration of the rare earth element other than the light rare earth element is more increased) in the shell portion 14 than in the core portion 12. For realizing this, the following indices should be satisfied.
With respect to the core portion 12, the molar ratio of the total content of Ce, La, Y, and Sc (the content of the light rare earth element) relative to the total content of Ce, La, Y, Sc, Nd, Pr, Gd, Tb, Dy, and Ho (the total of the content of the light rare earth element and the content of the rare earth element other than the light rare earth element) is denoted by a. In addition, with respect to the shell portion 14, the molar ratio of the total content of Ce, La, Y, and Sc (the content of the light rare earth element) relative to the total content of Ce, La, Y, Sc, Nd, Pr, Gd, Tb, Dy, and Ho (the total of the content of the light rare earth element and the content of the rare earth element other than the light rare earth element) is denoted by b. At this time, these satisfy 0≤b≤0.30 and 0≤b/a≤0.50.
b represents the molar ratio of the content of the light rare earth element relative to the content of all rare earth elements in the shell portion 14. When b is 0.30 or less, the concentration of the light rare earth element in the shell portion 14 is low (the concentration of the rare earth element other than the light rare earth element is high), and this is advantageous for enhancing the anisotropic magnetic field (coercive force) and the residual magnetization. b is preferably lower and may be 0. From this viewpoint, b may be 0.27 or less, 0.25 or less, 0.20 or less, 0.15 or less, 0.12 or less, or 0.10 or less.
When all light rare earth elements of the main phase 10 before diffusion and infiltration (the rare earth magnet precursor 50) are replaced by the rare earth element of the modifier other than the light rare earth element, b becomes 0. However, even if all are not replaced, there is practically no problem in enhancement of the anisotropic magnetic field (coercive force) and the residual magnetization. From this viewpoint, b may be 0.01 or more, 0.03 or more, 0.05 or more, 0.07 or more, or 0.09 or more.
When the molar ratio of the content of the light rare earth element to the content of all rare earth elements (hereinafter, sometimes simply referred to as “ratio of light rare earth element”) is low in both the core portion 12 and the shell portion 14, this is advantageous for enhancing the anisotropic magnetic field (coercive force) and the residual magnetization. In other words, when the molar ratio of the content of the rare earth element other than the light rare earth element to the content of all rare earth elements (hereinafter, sometimes simply referred to as “ratio of rare earth element other than light rare earth element”) is high in both the core portion 12 and the shell portion, this is advantageous for enhancing the anisotropic magnetic field (coercive force) and the residual magnetization.
It is advantageous for enhancing the anisotropic magnetic field (coercive force) and residual magnetization of the rare earth magnet 100 as a whole of the present disclosure to more enhance the anisotropic magnetic field (coercive force) and residual magnetization in the shell portion 14 than in the core portion 12. Accordingly, it is preferable to more reduce the ratio of the light rare earth element in the shell portion 14 than in the core portion 12, and b (ratio of light rare earth element in the shell portion 14)/a (ratio of light rare earth element in the core portion 12) is preferably smaller and may be 0. From this viewpoint, b/a may be 0.50 or less, 0.47 or less, 0.44 or less, 0.41 or less, 0.38 or less, 0.35 or less, 0.32 or less, 0.25 or less, 0.20 or less, or 0.15 or less.
On the other hand, b/a being 0 means that b is 0, i.e., in the shell portion 14, all rare earth elements are replaced by a rare earth element of the modifier other than the light rare earth element. However, even if all are not replaced, the enhancement of anisotropic magnetic field (coercive force) and residual magnetization is substantially recognized. From this viewpoint, it may be 0.01 or more, 0.03 or more, 0.05 or more, 0.07 or more, 0.09 or more, 0.10 or more, or 0.13 or more.
Incidentally, regarding the above-described “with respect to the core portion 12, the molar ratio of the total content of Ce, La, Y, and Sc relative to the total content of Ce, La, Y, Sc, Nd, Pr, Gd, Tb, Dy, and Ho is denoted by a”, and “with respect to the shell portion 14, the molar ratio of the total content of Ce, La, Y, and Sc relative to the total content of Ce, La, Y, Sc, Nd, Pr, Gd, Tb, Dy, and Ho is denoted by b”, a supplementary explanation is given below
Since the modifier does not diffuse and infiltrate into the core portion 12, all of Ce, La, Y, Sc, Nd, Pr, Gd, Tb, Dy, and Ho in the core portion 12 are derived from the rare earth element of the rare earth magnet precursor, that is, R1 and R2. On the other hand, since the modifier diffuses and infiltrates into the shell portion 14, Ce, La, Y, Sc, Nd, Pr, Gd, Tb, Dy, and Ho in the shell portion 14 are derived from the rare earth elements of the rare earth magnet precursor 50 and the modifier 60, that is, R1, R2, and R3. However, in the shell portion 14, as concerns Nd, Pr, Gd, Tb, Dy, and Ho, the element derived from R2 and the element derived from R3 cannot be actually distinguished as “a material”. For this reason, R1 and R2 as well as R3 are not used when defining a, b and b/a.
Incidentally, a and b are determined based on the results of component analysis performed using Cs-STEM-EDX (Corrector-Spherical Aberration-Scanning Transmission Electron Microscope-Energy Dispersive X-ray Spectrometry). Because, it is not easy to separately observe the core portion 12 and the shell portion 14 by SEM-EDX (Scanning Electron Microscope-Energy Dispersive X-ray Spectrometry).
As illustrated in
The crystal boundary phase 20 has an indistinct crystal structure but has a composition in which the content ratio of R in the grain boundary phase 20 as a whole is higher than in the main phase 10 (R2Fe14B phase). Accordingly, the grain boundary phase 20 is sometimes referred to as “R-rich phase”, “rare earth element-rich phase”, or “rare earth-rich phase”.
