# Nanocompositional Electron Microscopic Analysis and Role of Grain Boundary Phase of Isotropically Oriented Nd-Fe-B Magnets

Authors: Gregor A. Zickler; Josef Fidler
Journal: Advances in Materials Science and Engineering
 (2017)

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## Abstract

Nanoanalytical TEM characterization in combination with finite element micromagnetic modelling clarifies the impact of the grain misalignment and grain boundary nanocomposition on the coercive field and gives guidelines how to improve coercivity in Nd-Fe-B based magnets. The nanoprobe electron energy loss spectroscopy measurements obtained an asymmetric composition profile of the Fe-content across the grain boundary phase in isotropically oriented melt-spun magnets and showed an enrichment of iron up to 60 at% in the Nd-containing grain boundaries close to Nd2Fe14B grain surfaces parallel to the c-axis and a reduced iron content up to 35% close to grain surfaces perpendicular to the c-axis. The numerical micromagnetic simulations on isotropically oriented magnets using realistic model structures from the TEM results reveal a complex magnetization reversal starting at the grain boundary phase and show that the coercive field increases compared to directly coupled grains with no grain boundary phase independently of the grain boundary thickness. This behaviour is contrary to the one in aligned anisotropic magnets, where the coercive field decreases compared to directly coupled grains with an increasing grain boundary thickness, if Js value is > 0.2 T, and the magnetization reversal and expansion of reversed magnetic domains primarily start as Bloch domain wall at grain boundaries at the prismatic planes parallel to the c-axis and secondly as Néel domain wall at the basal planes perpendicular to the c-axis. In summary our study shows an increase of coercive field in isotropically oriented Nd-Fe-B magnets for GB layer thickness > 5 nm and an average Js value of the GB layer < 0.8 T compared to the magnet with perfectly aligned grains.


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## Body

## 1. Introduction

The increasing demand of high-performance rare earth permanent magnets with a high coercive field and an energy density product value suitable for large scale applications in wind turbines and electrically powered automotive devices led to the development of heavy rare earth lean/rare earth-free Nd-Fe-B based magnets and to the optimization of the complex multiphase microstructure of the magnets [1]. The hard magnetic properties are primarily controlled by the size, shape, and misalignment of the hard magnetic grains and their distributions and secondarily by the occurrence of other nonmagnetic and soft magnetic phases [2–4]. In addition, the coercive field also strongly depends on the intergranular grain boundary (GB) phases separating the hard magnetic grains [5, 6]. The role of dopant elements, the thickness, and magnetic properties of the GB-phases have extensively been studied during the last 30 years [7, 8]. Local changes of the exchange coupling between grains and the decrease of the anisotropy field and demagnetizing field at/near intergranular phases considerably reduce the overall coercive field. First principles ab initio calculations claimed that even an antiparallel exchange coupling between a crystalline α-Fe phase and the prismatic {100} planes of Nd2Fe14B would be energetically favorable, while a positive exchange-coupling constant was predicted in the Nd2Fe14B (001)/α-Fe interface [9].Advances in electron microscopic characterization technology have greatly improved the ability to quantify real microstructures found in Nd-Fe-B magnets. These techniques, in combination with finite element micromagnetic modelling, are improving the understanding of magnetization reversal processes and coercivity mechanisms. Micromagnetic simulations give a deep insight into the mechanisms that cause magnetization reversal at external fields well below the anisotropy field [10]. Nowadays, the new nanoanalytical electron microscopic techniques with atomic resolution allow the creation of precise microstructural models suitable for the numerical micromagnetic calculation of the demagnetization curve including the coercive field value. A recent high resolution TEM/STEM investigation of the intergranular GB-phase of a large grained, anisotropic sintered heavy rare earth-free Nd‐Fe‐B magnet with grain sizes up to several microns revealed a difference in composition for grain boundaries parallel (large Fe‐content) and perpendicular (low Fe-content) to the alignment direction [11]. This combined TEM/STEM and micromagnetic study of the anisotropic nature of grain boundaries shows a decrease of the coercive field with an increasing thickness of the grain boundary layer.Two quite distinct methods are in commercial use for producing Nd-Fe-B magnets: the rapid-solidification technique of melt spinning and the traditional powder-metallurgy-sintering approach. The present study compares different microstructures of various melt-spun materials with isotropically oriented hard magnetic grains with a grain size ranging from 20 nm to 100 nm. The melt-spinning procedure involves the ejection of a molten starting alloy through a crucible orifice onto the surface of a substrate copper disc with a high rotating speed [12]. The microstructure and magnetic properties of melt-spun neodymium-iron-boron ribbons are sensitively dependent on the quench rate. The resulting hysteretic properties of an individual magnet material strongly depend on their nominal composition, microstructure, and processing parameters [13]. Melt-spun magnet materials have widely been used for bonded and hot deformed type magnets so far. Hot-pressed melt-spun nanocrystalline heavy rare earth-free Nd-Fe-B magnets are promising candidates for a low cost solution for applications that require thermal stability up to 175°C–200°C [14].The aim of the present paper is to determine the influence of the grain size, orientation of grains, and nanocomposition of GBs on the coercive field and magnetization reversal behaviour by a combined TEM/STEM and micromagnetic study with special emphasis on the nanoanalytical, high resolution EELS characterization of isotropically oriented GBs. The microstructural model structure based on an anisotropic compositional behaviour of GBs parallel and perpendicular to the easy axis of the grains which is used for the numerical micromagnetic simulations has been derived from the detailed nanoanalytical TEM/STEM analysis.


## 2. Materials

In the present study we investigated the microstructure of three rapidly quenched Nd-Fe-B ribbons in a nanoanalytical TEM/STEM study, which were provided by Magnequench Technology Center, Singapore. The isotropic RE-rich two-phase ribbon (MQU-F) with the nominal chemical composition (Pr,Nd)13.6Fe73.6Co6.6Ga0.6B5.6 [15] has a distinct 3 nm–6 nm thick RE-rich GB-phase separating the isotropically oriented equiaxed and platelet shaped Nd-Fe-B grains. The isotropic fine grained ribbon (MQP-B+) with the nominal chemical composition Nd12.4Fe77.3Co5.2B5.2 [16] is enriched in “Fe + Co” and possesses therefore a 1 nm–3 nm thin “Fe + Co”-rich GB-phase separating the isotropically orientated equiaxed Nd-Fe-B grains. In comparison an isotropically oriented and large grained nanocomposite with additional soft magnetic α-Fe and Nb-granular phases and without a GB-phase between the hard magnetic grains has been investigated.