The grain boundary phase 20 may have an R1.1Fe4B4 phase as the triple point 22. The triple point 22 corresponds to the solidified portion in the cooling step at the production of the rare earth magnet precursor 50, and the solidified portion may be an R1.1Fe4B4 phase. The R1.1Fe4B4 phase scarcely contributes to the anisotropic magnetic field (coercive force) and residual magnetization of the rare earth magnet 100 of the present disclosure. Therefore, it is preferred that, as described above, the R1.1Fe4B4 phase is changed to an R2Fe14B phase by Fe in the modifier 60 to constitute part of the main phase 10.
The production method of the rare earth magnet of the present disclosure is described below.
A rare earth magnet precursor 50 having an overall composition represented, in terms of molar ratio, by the formula: (R2(1-x)Rx)yFe(100-y-w-z-v)CowBzM1v is prepared. In the formula representing the overall composition of the rare earth magnet precursor 50, R1, R2, Fe, Co, B, M1, x, y, z, w, and v are as described in “«Rare Earth Magnet»”.
As illustrated in
In the production method of the rare earth magnet of the present disclosure (hereinafter, sometimes referred to as “production method of the present disclosure”), a modifier 60 is diffused and infiltrated into the rare earth magnet precursor 50 at such a “high temperature” as not to allow for coarsening of the main phase of the rare earth magnet precursor 50. Accordingly, the average particle diameter of the main phase 10 of the rare earth magnet precursor 50 and the average particle diameter of the main phase of the rare earth magnet 100 of the present disclosure are sizes substantially in the same range. Then, the average particle diameter of the main phase 10 of the rare earth magnet precursor 50 is as described in the “Rare Earth Magnet”. Incidentally, for the sake of convenience, the main phase 10 of the rare earth magnet precursor 50 may be referred to as the precursor main phase.
The grain boundary phase 20 of the rare earth magnet precursor 50 does not contain elements derived from the modifier 60, but, as with the rare earth magnet 100 of the present disclosure, the grain boundary phase 20 contains a phase whose crystal structure is indistinct, excluding the triple point 22. In addition, as with the rare earth magnet 100 of the present disclosure, the grain boundary phase 20 of the rare earth magnet precursor 50 may contain an R1.1Fe4B4 phase as the triple point 22. Incidentally, for the sake of convenience, the main phase 10 of the rare earth magnet precursor 50 may be referred to as the precursor grain boundary phase.
Anisotropy may be imparted to the rare earth magnet precursor 50 for use in the production method of the present disclosure. For the sake of convenience, this rare earth magnet precursor 50 may be referred to as “anisotropic rare earth magnet precursor”.
For the rare earth magnet precursor 50 used in the production method of the present disclosure, a conventional method for producing a rare earth sintered magnet can be used. In general, the rare earth sintered magnet means a rare earth magnet obtained by cooling a molten metal having a composition capable of giving an R2Fe14B phase at such a rate as to reduce the size of the main phase to a micro level, thereby obtaining a magnetic powder, and subjecting a green compact of the magnetic powder to pressureless high temperature sintering. The magnetic powder may be compacted in a magnetic field (molding in a magnetic field) to impart anisotropy to the rare earth magnet after sintering (rare earth sintered magnet).
On the other hand, the nanocrystallized rare earth magnet generally means a rare earth magnet obtained by cooling a molten metal having a composition capable of giving an R2Fe14B phase at such a rate as to nanocrystallize the main phase, thereby obtaining a magnetic powder, and subjecting the magnetic powder to low-temperature pressure sintering (low-temperature hot pressing). The nanocrystallized main phase may also be obtained by heat-treating an amorphous phase. Since it is difficult to orient the nanocrystallized magnetic powder by the molding in a magnetic field, the magnetic powder is oriented by subjecting a sintered body obtained by low-temperature pressure sintering to hot plastic working. Such a magnet is referred to as a hot plastic worked rare earth magnet.
In the production method of the present disclosure, a modifier 60 is diffused and infiltrated into the rare earth magnet precursor 50 at a high temperature. The “high temperature” is a temperature at which the nanocrystallized main phase is coarsened, and therefore a rare earth magnet precursor having a nanocrystallized main phase cannot be used in the production method of the present disclosure. In addition, when a modifier is diffused and infiltrated at a “high temperature” referred to in the production method of the present disclosure into a rare earth magnet precursor having a nanocrystallized main phase, in addition to coarsening of the main phase, formation of a core/shell structure of the main phase is also inhibited. As a result, the effects of the production method of the present disclosure are not obtained.
Preparation of the rare earth magnet precursor in the production method of the present disclosure may be performed, for example, as follows, but the preparation is not limited thereto.
A molten metal represented, in terms of molar ratio, by the formula: (R2(1-x)R1x)yFe(100-y-w-z-v)CowBzM1v is cooled at a such a rate as to give an average particle diameter of 1 to 20 μm to the main phase (R2Fe14B phase), and a magnetic ribbon is thereby obtained. This cooling rate is, for example, from 1 to 1,000° C./s. In addition, the method for obtaining a magnetic powder at such a cooling rate includes, for example, a strip casting method, a book molding method, etc. The composition of the molten metal is fundamentally the same as the overall composition of the rare earth magnet precursor, but as for the element that may be consumed in the process of producing the rare earth magnet precursor, the overall composition can be made up in consideration of the consumption.
A magnetic powder obtained by pulverizing a magnetic ribbon obtained as above is compacted. The powder compacting may be performed in a magnetic field. The molding pressure during powder compacting may be, for example, 50 MPa or more, 100 MPa or more, 200 MPa or more, or 300 MPa or more, and may be 1000 MPa or less, 800 MPa or less, or 600 MPa or less. The magnetic field applied may be 0.1 T or more, 0.5 T or more, 1 T or more, 1.5 T or more, or 2.0 T or more, and may be 10.0 T or less, 8.0 T or less, 6.0 T or less, or 4.0 T or less. The pulverization method includes, for example, a method where the magnetic ribbon is coarsely pulverized and then further pulverized by means of a jet mill, etc. The method for coarse pulverization includes, for example, a method using a hammer mill, a method where the magnetic ribbon is embrittled by hydrogen, and a combination thereof, etc.
The thus-obtained green compact is subjected to pressureless sintering to obtain a rare earth magnet precursor. In order to sinter the green compact without applying a pressure and thereby increase the density of the sintered body, the green compact is sintered at a high temperature over a long period of time. The sintering temperature may be, for example, 900° C. or more, 950° C. or more, or 1,000° C. or more, and may be 1,100° C. or less, 1,050° C. or less, or 1,040° C. or less. The sintering time may be, for example, 1 hour or more, 2 hours or more, 3 hours or more, or 4 hours or more, and may be 24 hours or less, 18 hours or less, 12 hours or less, or 6 hours or less. In order to suppress oxidation of the green compact during sintering, the sintering atmosphere is preferably an inert gas atmosphere. The inert gas atmosphere includes a nitrogen gas atmosphere.
With respect to the main phase 10 of the rare earth magnet precursor 50, the volume fraction of the main phase 10 relative to the rare earth magnet precursor 50 can be controlled by appropriately changing, for example, the total content ratio y of R1 and R2, the content ratio z of B, or the cooling rate at the production of the rare earth magnet precursor 50.
In the rare earth magnet precursor 50, as long as the volume fraction of the main phase 10 is not excessively increased to excessively decrease the volume fraction of the grain boundary phase 20, the volume fraction of the main phase 10 is preferably higher. When the volume fraction of the main phase 10 of the rare earth magnet precursor 50 is high, the volume fraction of the main phase 10 of the rare earth magnet 100 of the present disclosure is also increased, and this contributes to enhancement of the residual magnetization.
On the other hand, if the volume fraction of the main phase 10 of the rare earth magnet precursor 50 is excessively increased and the volume fraction of the grain boundary phase 20 is excessively decreased, although not bound by theory, the modifier 60 may diffuse and infiltrate into the grain boundary phase 20, but the shell portion 14 is not formed. As a result, in the rare earth magnet 100 of the present disclosure, both the anisotropic magnetic field (coercive force) and the residual magnetization are significantly reduced.
From the viewpoint of contributing the enhancement of the residual magnetization, the volume fraction of the main phase 10 of the rare earth magnet precursor 50 may be 90.0% or more, 90.5% or more, 91.0% or more, 92.0% or more, 94.0% or more, or 95.0% or more. On the other hand, from the viewpoint of preventing the volume fraction of the main phase 10 of the rare earth magnet precursor 50 from excessively increasing, the volume fraction of the main phase 10 of the rare earth magnet precursor 50 may be 97.0% or less, 96.5% or less, or 95.9% or less.
A modifier having a composition represented, in terms of molar ratio, by the formula: R3(1-p)M2p is prepared. In the formula representing the composition of the modifier, R3, M2 and p are as described in “«Rare Earth Magnet»”.
The method for preparing the modifier includes, for example, a method where a molten metal having the composition of the modifier is formed using a liquid quenching method or a strip casting method, etc. to obtain a ribbon, etc. In this method, the molten metal is quenched, and therefore segregation is less likely to occur in the modifier. In addition, the method for preparing the modifier includes, for example, a method where a molten metal having the composition of the modifier is cast in a casting mold such as book mold. In this method, a large amount of modifier is relatively easily obtained. In order to decrease the segregation of the modifier, the book mold is preferably made of a material having a high thermal conductivity. Furthermore, the casting material is preferably heat-treated for homogenization so as to suppress segregation. Moreover, the method for preparing the modifier includes a method where raw materials of the modifier are loaded into a container, the raw materials are arc-melted, and the melted product is cooled to obtain an ingot. In this method, even when the melting point of the raw material is high, the modifier can relatively easily be obtained. From the viewpoint of reducing segregation of the modifier, the ingot is preferably heat-treated for homogenization.
A modifier is diffused and infiltrated into the rare earth magnet precursor at a temperature of not less than the melting point of the modifier and from 750 to 1,000° C.
As illustrated in
In the case where the melting point of the modifier 60 is less than 750° C., when the modifier 60 is diffused and infiltrated into the rare earth magnet precursor 50 at a temperature of not less than the melting point of the modifier 60 and less than 750° C., the melt 62 of the modifier 60 only diffuses and infiltrates into the grain boundary phase 20, and a shell portion 14 having a sufficient Nd concentration is not formed. For example, in the case of using a Nd0.7Cu0.3 alloy as the modifier 60, the melting point of the Nd0.7Cu0.3 alloy is 520° C. When the diffusion and infiltration temperature is 650° C., the melt 62 of the Nd0.7Cu0.3 alloy diffuses and infiltrates into the grain boundary phase 20 but fails in forming a shell portion 14.
As long as the main phase 10 of the rare earth magnet precursor 50 is not coarsened during diffusion and infiltration of the modifier 60, the diffusion and infiltration temperature is preferably higher for forming a predetermined shell portion 14. When the diffusion and infiltration temperature is 1,000° C. or less, coarsening of the main phase 10 of the rare earth magnet precursor 50 can be suppressed. For this reason, the modifier 60 is diffused and infiltrated at a temperature of not less than the melting point of the modifier 60 and from 750 to 1,000° C. As long as the temperature is not less than the melting point of the modifier 60, the lower limit of the diffusion and infiltration temperature may be 800° C., 850° C., or 900° C. In addition, as long as the temperature is not less than the melting point of the modifier, the upper limit of the diffusion and infiltration temperature may be 975° C. or 950° C.
At the time of diffusion and infiltration of the modifier 60, relative to 100 parts by mol of the rare earth magnet precursor 50, from 0.1 to 15.0 parts by mol of the modifier 60 is brought into contact with the rare earth magnet precursor 50. When 0.1 parts by mol or more, 2.0 parts by mol or more, 3.0 parts by mol or more, 3.6 parts by mol or more, or 4.0 parts by mol or more of the modifier 60 is diffused and infiltrated by bringing it into contact with the rare earth magnet precursor 50, formation of the shell portion 14 can be substantially recognized. On the other hand, when 15.0 parts by mol or less, 14.0 parts by mol or less, 12.0 parts by mol or less, 10.4 parts by mol or less, 10.0 parts by mol or less, 8.0 parts by mol or less, or 6.0 parts by mol or less of the modifier 60 is diffused and infiltrated by bringing it into contact with the rare earth magnet precursor 50, the amount of M2 remaining in the grain boundary phase 20 can be decreased, and the reduction in the residual magnetization can be suppressed.