## 3. Methods

The nanoanalytical and structural investigations of the rapidly quenched Nd-Fe-B permanent magnet materials have been carried out with an analytical field emission transmission electron microscope (TEM) (FEI Tecnai F20) at 200 kV, which is equipped with a silicon drift energy dispersive X-ray (EDX) detector, a Gatan GIF Tridiem image filter and electron energy loss spectrometer (EELS) and a high angle annular dark field (HAADF) detector. Conventional sample TEM preparation including cutting, polishing, and ion milling in a Precision Ion Polishing System (PIPS) from Gatan was conducted. The structural investigations were performed with Fast Fourier Transformation (FFT) of high resolution TEM/STEM (HRTEM) images and selected area electron diffraction (SAED).EELS experiments were conducted to accurately determine the relative chemical composition of the intergranular phases via thek-factor method. This method calculates the relative atomic percentage of an element (e.g., Nd) with respect to another element (e.g., Fe) from the ratio of their edge intensities in the EELS (or EDX) spectrum via the k-factor (e.g., k(Nd/Fe)), which was derived from the measurement of a standard specimen (e.g., Nd2Fe14B single crystal). TEM specimens with a relative thickness t/λ<0.7, where t is the absolute specimen thickness and λ the mean free path in the specimen, were used in these experiments. Firstly, the k-factors of Pr/Fe and Nd/Fe were calculated from EELS spectra of single crystalline Pr2Fe14B and Nd2Fe14B standards. Secondly, the background in the EELS spectra was fitted with a power-law function and subtracted, which resulted in the edge intensities of the elements. Thirdly, the relative atomic composition was calculated from the edge intensities via the k-factors. The determination of the relative chemical composition via the k-factor method is accurate for t/λ<1.0 with a relative error of ±5% [17]. An optimized background model was used to measure the Fe-L2,3 ionization edge due to its close vicinity to the F-K edge and the Nd-M4,5 ionization edge due to its close vicinity to the Pr-M4,5 edge [18]. To avoid the development of an oxidized layer on the surface of the TEM specimen, precise precautions were taken. The influence of the electron beam broadening and the tilt of the GBs with respect to the incident electron beam on the chemical composition of 2 nm–6 nm thin GBs, as described in our previous publication [11], were taken into account. The higher yield in the elastic scattering events in EELS with respect to EDX [19] leads to a shorter acquisition time of each spectrum in a line scan. This is an advantage especially in the chemical analysis of thin GBs in thin (<50 nm) TEM specimens.The finite element software package FEMME, which is a hybrid finite element/boundary element method code, was used for the numerical micromagnetic simulations [20]. On each point of the finite element mesh the Landau-Lifshitz-Gilbert equation is being solved [21]. Besides the intrinsic magnetic properties, namely, the exchange constantA, the saturation polarization Js, and the uniaxial magnetocrystalline anisotropy constant K1, also the direction of the easy axis (direction of K1) of a volume of a phase, which can be set with the polar angle ϑ and the azimuthal angle φ, is an input parameter for the simulation. K1 was set to zero in the GBs, since it is expected to have a negligibly small or zero value. The long range demagnetizing field and the direct exchange coupling between neighbouring atomic moments in the hard magnetic grains and soft magnetic grain boundary layers strongly influence the magnetization reversal. Besides the exchange and the demagnetizing field, the magnetocrystalline anisotropy and the misorientation of the individual grains also contribute to the resulting magnetization reversal and coercivity [10].Realistic finite element granular structures based on TEM investigations of melt-spun Nd-Fe-B magnets have been generated using the Voronoi algorithm [22]. This algorithm creates a unique volume decomposition based on a set of seeding points, similar to the Wigner-Seitz cell construction. We used the voro++ code [23] to create a Voronoi structure of equiaxed grains. The output from voro++ acts as an input for a Salome [24] script that creates a finite element discretization (mesh) of the granular structure. Two finite element model structures were created, one with directly coupled grains and one with a grain boundary phase with an approximate thickness of 10% of the grain size (Figures 1 and 2). The distribution of the easy axes of an isotropically orientated magnet is equal to the random distribution of points on a half sphere with a calculated azimuthal angle φ=2π·u and polar angle ϑ=cos-1⁡v, where u and v have to be chosen from random variates between 0 and 1. This results in an average misorientation angle ϑ0=60° and a projection of the magnetization parallel to the external field of 0.5 Js [25, 26].Figure 1
Micromagnetic finite element model structure with 29 Voronoi grains separated by a GB-phase with a thickness of about 10% of the grain diameter.Figure 2
(a) Micromagnetic finite element model structure with 29 directly coupled Voronoi grains and (b) fourα-Fe grains (red) and four Fe-Nb-B grains (blue).
(a)
(b)For a clear distinction between GBs parallel and perpendicular to the external field and thec-axis of the adjacent grains a simple two-grain model structure with an edge length of 40 nm was created and meshed with the software package GID version 12.0.4 [27] (Figure 3). Two Nd2Fe14B grains are separated by a GB-phase consisting of two equally thick GB-volumes with a total GB thickness between 2, 4, 5, 6, and 8 nm. All model structures were discretized with a 0.5 nm–2.5 nm mesh size, where the mesh tessellation was chosen in a way to ensure that the smallest GB volume has at least one central node surrounded with the nearest neighbours corresponding to GB material.Figure 3
Micromagnetic finite element model structure with two Nd2Fe14B grains separated by a 2-phase GB, (a) “aligned” magnet with GB ⊥ to [001]: x-GB, (b) “aligned” magnet with GB ∥ to [001]: y-GB, and (c) “random” magnet with mixed GB-phase: x-GB ⊥ to [001] and y-GB ∥ to [001].
(a)
(b)
(c)


## 4. Results and Discussion

### 4.1. TEM/STEM Characterization and Micromagnetic Simulation

#### 4.1.1. Isotropic RE-Rich Two-Phase Melt-Spun Ribbon (MQU-F)

The polycrystalline microstructure of a rapidly quenched MQU-F ribbon with isotropic orientatedc-axis of hard magnetic Nd-Fe-B grains with a size ranging from 20 nm to over 100 nm is shown in the TEM bright field (BF) and HAADF images of Figure 4. The contrast of the TEM-BF image is originated by the combination of orientation/diffraction contrast and absorption contrast, which depends on the thickness and average density of the TEM specimen leading to the bright contrast of the GB-phase. A HAADF image is generated in the STEM mode and the origin of the images contrast depends on the chosen camera length. At a cameral length (cl) below ≈ 80 mm the intensity distribution in the HAADF image mainly consists of the average atomic number Z1.65 of the probed volume (Z-contrast) and the thickness of the specimen [28]. The GB-phase shows a double contrast with a dark interface to the adjacent grains and a bright center in the HAADF image in Figure 4(b). The HAADF intensity profile along the EELS-1 line scan and Z1.65 dependence (Z-contrast) are shown in the insert in Figure 4(b). The Z-contrast was calculated from the atomic percentage of the elements measured with EELS (Figure 7(a)). The dark interface between the grains and the GB is enriched in “Fe + Co” and contains less “Pr + Nd,” leading to a lower average atomic number. The c-axis of elongated grains was always found to be perpendicular to the longer edge of the grains.Figure 4
(a) TEM-BF image showing several misaligned grains with the marked[001] directions and the framed section of the HRTEM image of Figure 6. (b) HAADF image (cl=30 mm) with the EELS-1 line scan (Figure 7) across GB with a double contrast. Insert in (b) correlates the double contrast of the GB (HAADF signal (red)) and the average Z1.65 (blue) along the EELS-1 line scan.
(a)
(b)The hard magnetic Nd-Fe-B grains are separated by a 3 nm–6 nm thick rare earth- (RE-) rich GB-phase and near GB junctions by the cubicc-(Pr,Nd)2O3 phase, which also has previously been reported in literature [2, 7, 11, 29–32]. The weakly paramagnetic c-(Pr,Nd)2O3 phase has only a negligible influence on the magnetization reversal compared to the soft ferromagnetic GB-phases. Dopants like Al, Ga, and Cu influence the liquid phase during sintering [3]. Ga-atoms were dissolved in the hard magnetic grains and GBs partially replacing the Fe-atoms during rapid quenching, since their amount is too low to form separate phases. The amorphous oxygen containing RE-rich GB-phase, shown in the HRTEM image in Figure 5, has an approximate composition of (Pr,Nd)41(Fe,Co)49O6F4. The RE/Fe ratio is in agreement with the composition of Nd48Fe48Cu4 reported by Sasaki et al. [33]. A combined STEM and three-dimensional atom probe tomography (3D-AP) study of sintered Nd-Fe-B magnets reported a chemical composition of the Nd enriched amorphous GB-phase of Nd30Fe45Cu24.1B0.9 [34]. Sepehri-Amin et al. [35] produced a ferromagnetic Nd30Fe66B3Cu1 thin film, whose chemical composition was derived from a laser assisted 3D-AP investigation of GB-phases of sintered Nd-Fe-B magnets. Woodcock et al. [36] reported of an amorphous oxide containing RE-rich GB-phase in a hot deformed Nd-Fe-Co-B-Ga magnet. The (001), (112), and (101) lattice fringes of the hard magnetic Nd2Fe14B grains are visible in Figure 5.Figure 5
HRTEM image of randomly orientated grains separated by amorphous GBs. The (001), (112), and (101) lattice fringes of three grains are visible.Figure 6
HRTEM image of three grains separated by crystalline GBs showing the (001) lattice fringes of the top right grain, (114) of the left grain, and (111) of the bottom grain are visible; the positions of the EELS line scans 2 and 3 of Figure7 are shown.Figure 7
EELS line scans across GBs showing the asymmetric change of composition depending on the relative orientation of the GBs with respect to the neighbouring hard magnetic grains. (a) EELS-1 transition between001 and 111 orientation (x-z-GB). (b) EELS-2 line scan across the asymmetric y-x-GB (from 100 to 001) and (c) EELS-3 line scan across z-y-GB (from 111 to 100). The change in the chemical composition from the 2-14-1 grain into the GB is steeper in the x-GB compared to z-GB in (a); in the x-GB compared to the y-GB in (b); and in the z-GB compared with the y-GB in (c).
(a)
(b)
(c)Crystalline GBs with a lattice plane spacing of 0.31 nm and 0.34 nm are shown in the HRTEM image in Figure6. The (001), (114), and (111) lattice fringes of the hard magnetic grains are visible. Sasaki et al. [37] reported about a crystalline GB-phase with a RE content of 60 at% in Nd13.5Pr0.2Dy0.2Tb0.2Fe76.0Co1.8B6.6Cu0.1Al0.5Ni0.4O0.5 sintered magnet with a high energy product investigated with STEM methods. Another 3D-AP study [33] of a sintered Nd-Fe-B magnet reported about a crystalline GB with Nd-content of 55 at%. A crystalline 5 nm–10 nm thick Cu enriched cubic c-Nd2O3GB-phase in Nd12.0Dy2.7Fe76.3Cu0.4B6.0M2.6 (M = Al, Co, and Nb) sintered Nd-Fe-B magnet was reported by Kim et al. [38]. A crystalline Nd enriched Nd16.4Fe71.8Co7.8B3.5Ga0.5GB-phase in Nd-Fe-B magnets subjected to a hydrogen-disproportion-desorption-recombination process was reported in 3D-AP study [39].In a previous study we have shown [11] that in an aligned sintered magnet the GBs perpendicular (x-GB) to the alignment direction of the magnet have a higher RE content (up to 60 at%) than the GBs parallel (y-GB) to the alignment direction (RE content below 30 at%). GBs with intermediate misorientation to the alignment direction (z-GB) show a chemical composition corresponding to an average of x- and y-GB. In sintered anisotropic magnets pure x- and y-GBs are common, but in melt-spun isotropic magnet materials the GB is a mix of x- and y-GB in general, due to the strong misalignment of the neighbouring grains. The EELS-1 line scan starts from a 2-14-1 grain into a x-GB, resulting in a strong gradient of the chemical composition, and continues from the z-GB into a grain with approximately 45° misorientation of the c-axis with respect to the surface normal of the GB (Figures 4(b) and 7(a)). This correlates with a gradual change of the chemical composition. The EELS-2 line scan starts in a grain whose c-axis is orientated perpendicular to the surface normal of the GB resulting in a slow change in chemical composition (Figures 6 and 7(b)). Since the c-axis of the second grain is orientated parallel to the surface normal of the GB the change in chemical composition is faster. The faster change in the chemical composition from a z-GB with respect to the y-GB is shown in the EELS-3 line scan (Figures 6 and 7(c)).The average “Fe + Co” concentration of the GB-phase in the investigated MQU-F ribbon is 55 at%, if only “Fe + Co” and “Pr + Nd” elements are considered. According to the magnetic phase diagram of Nd100−xFex which was recently published by Sakuma et al. [40] we assumed for the GB-phase a magnetic saturation polarization Js of 0.43 T and calculated an exchange stiffness constant A of 1.0 pJ/T. The relation A∝ε·Js2 between Js and the exchange constant A was used, as suggested by Kronmüller and Fähnle [41].Using the Voronoi model structure of isotropically orientated Nd2Fe14B grains (Figure 1) with an average grain size of 50 nm and a GB-phase with a thickness of 4 nm–6 nm (Figures 5 and 6) we calculated the demagnetization curves obtained from the numerical finite element micromagnetic simulations depending on the coupling between the grains and the degree of misorientation of the grains. Figure 8 shows a high accordance of the coercive field HcJ between the measured value and the randomly misoriented grains. It should be noted that for the simulated demagnetization curve (sm-GB_60°) the remanence Jr gets underestimated in the simulation with a perfectly isotropic distribution of the c-axes (ϑ0≈60°). In addition Figure 8 shows that the simulations for directly coupled Nd2Fe14B grains (no-GB-phase) underestimate the coercive field by 1.5 T (ϑ0≈60°). The simulation with a smaller degree of misalignment of the hard magnetic grains (ϑ0≈45°) reveals the significant increase of HcJ and Jr with respect to the perfectly isotropically oriented case (ϑ0≈60°). This is in agreement with the Stoner-Wohlfarth model of noninteracting single-domain particles [26], where HcJ is increasing by ≈5% of the anisotropy field HA, which corresponds to ≈0.4 T in Nd2Fe14B, if ϑ0 is reduced from 60° to 45°. The reduction of HcJ with rising value of ϑ0 is attenuated in the simulations with a ferromagnetic GB-phase. The higher Jr value of the simulation with ϑ0≈45° with respect to the simulation with ϑ0≈60° is explained by the higher value of the component of the polarization parallel to the applied field direction (z-direction).Figure 8
Comparison of the measured demagnetization curve of the MQU-F melt-spun ribbon with calculated curves for directly coupled Nd2Fe14B grains (no-GB) and grains separated by a weakly soft magnetic GB-phase (sm-GB) with Js=0.43 T and A=1.0 pJ/T for an average grain misorientation of 45° and 60°. The average grain size is 50 nm and the average GB thickness is 5 nm.