After the ratio of the modifier 60 brought into contact with the rare earth magnet precursor 50 is set as above, the composition of the modifier 60 is appropriately determined to set the above-described b and b/a to fall in predetermined ranges. For this purpose, when the diffusion and infiltration ratio of R3 of the modifier 60 relative to the total of the rare earth magnet precursor 50 and the modifier 60 (100 parts by mol+q parts by mol) is 3.7 parts by mol or more, predetermined b and b/a are obtained. From this viewpoint, the diffusion and infiltration ratio of R3 of the modifier 60 may be 3.8 parts by mol or more, 4.0 parts by mol or more, 4.6 parts by mol or more, 5.2 parts by mol or more, or 5.8 parts by mol or more. On the other hand, when the diffusion and infiltration ratio of R3 of the modifier 60 is 10.0 parts by mol or less, predetermined b and b/a are obtained, and the enhancement of the anisotropic magnetic field (coercive force) and residual magnetization is saturated, nevertheless, it is less likely that the modifier 60 is unnecessarily diffused and infiltrated. From this viewpoint, the diffusion and infiltration ratio of R3 of the modifier 60 may be 9.0 parts by mol or less, 8.5 parts by mol or less, 8.0 parts by mol or less, 7.8 parts by mol or less, 7.5 parts by mol or less, 7.0 parts by mol or less, or 6.5 parts by mol or less.
The above-described state where “predetermined band b/a are obtained, and the enhancement of the anisotropic magnetic field (coercive force) and residual magnetization is saturated” is described. Although not bound by theory, even when R3 of the modifier 60 is excessively diffused and infiltrated into the rare earth magnet precursor 50, the ratio at which R1 in the vicinity of the surface layer part of the main phase 10 of the rare earth magnet precursor 50 is replaced by R3 of the modifier 60 is limited. Therefore, it is considered that after b and b/a have reached predetermined ranges in the shell portion 14, redundant R3 remains in the grain boundary phase 20 and the enhancement of the anisotropic magnetic field (coercive force) and residual magnetization is saturated.
Incidentally, when the diffusion and infiltration ratio of R3 of the modifier 60 relative to the total of the rare earth magnet precursor 50 and the modifier 60 (100 parts by mol+q parts by mol) is expressed using p and q in the overall composition of the rare earth magnet 100 of the present disclosure, the diffusion and infiltration ratio is represented by {(1−p)×q}/(100+q).
After the modifier 60 is diffused and infiltrated into the rare earth magnet precursor 50, the rare earth magnet precursor 50 and the modifier 60 are cooled to obtain the rare earth magnet 100 of the present disclosure. As described above, when the modifier 60 is diffused and infiltrated into the grain boundary phase 20, the vicinity of the surface layer of the main phase 10 melts (see,
Although not bound by theory, as long as the productivity is not inhibited, when the cooling rate is slow, the interface between the shell portion 14 and the grain boundary phase 20 is likely to form a facet surface. This facet surface is considered to enhance the coercive force.
From the viewpoint of enhancing the coercive force, the cooling rate may be 10° C./min or less, 7° C./min or less, 4° C./min or less, or 1° C./min or less. On the other hand, from the viewpoint of not inhibiting the productivity, the cooling rate may be 0.1° C./min or more, 0.2° C./min or more, 0.3° C./min or more, 0.5° C./min or more, or 0.6° C./min or more. Incidentally, the cooling rate described here is a cooling rate up to 500° C.
As described above, when a Fe-containing modifier 60 is used (see
The content of B is larger in the R1.1Fe4B4 phase than in the R2Fe14B phase (main phase 10). Therefore, in the case of using a Fe-containing modifier, it is preferable to increase the content of B of the rare earth magnet precursor 50 and thereby facilitate the formation of the R1.1Fe4B4 phase as the triple point 22. This is described by referring to the drawing.
The rare earth magnet precursor 50 is produced by cooling the molten metal having the composition of the rare earth magnet precursor 50. When z is set to the range above, the R1.1Fe4B4 phase is likely to be formed and furthermore, when the cooling rate of the molten metal is smaller, the R1.1Fe4B4 phase is readily formed. These teach that the volume fraction of the R1.1Fe4B4 phase relative to the rare earth magnet precursor 50 can be controlled by the value of z and the molten metal cooling rate.
The volume fraction of the R1.1Fe4B4 phase relative to the rare earth magnet precursor 50 may be 0 vol % or more, 0.1 vol % or more, 0.4 vol % or more, 0.8 vol % or more, 1.4 vol % or more, 2.0 vol % or more, or 5.0 vol % or more, and may be 30.0 vol % or less, 25.0 vol % or less, 20.0 vol % or less, 15.0 vol % or less, 10.0 vol % or less, or 8.0 vol % or less.
As described above, the composition of the modifier 60 is represented, in terms of molar ratio, by the formula: R3(1-p)M2p (wherein R3 is one or more elements selected from the group consisting of Nd, Pr, Gd, Tb, Dy, and Ho, M2 is composed of a transition metal element which is other than a rare earth element and can be alloyed with R3, and unavoidable impurity elements, and 0.05≤p≤0.40). The composition of the Fe-containing modifier 60 is represented as follows using Fe and M3 in place of M2.
The composition of the modifier 60 is represented, in terms of molar ratio, by the formula: R3(1-s-t)FesM3t. M3 is composed of a transition metal element which is other than a rare earth element and can be alloyed with R3 and Fe, and unavoidable impurity elements, and 0.05≤s≤0.30, 0≤t≤0.20 and 0.05≤s+t≤0.40 are satisfied.
The molar ratio s of Fe in the modifier 60 is described using a Fe—Nd phase diagram assuming the modifier 60 is, for example, a Nd—Fe alloy (the case where R3 is Nd and M3 is not contained (t=0)).
The description above is based on the assumption that the modifier 60 is a Nd—Fe alloy (the case where R3 is Nd and M3 is not contained (t=0)), but since R3 is one or more elements selected from the group consisting of Nd, Pr, Gd, Tb, Dy, and Ho, the value of s can be changed from the range above. In addition, the melting point of the modifier 60 can change depending on M2, and therefore the value of s can be changed from the range above. Accordingly, when the range that the value of s can take is verified experimentally, s may be 0.05 or more, 0.10 or more, or 0.15 or more, and may be 0.30 or less, 0.25 or less, or 0.20 or less.
When s is in the range above, the modifier 60 can be diffused and infiltrate at a temperature where the main phase 10 of the rare earth magnet precursor 50 is not coarsened, but by optionally containing M3, the melting point of the modifier can be reduced. From this viewpoint, t may be 0 or more, 0.05 or more, or 0.10 or more. On the other hand, when t is 0.20 or less, the component does not contribute to forming of the R2Fe14B phase (main phase 10) from the R1.1Fe4B4 phase and can be prevented from remaining in the grain boundary phase 20 to cause a reduction in the residual magnetization of the rare earth magnet 100 of the present disclosure. From this viewpoint, t may be 0.18 or less, 0.16 or less, or 0.14 or less.
R3(1-s-t)FesM3t is a formula where M2 of R3(1-p)M2p is divided into Fe and M3, and therefore, the range of (s+t) is the same as the range of p. That is, 0.05≤s+t≤0.40 is satisfied. Incidentally, s and t satisfy 0.05≤s≤0.30 and 0≤t≤0.20, respectively, and at the same time, satisfy 0.05≤s+t≤0.40. Accordingly, for example, when t is 0.20, the upper limit of s is 0.20.
After diffusing and infiltrating the modifier 60 into the rare earth magnet precursor 50, the precursor may be cooled and directly used as the rare earth magnet 100 of the present disclosure, or the rare earth magnet after cooling may be further heat-treated and used as the rare earth magnet 100 of the present disclosure. Although not bound by theory, it is believed that due to this heat treatment, part of the grain boundary phase 20 after diffusing and infiltrating the modifier 60 is melted without altering (without melting) the structure of the main phase 10 and the melt is solidified to evenly cover the main phase 10, contributing the enhancement of the coercive force.
For enjoying the effect of enhancing the coercive force, the heat treatment temperature is preferably 450° C. or more, more preferably 475° C. or more, still more preferably 500° C. or more. On the other hand, for avoiding alteration of the structure of the main phase 10, the heat treatment temperature is preferably 600° C. or less, more preferably 575° C. or less, still more preferably 550° C. or less.
For avoiding oxidation of the rare earth magnet 100 of the present disclosure, the heat treatment is preferably performed in an inert gas atmosphere. The inert gas atmosphere includes a nitrogen gas atmosphere.
Incidentally, in the present description, the hereinbefore-described heat treatment after diffusion and infiltration is sometimes referred to as “heat treatment for optimization”.
The rare earth magnet of the present disclosure and the production method thereof are described more specifically below by referring to Examples and Comparative Examples. Note that the rare earth magnet of the present disclosure and the production method thereof are not limited to the conditions employed in the following Examples.
The following samples were prepared mainly for verifying the effect of the diffusion and infiltration temperature.
A strip cast material having an overall composition represented, in terms of molar ratio, by Nd7.6Ce5.4La1.7FebalB6.4Cu0.1Ga0.3 was pulverized by hydrogenation and then further pulverized using a jet mill to obtain a magnetic powder. The magnetic powder was molded in a magnetic field of 2 T to obtain a green compact. At this time, the molding pressure was 200 MPa. This green compact was subjected to pressureless sintering at 1,040° C. over 4 hours to obtain a sintered magnet.
The resulting sintered magnet was cutout to 4 mm×4 mm×2 mm (t) and used as a rare earth magnet precursor, and a modifier having the composition shown in Table 1 was diffused and infiltrated into the rare earth magnet precursor. The diffusion and infiltration time was 165 minutes. The rare earth magnet precursor after the diffusion and infiltration of the modifier was then cooled to 500° C. at a rate of 10° C./min and further furnace-cooled.
The magnetic properties of each of the obtained samples were measured at room temperature by using Vibrating Sample Magnetometer (VSM). In addition, as for the sample of Example 9, area analysis was performed using SEM-EDX.
The results are shown in Table 1. In Table 1, the average particle diameter of the main phase of the rare earth magnet precursor was determined by the method described in the paragraph of “«Rare Earth Magnet»”. Unless otherwise indicted, the same holds true for Tables other than Table 1.
It could be confirmed from Table 1 and
On the other hand, in the samples of Comparative Examples 1 and 3 where the diffusion and infiltration temperature is more than the melting point of the modifier, the modifier is diffused and infiltrated into the grain boundary phase. However, the diffusion and infiltration temperature is less than 750° C., and therefore the residual magnetization is low. This is considered to occur because a desired shell portion is not formed. Furthermore, in the samples of Comparative Examples 2 and 5 where the diffusion and infiltration temperature exceeds 1,000° C., both the coercive force and the residual magnetization are reduced. This is considered to occur due to coarsening of the main phase. Furthermore, in the sample of Comparative Example 3 where the diffusion and infiltration temperature is not more than the melting point of the modifier, modification is not effected, and the coercive force is extremely low.
The following samples were prepared mainly for confirming the effect of the composition of the modifier.
A strip cast material having an overall composition represented, in terms of molar ratio, by Nd7.6Ce5.4La1.7FebalB6.4Cu0.1Ga0.3 was pulverized by hydrogenation and then further pulverized using a jet mill to obtain a magnetic powder. The magnetic powder was molded in a magnetic field of 2 T to obtain a green compact. At this time, the molding pressure was 200 MPa. This green compact was subjected to pressureless sintering at 1,040° C. over 4 hours to obtain a sintered magnet.