#### 4.1.2. Isotropic Fine Grained Melt-Spun Ribbon (MQP-B+)

The small grained microstructure of the sample MQP-B+ is shown in the TEM-BF image of Figure9(a). The isotropic orientation of the c-axes of the Nd-Fe-B grains with a grain size ranging from 15 nm to 50 nm is displayed in the medium angle annular dark field image (MAADF) of Figure 9(b), which is generated at a higher camera length (cl=970 mm) compared to the HAADF image. The MAADF contrast generation is similar to the one of a TEM-BF image. The insert in Figure 9(a) shows EELS line scan across a 3 nm thick “Pr + Nd” enriched GB-phase.Figure 9
(a) TEM bright field (BF) image of small grained MQP-B+ magnet, [(a) insert] EELS line scan across a 3 nm thick “Pr + Nd” enriched GB-phase, and (b) MAADF (cl = 970 mm) image with an isotropic distribution of the (001) lattice plane normal of the 2-14-1 grains and the EELS scan of Figure9(a) (red line).
(a)
(b)Under the assumption that all boron is bound in the Nd2(Fe,Co)14B phase the chemical composition of the intergranular GB-phases has been calculated from the nominal composition Nd12.4(Fe,Co)82.5B5.2 to be Nd17(Fe,Co)83. This corresponds to 12 at% of the total composition. With the approximation of 30 nm large rhombic dodecahedron shaped grains separated by a 2 nm–3 nm thick GB-phase the volume fraction of the GB-phase is 21%. The chemical composition of the GB measured by EELS is Nd20(Fe,Co)77O3. These results are in good agreement with experiments with an Auger Microprobe spectrometer [42].The micromagnetic simulations were carried out with the Voronoi model structure with isotropically orientated grains (Figure1) with an average grain size of 35 nm and a soft magnetic GB-phase with a thickness of 2 nm–4 nm and average values for Js=1.1 T and A=6.54 pJ/m, which is similar as described for the MQU-F sample. The simulated coercive field value is in good agreement with the measured value (Figure 10). Due to the high Js value of the GB the coercive field value (sm-GB) is only slightly increased with respect to HcJ of the simulation from directly coupled Nd2Fe14B grains (no-GB).Figure 10
Comparison of the measured demagnetization curve of the MQP-B+ melt-spun ribbon with calculated curves for directly coupled Nd2Fe14B grains (no-GB) and grains separated by a weakly soft magnetic GB-phase (sm-GB) with Js=1.1 T and A=6.54 pJ/T for an average grain misorientation of 60°. The average grain size is 35 nm and the average GB thickness is 3 nm.