The resulting sintered magnet was cutout to 4 mm×4 mm×2 mm (t) and used as a rare earth magnet precursor, and a modifier having the composition shown in Table 2 was diffused and infiltrated into the rare earth magnet precursor. The diffusion and infiltration time was 165 minutes. The rare earth magnet precursor after the diffusion and infiltration of the modifier was then cooled to 500° C. at a rate of 1° C./min and further furnace-cooled.
The magnetic properties of each of the obtained samples were measured at room temperature by using Vibrating Sample Magnetometer (VSM).
The results are shown in Table 2. In Table 2, Di indicates didymium. In addition,
It could be confirmed from Table 2 and
The following samples were prepared mainly for verifying the effect of the content ratio of B of the rare earth magnet precursor in the case of using a Fe-containing modifier.
A strip cast material having the overall composition shown, in terms of molar ratio, in Table 3 was pulverized by hydrogenation and then further pulverized using a jet mill to obtain a magnetic powder. The magnetic powder was molded in a magnetic field of 2 T to obtain a green compact. At this time, the molding pressure was 400 MPa. This green compact was subjected to pressureless sintering at 1,040° C. over 4 hours to obtain a sintered magnet.
The resulting sintered magnet was cutout to 4 mm×4 mm×2 mm (t) and used as a rare earth magnet precursor, and a modifier having the composition shown in Table 3 was diffused and infiltrated into the rare earth magnet precursor. The diffusion and infiltration time was 165 minutes. The rare earth magnet precursor after the diffusion and infiltration of the modifier was then cooled to 500° C. at a rate of 1° C./min and further furnace-cooled.
The magnetic properties of each of the obtained samples were measured at room temperature by using Vibrating Sample Magnetometer (VSM).
The results are shown in Table 3. In addition,
It could be confirmed that all of the samples of Examples 19 to 20 are excellent in both the coercive force and the residual magnetization. Furthermore, the residual magnetization of the sample of Example 20 is higher than the residual magnetization of the sample of Example 19. This is considered to occur because, as understood from
On the other hand, in the sample of Comparative Example 10 where the content ratio of B in the rare earth magnet precursor is very low, it is considered that a large amount of R2Fe17 phase (a phase having a Th2Zn17-type and/or Th2Ni17-type crystal structure) is generated to inhibit the generation of the R2Fe14B phase (main phase), as a result, the coercive force and the residual magnetization are significantly reduced.
The following samples were prepared mainly for verifying the effect of the volume fraction of the main phase of the rare earth magnet precursor.
A strip cast material having the overall composition shown, in terms of molar ratio, in Table 4 was pulverized by hydrogenation and then further pulverized using a jet mill to obtain a magnetic powder. The magnetic powder was molded in a magnetic field of 2 T to obtain a green compact. At this time, the molding pressure was 400 MPa. This green compact was subjected to pressureless sintering at 1,040° C. over 4 hours to obtain a sintered magnet.
The resulting sintered magnet was cutout to 4 mm×4 mm×2 mm (t) and used as a rare earth magnet precursor, and a modifier having the composition shown in Table 4 was diffused and infiltrated into the rare earth magnet precursor. The diffusion and infiltration time was 165 minutes. The rare earth magnet precursor after the diffusion and infiltration of the modifier was then cooled to 500° C. at a rate of 1° C./min and further furnace-cooled.
The magnetic properties of each of the obtained samples were measured at room temperature by using Vibrating Sample Magnetometer (VSM).
The results are shown in Table 4.
It could be confirmed that all of the samples of Examples 21 and 22 are excellent in both the coercive force and the residual magnetization. This is considered to occur because in Examples 21 and 22, the volume fraction of the main phase of the rare earth magnet precursor is within the predetermined range. On the other hand, the sample of Comparative Example 11 is significantly low in both the coercive force and the residual magnetization. This is considered to occur because in Comparative Example 11, the volume fraction of the main phase of the rare earth magnet precursor is excessively large.
The following samples were prepared mainly for verifying the effect of the content ratio of B of the rare earth magnet precursor in the case of using a Fe-containing modifier.
A strip cast material having the overall composition shown, in terms of molar ratio, in Table 5 was pulverized by hydrogenation and then further pulverized using a jet mill to obtain a magnetic powder. The magnetic powder was molded in a magnetic field of 2 T to obtain a green compact. At this time, the molding pressure was 400 MPa. This green compact was subjected to pressureless sintering at 1,040° C. over 4 hours to obtain a sintered magnet.
The resulting sintered magnet was cutout to 4 mm×4 mm×2 mm (t) and used as a rare earth magnet precursor, and a modifier having the composition shown in Table 5 was diffused and infiltrated into the rare earth magnet precursor. The diffusion and infiltration time was 165 minutes. The rare earth magnet precursor after the diffusion and infiltration of the modifier was then cooled to 500° C. at a rate of 1° C./min and further furnace-cooled.
The magnetic properties of each of the obtained samples were measured at room temperature by using Vibrating Sample Magnetometer (VSM).
The results are shown in Table 5.
It could be confirmed that all of the samples of Examples 23 and 24 are excellent in both the coercive force and the residual magnetization. This is considered to occur because R2Fe14B phase is formed from R1.1Fe4B4 phase due to Fe of the modifier.
On the other hand, in the sample of Comparative Example 12, the content ratio of B in the rare earth magnet precursor is excessively large and in turn, an excess of R1.1Fe4B4 phase is generated. It is considered that in the sample of Comparative Example 12, although the R2Fe14B phase is formed from part of R1.1Fe4B4 phase due to Fe of the modifier, a lot of R1.1Fe4B4 phase remains as it is, as a result, the sample of Comparative Example 12 lacks R2Fe14B phase, leading to reduction of the residual magnetization, and since the rare earth element-rich phase surrounding the main phase is relatively decreased, the coercive force is reduced.