#### 4.1.3. Isotropic Large Grained Nanocomposite withα-Fe and Nb-Containing Granular Phases

The large grained microstructure of the exchange coupled nanocomposite with isotropically orientated Nd-Fe-B grains and a grain size ranging from 30 nm to 150 nm is shown in the TEM-BF image of Figure11(a). The insert in Figure 11(a) is EELS line scan across a GB of two Nd2Fe14B grains with no detected intergranular GB-phase. Besides the hard magnetic 2-14-1 phase the soft ferromagnetic α-Fe and the weakly antiferromagnetic Fe2Nb phase (T<TN≈270 K) [43] are shown in the HRTEM image in Figure 11(b).Figure 11
(a) TEM-BF image of the multiphase large grained nanocomposite. ((a) insert) No change in chemical composition in the EELS line scan across a GB. No separate GB-phase is detected. (b) HRTEM image of three granular phases.
(a)
(b)A large area EDX mapping in the HAADF image in Figure12(b)–12(e) was used to determine the areal fraction of the identified granular phases (Figure 12(a)). Besides the α-Fe phase another soft magnetic Nb6Fe76B18 (Js=1.41 T, HcJ=2.8 mT) phase which was formed by rapid quenching [44] was identified. Table 1 summarizes the lattice parameter, space groups, and prototypes of the analyzed phases which were used to identify the phases in the HRTEM images. The bright areas in the Fe-K map (Figure 12(c)) correspond to the α-Fe phase. The Fe2Nb phase is located at the high intensities of the Nb-K map (Figure 12(d)) and the Nb6Fe76B18 phase at the more dull yellow regions. The location of the 2-14-1 phase is clearly visible in the bright areas in the Nd-L map (Figure 12(e)).Table 1
Crystal structure and lattice parameters of identified phases in the large grained nanocomposite Nd-Fe-B melt-spun ribbon.
Crystal structure
Lattice parameter
Space group
Prototype
Reference
a [nm]
c [nm]
Nd2Fe14B
0.8803
1.2196
P
4
2
/
m
n
m
136
Nd2Fe14B
[46]
α-Fe
0.2865
—
I
m
3
-
m
229
W
[47]
Nb6Fe76B18
1.0819
—
F
m
3
-
m
225
NaCl
[44]
Fe2Nb
0.4835
0.7881
P
6
3
/
m
m
c
194
MgZn2
[48]Figure 12
(a) Morphological map of the four identified granular phases obtained from TEM analysis. (b) HAADF image (cl=200 mm). (c–e) elemental (Fe, Nb, and Nd) EDX maps of sample area as shown in (b). Nd2Fe14B (grey), α-Fe (red), Nb6Fe76B18 (blue), and Fe2Nb (yellow).
(a)
(b)
(c)
(d)
(e)A Voronoi model structure with 29 directly coupled grains (Figure2) with an average size of 60 nm was used to simulate the hysteretic properties. Corresponding to the analyzed volume distribution of the phases we assumed 21 (72%) Nd2Fe14B grains, 4 (14%) α-Fe grains, and 4 (14%) Nb6Fe76B18 grains. The magnetic properties of the phases are summarized in Table 2. All K1 values were set to zero except in the hard magnetic Nd2Fe14B phase.Table 2
Areal fraction and magnetic properties of the four identified granular phases used in the micromagnetic simulations.
Phase
Areal fraction [%]
K
1 [MJ/m3]
J
s [T]
A [pJ/m]
Reference
Nd2Fe14B
65
4.9
1.61
7.7
[49, 50]
α-Fe
16
0
2.15
25.0
[51]
Nb6Fe76B18
15
0
1.41
10.8
[44]
Fe2Nb
4
0
0.001
0.01
[43]
1The Néel temperature of the weakly antiferromagnetic Fe2Nb phase is ≈ 270 K and therefore we assumed nonmagnetic properties for the simulation at room temperature.The measured demagnetization curve and the simulated curves of directly coupled grains with an average grain misorientation of 45° and 60° are shown in Figure13. For the realistic phase distribution the calculated coercive field is slightly underestimated in the simulation compared to the measured value. One reason for this discrepancy is relatively small sample area where the areal distribution was acquired, with respect to the whole ribbon volume. A higher quality of the random distribution of the granular phases would be achieved in a model with a larger number of grains. The model with 29 directly coupled Nd2Fe14B grains overestimates both HcJ and Jr significantly. The strong decrease of HcJ in the model structure with the realistic assumption of soft magnetic grains, compared to the case of only hard magnetic Nd2Fe14B grains, was also reported in a detailed micromagnetic study of Nd-Fe-B magnet with soft magnetic granular phases [45].Figure 13
Comparison of the measured demagnetization curve of the Nd-Fe-B nanocomposite melt-spun ribbon with calculated curves for directly coupled only hard magnetic grains (only Nd2Fe14B) and for the model structure with 8 soft ferromagnetic grains and 21 Nd2Fe14B grains (8 sm-G). 45° and 60° denote the average misorientation of the granular model structure. The average grain size is 60 nm.