The following samples were prepared mainly for verifying the effect of the average particle diameter of the main phase of the rare earth magnet precursor.
A strip cast material having an overall composition represented, in terms of molar ratio, by Nd6.6Ce4.9La1.6FebalB6.0Cu0.1Ga0.3 was pulverized by hydrogenation and then further pulverized using a jet mill to obtain a magnetic powder. The magnetic powder was molded in a magnetic field of 2 T to obtain a green compact. At this time, the molding pressure was 200 MPa. This green compact was subjected to pressureless sintering at 1,040° C. over 4 hours to obtain a sintered magnet.
The resulting sintered magnet was cutout to 4 mm×4 mm×2 mm (t) and used as a rare earth magnet precursor, and a modifier having the composition shown in Table 6 was diffused and infiltrated at 950° C. into the rare earth magnet precursor. The diffusion and infiltration time was 165 minutes. The rare earth magnet precursor after the diffusion and infiltration of the modifier was then cooled to 500° C. at a rate of 10° C./min and further furnace-cooled. This is designated as the sample of Example 25.
A magnetic powder having the same composition as the sintered magnet of Example 25 and having a nanocrystallized main phase was subjected to hot pressing (low-temperature pressure sintering) to obtain a sintered body. This sintered body was subjected to hot plastic working to obtain a hot-worked magnet.
The resulting hot-plastic worked magnet was cutout to 4 mm×4 mm×2 mm (t) and used as a rare earth magnet precursor, and a modifier having the composition shown in Table 6 was diffused and infiltrated at 950° C. into the rare earth magnet precursor. The diffusion and infiltration time was 165 minutes. The rare earth magnet precursor after the diffusion and infiltration of the modifier was then cooled to 500° C. at a rate of 10° C./min and further furnace-cooled. This is designated as the sample of Comparative Example 13.
The magnetic properties of each of the obtained samples were measured at room temperature by using Vibrating Sample Magnetometer (VSM). In addition, area analysis was performed using SEM-EDX on both samples of Example 25 and Comparative Example 13.
The results are shown in Table 6.
It could be confirmed from Table 6 that the sample of Example 25 is excellent in both the coercive force and the residual magnetization. In addition, it could be confirmed from
On the other hand, it could be confirmed from Table 6 that in the sample of Comparative Example 13, both the coercive force and the residual magnetization are low. In addition, it could be confirmed from
Incidentally, with respect to the sample of Example 25,
The following samples were prepared mainly for verifying the effect of the cooling rate after the diffusion and infiltration of the modifier.
A strip cast material having an overall composition represented, in terms of molar ratio, by Nd7.6Ce5.4La1.7FebalB6.4Cu0.1Ga0.3 was pulverized by hydrogenation and then further pulverized using a jet mill to obtain a magnetic powder. The magnetic powder was molded in a magnetic field of 2 T to obtain a green compact. At this time, the molding pressure was 200 MPa. This green compact was subjected to pressureless sintering at 1,040° C. over 4 hours to obtain a sintered magnet.
The resulting sintered magnet was cutout to 4 mm×4 mm×2 mm (t) and used as a rare earth magnet precursor, and a modifier having the composition shown in Table 7 was diffused and infiltrated at 950° C. into the rare earth magnet precursor. The diffusion and infiltration time was 165 minutes. The rare earth magnet precursor after the diffusion and infiltration of the modifier was then cooled to 500° C. at a rate of 10° C./min or 1° C./min and further furnace-cooled.
The magnetic properties of each of the obtained samples were measured at room temperature by using Vibrating Sample Magnetometer (VSM).
The results are shown in Table 7.
It could be confirmed from Table 7 that the samples of Examples 26 to 29 are excellent in both the coercive force and the residual magnetization. In addition, it could be confirmed that the samples of Examples 27 and 29 are further excellent in the coercive force, compared with those of Examples 26 and 28. This is considered to be attributable to the face that, as described above, the interface between the shell portion and the grain boundary phase is a facet surface.
The following samples were prepared mainly for verifying the effect of the contact amount of the modifier and the heat treatment for optimization.
A strip cast material having an overall composition represented, in terms of molar ratio, by Nd6.6Ce4.9La1.6FebalB6.0Cu0.1Ga0.3 was pulverized by hydrogenation and then further pulverized using a jet mill to obtain a magnetic powder. The magnetic powder was molded in a magnetic field of 2 T to obtain a green compact. At this time, the molding pressure was 200 MPa. This green compact was subjected to pressureless sintering at 1,040° C. over 4 hours to obtain a sintered magnet.
The resulting sintered magnet was cutout to 4 mm×4 mm×2 mm (t) and used as a rare earth magnet precursor, and a modifier having the composition shown in Table 8 was diffused and infiltrated into the rare earth magnet precursor. The diffusion and infiltration time was 165 minutes. The rare earth magnet precursor after the diffusion and infiltration of the modifier was then cooled to 500° C. at a rate of 1° C./min and further furnace-cooled.
After the furnace cooling, the samples of Examples 33 to 41 and Examples 45 to 53 were further heat-treated at the temperature shown in Table 8 (heat treatment for optimization). The heat treatment was performed in an argon gas atmosphere.
The magnetic properties of each of the obtained samples were measured at room temperature by using Vibrating Sample Magnetometer (VSM).
The results are shown in Table 8.
It could be confirmed from Table 8 that the samples of Examples 30 to 53 are excellent in both the coercive force and the residual magnetization. Then, it could be confirmed that both the coercive force and the residual magnetization are higher in the sample where from 7.1 to 7.8 parts by mol of the modifier is diffused and infiltrated relative to 100 parts by mol of the rare earth magnet precursor, than in the sample where from 4.7 to 5.2 parts by mol of the modifier is diffused an infiltrated. In addition, it could be confirmed that compared with the sample where from 7.1 to 7.8 parts by mol of the modifier is diffused and infiltrated relative to 100 parts by mol of the rare earth magnet precursor, in the sample where from 9.5 to 10.4 parts by mol of the modifier is diffused and infiltrated, the coercive force tends to be further enhanced, but the enhancement of the residual magnetization is being saturated.