### 4.2. Micromagnetic Simulations of the Switching Field of Randomly Orientated Grains

The orientation relation of grain boundaries of adjacent grains and their composition close to their grain surfaces with respect to the alignment direction of the magnet and external field direction influence the resulting magnetic switching field and coercive field, respectively. Using the two-grain (2-G) model structure of Figure3 we compare in Figure 14 three different configurations which possibly occur in anisotropically and isotropically oriented magnets. The first and second case in Figure 14 show a pure x-GB and pure y-GB, commonly found in anisotropic aligned sintered Nd-Fe-B magnets. The external field is parallel to [001] direction in both cases. The third case shows x-GB facing the lower grain and y-GB facing the upper grain and Hext is parallel to [111], typically found in isotropically oriented melt-spun Nd-Fe-B magnets.Figure 14
Three different configurations with the orientation of the GB parallel and normal toHext and the c-axis of the grain perpendicular to the GB (x-GB) and parallel to the GB (y-GB).J
s values for x- and y-GB were calculated from the chemical composition obtained from TEM/EELS measurements of GBs in anisotropic sintered Nd-Fe-B magnets [11]. The measured “Fe + Co” concentrations of the GBs in melt-spun magnets (Figures 7 and 9(a)) and the corresponding Js and A values are summarized in Table 3.Table 3
Measured Fe + Co content in GBs in sintered and melt-spun Nd-Fe-B magnets and resulting magnetic properties.
Measured Fe + Co [at%]
J
s [T]1
A [pJ/m]2
x-GB (sintered)
403
0.15
0.12
y-GB (sintered)
753
1.00
5.41
MQU-F
55
0.43
1.00
MQP-B+
79
1.10
6.54
1After Sakuma et al. [40], 2A is proportional to Js2 [41]. 3[11].The micromagnetic simulations show that the switching fieldHsw depends on both, the GB thickness and Js value of the GB layer (Figure 15(a)). For small Js value of the x-GB (<0.2 T) Hsw slightly increases with rising GB thickness (x-GB). For high Js value of the y-GB (1.0 T) Hsw is significantly lower with rising GB thickness (y-GB). In both cases the external field is parallel to [001] direction. This behaviour is typical for anisotropic magnets with perfectly aligned grains. In the isotropic case (xy-GB), with Hext∥[111], the switching field value slightly decreases with rising GB thickness (Figure 15(a)). For a GB thickness > 5 nm the anisotropic y-GB (Hext∥[001]) has a lower Hsw compared to the isotropic xy-GB (Hext∥[111]). This is an explanation for the trend of higher Hsw values of magnets with higher misorientation degree, which contradicts the results formulated by Stoner and Wohlfarth [26] for noninteracting grains or particles but agrees with experimental results [52] and previous simulations [11]. In comparison, the dependence of the switching field of a 2-G model structure with averaged homogeneous magnetic properties in the GB layer Js=0.43 T and A=1.00 pJ/m and Js=1.1 T and A=6.54 pJ/m, respectively, is shown in Figure 15(a) (dotted lines). With a low Js value (0.43 T) of the GB layer and Hext∥[111]  Hsw is above the value of the anisotropic y-GB (Hext∥[001]). The switching field value of the averaged GB (Hext∥[111]) with a Js of 1.10 T is below Hsw of the y-GB (Hext∥[001]) for all GB thicknesses. At a GB thickness of about 4 nm the xy-GB and the homogeneous GB with a Js of 0.43 T have approximately the same switching field values. Therefore it is justified to use a single phased GB with homogeneous magnetic properties in isotropic multigrain finite element model structures. Figure 15(b) shows that the switching field constantly decreases from 0.44 HA to 0.33 HA for GB thickness ranging from 2 nm to 20 nm with rising Js value of the GB layer, as shown in the results of the simulations of the 2-G model structure with an averaged homogeneous GB composition (Hext∥[111]). It should be noted that the switching field values of the isotropic cases xy-GB [111], GB (0.43 T) [111], and GB(1.10 T) [111] (Figure 15(a)) and 2, 8, and 20 nm GB (Figure 15(b)) are more or less independent of the GB layer thickness.Figure 15
(a) Influence of the GB thickness onHsw: for the three different 2-G model structures of Figure 14 (solid lines). In comparison the GB with averaged homogeneous magnetic properties of Js=0.43 T  Js=1.10 T are shown (dotted line). (b) Influence of the averaged homogeneous saturation polarization of the GB-phase on Hsw in the 2-G model structure for different GB thickness, Hext∥[111]. The 2-G model structure with a GB thickness of 20 nm has a size of 60×60×60 nm.
(a)
(b)During the magnetization reversal processes different types of domain wall (DW) types, such as Bloch and Néel DWs, are formed in perfectly aligned magnets depending on the orientation of the GB with respect to thec-axis of the adjacent grains and the direction of the external field. The calculated demagnetization curves for the pure x-GB with Hext // [001] and Js=0.15 T (Table 3) and for the pure y-GB with Hext // [001] and Js=1.0 T and a GB thickness of 8 nm are shown in Figure 16. As a result of the large difference in Js and A values the coercive field for x- and y-GB varies from 2.7 T to 6.5 T. The x-GB shows a 12% higher coercive field, if the magnetic properties of x- and y-GB are the same. This difference is originated by the different total energies for the formation of a Bloch domain wall (DW) (y-GB) and a Néel DW (x-GB) with an additional stray field contribution.Figure 16
Calculated demagnetization curves forx-GB with Hext // [001] and y-GB with Hext // [001] and a GB thickness of 8 nm. The details of the magnetic states ①–④ are shown in Figures 17 and 18.Figure 17
Calculated magnetization states of thex-GB with Hext // [001]: ① the magnetization of the GB is in plane and ② the magnetization of the GB is parallel to the external field and antiparallel to the adjacent grains forming two Néel DWs close to the grain surfaces.Figure 18
Magnetization states of they-GB [001]: ③ the magnetization of the GB is perpendicular to Hext and the adjacent grains and ④ the magnetization of the GB is parallel to the external field and antiparallel to the adjacent grains forming a Bloch DW.The magnetization of thex-GB rotates in the perpendicular direction with respect to the adjacent grains at a relatively small external field of 0.95 T (Figure 17①). Two Néel DWs are formed, whereby the magnetization within the center of the GB is antiparallel to one of the adjacent grains, until being at a high external field value of 6.45 T (Figure 17②). The high value of the necessary external field is originated by the large formation energy of a Néel DW due to the strong stray field occurring along the whole interfaces between the GB and the neighbouring grains.The magnetization reversal state ③ is typical for a Bloch DW nucleated in they-GB (Figure 18③). Since the magnetization vector has a degree of freedom to rotate along the y-axis with relatively low activation energy, the y-GB switches at a lower external field of 3.78 T and finally forms two Bloch DWs at the interfaces with the hard magnetic grains (Figure 18④). The formation energy of the stray-field-free Bloch DWs is smaller than the one of the Néel DWs. In general the DWs are complex magnetization transitions between neighbouring magnetic domains. Their energy, thickness, and shape depend on various parameters such as the intrinsic magnetic properties and the shape of the magnetic material. The complex structure of DWs can only be calculated numerically by means of micromagnetic simulations [53].The saturation polarization and the thickness of the GB layer have been varied using the isotropic Voronoi model structure of Figure1 in order to verify the results of the 2-G model structure of Figure 15 with a realistic model structure with averaged homogeneous magnetic properties. At a small value of Js and A the GB magnetically decouples the isotropically orientated hard magnetic grains leading to an increase of HcJ with respect to direct coupled Nd2Fe14B grains (Figure 19(a)). This behaviour is strongly pronounced in the MQU-F magnet material and also present in the MQP-B+ ribbon. As Js and A of the GB-phase rise, HcJ decreases linearly due to stronger coupling of the hard magnetic grains and the higher probability of a nucleation of a reverse magnetic domain in the GB. Simultaneously the remanence increases because of the stronger remanence enhancement effect of the coupled Nd-Fe-B grains [54]. At a GB thickness of 5 nm and grain size of 50 nm the coercive fields for the model structures with and without a GB-phase are equal at Js≈1.40 T (A=10.60 pJ/m) and equal at Js≈1.34 T (A=9.71 pJ/m) for a GB thickness of 3 nm and a grain size of 30 nm (Figure 19(a)). The further increase in Js and A leads to a reduction of HcJ with respect to directly coupled Nd2Fe14B grains. In these simulations the ratio between the grain size and the GB thickness was kept constant. This accredits the significant difference in HcJ of the 30 nm G_3 nm GB and 50 nm G_5 nm GB simulations. This influence of the grain size is approximately equal to the difference of the calculated HcJ values of the simulations of the model structure of directly coupled grains without a GB-phase (dotted lines in Figure 19(a)). Bance et al. [55] showed that the decrease of HcJ with increasing grain size in hard magnets is caused by the nonuniform magnetostatic field in the polyhedral grains. In summary the results from the 2-G model structure that HcJ is mostly independent of the GB thickness in isotropically oriented Nd-Fe-B magnets were also verified with the realistic Voronoi model structure calculations.Figure 19
Influence of the averaged magnetic properties, the grain size and GB thickness on the coercive field. (a) Isotropically oriented grains. (b) Isotropically oriented grains.
(a)
(b)The dependence ofHcJ on the GB properties is more strongly pronounced in aligned Nd-Fe-B magnets. Figure 19(b) compares the results of simulations using the Voronoi model structure of Figure 1 with an average grain misalignment ϑ0≈7°. We observed that the decrease of HcJ with rising grain size is less pronounced in the simulations of anisotropically oriented directly coupled Nd-Fe-B grains (dotted lines in Figure 19(b)). Secondly, the GB thickness has a stronger influence on the reduction of HcJ in anisotropic magnets, which is shown in the greater difference in the HcJ values of the 30 nm G_3 nm GB and 50 nm G_5 nm GB simulations compared to the directly coupled simulations (no-GB). This is in accordance with our recently published results of the strong decrease of HcJ with rising GB thickness in anisotropic Nd-Fe-B magnets [11]. It should be emphasized that the presence of a soft magnetic GB layer always leads to a reduction of the coercive field in aligned magnet, if the saturation polarization of the GB is >0.1 T (A=0.05 pJ/m). The decrease of HcJ with rising Js of the GB layer shows a nonlinear behaviour in anisotropically oriented grains, compared to the linear decrease in the isotropic case.