Furthermore, it could be confirmed from Table 8 that compared with the sample to which heat treatment for optimization is not applied, in the sample subjected to heat treatment for optimization, the coercive force is enhanced. It could also be confirmed that the coercive force-enhancing effect is particularly high at 500 to 550° C.
The following samples were prepared mainly for verifying the magnetic properties at a high temperature (75 to 200° C.).
The method for preparing the rare earth magnet precursor of Example 37 is as described above (see, Table 8, etc.). Then, the rare earth magnet precursor of Comparative Example 14 was prepared by the same method as the rare earth magnet precursor of Example 37 except that the rare earth magnet precursor is a hot-plastic worked magnet. More specifically, in the rare earth magnet precursor of Example 37, the main phase is a microcrystal and the anisotropy is imparted by the molding in a magnetic field, whereas in the rare earth magnet precursor of Comparative Example 14, the main phase is a nanocrystal and the anisotropy is imparted by hot-plastic working.
The outline of the method for preparing the rare earth magnet precursor of Comparative Example 14 is as follows. A molten metal having the same composition as the rare earth magnet precursor of Example 37 was liquid-quenched to obtain a rapid-quenched ribbon. This rapid-quenched ribbon was subjected to hot pressing (temperature: 650° C., pressure: 400 MPa) to obtain a molded body. This molded body was subjected to hot-plastic working (temperature: 780° C., strain rate: 0.1 s−1, working rate: 70%) to obtain a rare earth magnet precursor.
A modifier having the composition shown in Table 9 was diffused and infiltrated into the obtained rare earth magnet precursor (size: 4 mm×4 mm×2 mm (t)). In the rare earth magnet precursor of Example 37, the modifier was diffused and infiltrated at a high temperature (950° C.), and in the sample of Comparative Example 14, the modifier was diffused and infiltrated at a low temperature (650° C.). The diffusion and infiltration time was 165 minutes. Other conditions are as shown in Table 9.
The magnetic properties of each of the obtained samples were measured in the range of room temperature to 200° C. by using Vibrating Sample Magnetometer (VSM).
The results are shown in Table 9. The coercive force and residual magnetization shown in Table 9 were measured at room temperature. In addition,
It could be confirmed from Table 9 that the sample of Example 37 is excellent in both the coercive force and the residual magnetization. In addition, it could be confirmed from
From these results, it could be ascertained that both of the coercive force and the residual magnetization are more excellent in the case of diffusing the modifier at a high temperature into a rare earth magnet precursor having a microcrystal main phase than in the case of diffusing and infiltrating the modifier at a low temperature into a rare earth magnet precursor having a nanocrystallized main phase.
The following samples were prepared mainly for verifying the structures of the core portion and the shell portion.
The preparation method for the samples of Examples 22, 37 and 44 and Comparative Example 14 are as described above (see, Tables 4, 8 and 9, etc.). Furthermore, the samples of Examples 54 and 55 were prepared in the same manner as in Example 37 except that the composition of the strip cast material (the composition of the rare earth magnet precursor) is changed as shown in Table 10.
The magnetic properties of each of the obtained samples were measured at room temperature by using Vibrating Sample Magnetometer (VSM). In addition, with respect to the core portion and the shell portion, the content ratio in a predetermined rare earth magnet was analyzed using Corrector-Spherical Aberration-Scanning Transmission Electron Microscope-Energy Dispersive X-ray Spectrometry (Cs-STEM-EDX), and the above-described a, b and b/a were determined. Furthermore, the thickness of the shell portion was determined.
The results are shown in Table 10. In addition,
First, the method for determining a, b and b/a in the sample of Example 37 is described. When a section of the sample is observed by Cs-STEM, an image illustrated in
In
In
The dark field running along the grain boundary phase in
With respect to the core portion and the shell portion, which can be recognized in this way, when component analysis is performed using Cs-STEM-EDX, the results shown in Table 11 are obtained. Incidentally, in Table 11, the molar ratio of each element determined from the overall composition of the rare earth magnet precursor of Example 37 is shown together. This is determined as follows.
As seen from Table 10, the overall composition of the rare earth magnet precursor of Example 37 is represented by the formula: Nd6.6Ce4.9La1.6FebalB6.0Cu0.1Ga0.3. This formula can also be represented by (Nd0.50Ce0.38La0.12)13.1FebalB6.0Cu0.1Ga0.3. The rare earth magnet precursor has a main phase and a grain boundary phase. The grain boundary phase contains a larger amount of the rare earth element than the main phase, but in the case of containing two or more kinds of rare earth elements, the molar ratios of respective rare earth elements are almost the same between the main phase and the grain boundary phase. In the case of the rare earth magnet precursor of Example 33, the molar ratios of Nd, Ce, and La are 0.50, 0.38, and 0.12, respectively.
It can be understood from Table 11 that Nd is concentrated in the shell portion. In addition, the molar ratio in the core portion substantially coincides with the molar ratio in the rare earth magnet precursor. This means that the light rare earth element (Ce and La) is replaced, in the main phase, by the rare earth element (Nd) other than the light rare earth element by the diffusion and infiltration of the modifier but such a replacement does not occur in the core portion. In addition, the molar ratio in the rare earth magnet precursor is determined from the blending of raw materials at the time pf preparation of the rare earth magnet precursor and substantially coincides with the molar ratio in the shell portion, which is determined using Cs-STEM-EDX. From these, it can be said that the values of a, b and b/a determined based on the analysis results using Cs-STEM-EDX have high reliability.
From Table 10 in which a, band b/a determined as above are shown together, it could be confirmed that the samples of Examples having a, b and b/a satisfying predetermined ranges and having a predetermined shell thickness are excellent in both the coercive force and the residual magnetization.
These results could prove the effect of the rare earth magnet of the present disclosure and the production method thereof.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2019-164896 | Sep 2019 | JP | national |