## 4.1. TEM/STEM Characterization and Micromagnetic Simulation

### 4.1.1. Isotropic RE-Rich Two-Phase Melt-Spun Ribbon (MQU-F)

The polycrystalline microstructure of a rapidly quenched MQU-F ribbon with isotropic orientatedc-axis of hard magnetic Nd-Fe-B grains with a size ranging from 20 nm to over 100 nm is shown in the TEM bright field (BF) and HAADF images of Figure 4. The contrast of the TEM-BF image is originated by the combination of orientation/diffraction contrast and absorption contrast, which depends on the thickness and average density of the TEM specimen leading to the bright contrast of the GB-phase. A HAADF image is generated in the STEM mode and the origin of the images contrast depends on the chosen camera length. At a cameral length (cl) below ≈ 80 mm the intensity distribution in the HAADF image mainly consists of the average atomic number Z1.65 of the probed volume (Z-contrast) and the thickness of the specimen [28]. The GB-phase shows a double contrast with a dark interface to the adjacent grains and a bright center in the HAADF image in Figure 4(b). The HAADF intensity profile along the EELS-1 line scan and Z1.65 dependence (Z-contrast) are shown in the insert in Figure 4(b). The Z-contrast was calculated from the atomic percentage of the elements measured with EELS (Figure 7(a)). The dark interface between the grains and the GB is enriched in “Fe + Co” and contains less “Pr + Nd,” leading to a lower average atomic number. The c-axis of elongated grains was always found to be perpendicular to the longer edge of the grains.Figure 4
(a) TEM-BF image showing several misaligned grains with the marked[001] directions and the framed section of the HRTEM image of Figure 6. (b) HAADF image (cl=30 mm) with the EELS-1 line scan (Figure 7) across GB with a double contrast. Insert in (b) correlates the double contrast of the GB (HAADF signal (red)) and the average Z1.65 (blue) along the EELS-1 line scan.
(a)
(b)The hard magnetic Nd-Fe-B grains are separated by a 3 nm–6 nm thick rare earth- (RE-) rich GB-phase and near GB junctions by the cubicc-(Pr,Nd)2O3 phase, which also has previously been reported in literature [2, 7, 11, 29–32]. The weakly paramagnetic c-(Pr,Nd)2O3 phase has only a negligible influence on the magnetization reversal compared to the soft ferromagnetic GB-phases. Dopants like Al, Ga, and Cu influence the liquid phase during sintering [3]. Ga-atoms were dissolved in the hard magnetic grains and GBs partially replacing the Fe-atoms during rapid quenching, since their amount is too low to form separate phases. The amorphous oxygen containing RE-rich GB-phase, shown in the HRTEM image in Figure 5, has an approximate composition of (Pr,Nd)41(Fe,Co)49O6F4. The RE/Fe ratio is in agreement with the composition of Nd48Fe48Cu4 reported by Sasaki et al. [33]. A combined STEM and three-dimensional atom probe tomography (3D-AP) study of sintered Nd-Fe-B magnets reported a chemical composition of the Nd enriched amorphous GB-phase of Nd30Fe45Cu24.1B0.9 [34]. Sepehri-Amin et al. [35] produced a ferromagnetic Nd30Fe66B3Cu1 thin film, whose chemical composition was derived from a laser assisted 3D-AP investigation of GB-phases of sintered Nd-Fe-B magnets. Woodcock et al. [36] reported of an amorphous oxide containing RE-rich GB-phase in a hot deformed Nd-Fe-Co-B-Ga magnet. The (001), (112), and (101) lattice fringes of the hard magnetic Nd2Fe14B grains are visible in Figure 5.Figure 5
HRTEM image of randomly orientated grains separated by amorphous GBs. The (001), (112), and (101) lattice fringes of three grains are visible.Figure 6
HRTEM image of three grains separated by crystalline GBs showing the (001) lattice fringes of the top right grain, (114) of the left grain, and (111) of the bottom grain are visible; the positions of the EELS line scans 2 and 3 of Figure7 are shown.Figure 7
EELS line scans across GBs showing the asymmetric change of composition depending on the relative orientation of the GBs with respect to the neighbouring hard magnetic grains. (a) EELS-1 transition between001 and 111 orientation (x-z-GB). (b) EELS-2 line scan across the asymmetric y-x-GB (from 100 to 001) and (c) EELS-3 line scan across z-y-GB (from 111 to 100). The change in the chemical composition from the 2-14-1 grain into the GB is steeper in the x-GB compared to z-GB in (a); in the x-GB compared to the y-GB in (b); and in the z-GB compared with the y-GB in (c).
(a)
(b)
(c)Crystalline GBs with a lattice plane spacing of 0.31 nm and 0.34 nm are shown in the HRTEM image in Figure6. The (001), (114), and (111) lattice fringes of the hard magnetic grains are visible. Sasaki et al. [37] reported about a crystalline GB-phase with a RE content of 60 at% in Nd13.5Pr0.2Dy0.2Tb0.2Fe76.0Co1.8B6.6Cu0.1Al0.5Ni0.4O0.5 sintered magnet with a high energy product investigated with STEM methods. Another 3D-AP study [33] of a sintered Nd-Fe-B magnet reported about a crystalline GB with Nd-content of 55 at%. A crystalline 5 nm–10 nm thick Cu enriched cubic c-Nd2O3GB-phase in Nd12.0Dy2.7Fe76.3Cu0.4B6.0M2.6 (M = Al, Co, and Nb) sintered Nd-Fe-B magnet was reported by Kim et al. [38]. A crystalline Nd enriched Nd16.4Fe71.8Co7.8B3.5Ga0.5GB-phase in Nd-Fe-B magnets subjected to a hydrogen-disproportion-desorption-recombination process was reported in 3D-AP study [39].In a previous study we have shown [11] that in an aligned sintered magnet the GBs perpendicular (x-GB) to the alignment direction of the magnet have a higher RE content (up to 60 at%) than the GBs parallel (y-GB) to the alignment direction (RE content below 30 at%). GBs with intermediate misorientation to the alignment direction (z-GB) show a chemical composition corresponding to an average of x- and y-GB. In sintered anisotropic magnets pure x- and y-GBs are common, but in melt-spun isotropic magnet materials the GB is a mix of x- and y-GB in general, due to the strong misalignment of the neighbouring grains. The EELS-1 line scan starts from a 2-14-1 grain into a x-GB, resulting in a strong gradient of the chemical composition, and continues from the z-GB into a grain with approximately 45° misorientation of the c-axis with respect to the surface normal of the GB (Figures 4(b) and 7(a)). This correlates with a gradual change of the chemical composition. The EELS-2 line scan starts in a grain whose c-axis is orientated perpendicular to the surface normal of the GB resulting in a slow change in chemical composition (Figures 6 and 7(b)). Since the c-axis of the second grain is orientated parallel to the surface normal of the GB the change in chemical composition is faster. The faster change in the chemical composition from a z-GB with respect to the y-GB is shown in the EELS-3 line scan (Figures 6 and 7(c)).The average “Fe + Co” concentration of the GB-phase in the investigated MQU-F ribbon is 55 at%, if only “Fe + Co” and “Pr + Nd” elements are considered. According to the magnetic phase diagram of Nd100−xFex which was recently published by Sakuma et al. [40] we assumed for the GB-phase a magnetic saturation polarization Js of 0.43 T and calculated an exchange stiffness constant A of 1.0 pJ/T. The relation A∝ε·Js2 between Js and the exchange constant A was used, as suggested by Kronmüller and Fähnle [41].Using the Voronoi model structure of isotropically orientated Nd2Fe14B grains (Figure 1) with an average grain size of 50 nm and a GB-phase with a thickness of 4 nm–6 nm (Figures 5 and 6) we calculated the demagnetization curves obtained from the numerical finite element micromagnetic simulations depending on the coupling between the grains and the degree of misorientation of the grains. Figure 8 shows a high accordance of the coercive field HcJ between the measured value and the randomly misoriented grains. It should be noted that for the simulated demagnetization curve (sm-GB_60°) the remanence Jr gets underestimated in the simulation with a perfectly isotropic distribution of the c-axes (ϑ0≈60°). In addition Figure 8 shows that the simulations for directly coupled Nd2Fe14B grains (no-GB-phase) underestimate the coercive field by 1.5 T (ϑ0≈60°). The simulation with a smaller degree of misalignment of the hard magnetic grains (ϑ0≈45°) reveals the significant increase of HcJ and Jr with respect to the perfectly isotropically oriented case (ϑ0≈60°). This is in agreement with the Stoner-Wohlfarth model of noninteracting single-domain particles [26], where HcJ is increasing by ≈5% of the anisotropy field HA, which corresponds to ≈0.4 T in Nd2Fe14B, if ϑ0 is reduced from 60° to 45°. The reduction of HcJ with rising value of ϑ0 is attenuated in the simulations with a ferromagnetic GB-phase. The higher Jr value of the simulation with ϑ0≈45° with respect to the simulation with ϑ0≈60° is explained by the higher value of the component of the polarization parallel to the applied field direction (z-direction).Figure 8
Comparison of the measured demagnetization curve of the MQU-F melt-spun ribbon with calculated curves for directly coupled Nd2Fe14B grains (no-GB) and grains separated by a weakly soft magnetic GB-phase (sm-GB) with Js=0.43 T and A=1.0 pJ/T for an average grain misorientation of 45° and 60°. The average grain size is 50 nm and the average GB thickness is 5 nm.


### 4.1.2. Isotropic Fine Grained Melt-Spun Ribbon (MQP-B+)

The small grained microstructure of the sample MQP-B+ is shown in the TEM-BF image of Figure9(a). The isotropic orientation of the c-axes of the Nd-Fe-B grains with a grain size ranging from 15 nm to 50 nm is displayed in the medium angle annular dark field image (MAADF) of Figure 9(b), which is generated at a higher camera length (cl=970 mm) compared to the HAADF image. The MAADF contrast generation is similar to the one of a TEM-BF image. The insert in Figure 9(a) shows EELS line scan across a 3 nm thick “Pr + Nd” enriched GB-phase.Figure 9
(a) TEM bright field (BF) image of small grained MQP-B+ magnet, [(a) insert] EELS line scan across a 3 nm thick “Pr + Nd” enriched GB-phase, and (b) MAADF (cl = 970 mm) image with an isotropic distribution of the (001) lattice plane normal of the 2-14-1 grains and the EELS scan of Figure9(a) (red line).
(a)
(b)Under the assumption that all boron is bound in the Nd2(Fe,Co)14B phase the chemical composition of the intergranular GB-phases has been calculated from the nominal composition Nd12.4(Fe,Co)82.5B5.2 to be Nd17(Fe,Co)83. This corresponds to 12 at% of the total composition. With the approximation of 30 nm large rhombic dodecahedron shaped grains separated by a 2 nm–3 nm thick GB-phase the volume fraction of the GB-phase is 21%. The chemical composition of the GB measured by EELS is Nd20(Fe,Co)77O3. These results are in good agreement with experiments with an Auger Microprobe spectrometer [42].The micromagnetic simulations were carried out with the Voronoi model structure with isotropically orientated grains (Figure1) with an average grain size of 35 nm and a soft magnetic GB-phase with a thickness of 2 nm–4 nm and average values for Js=1.1 T and A=6.54 pJ/m, which is similar as described for the MQU-F sample. The simulated coercive field value is in good agreement with the measured value (Figure 10). Due to the high Js value of the GB the coercive field value (sm-GB) is only slightly increased with respect to HcJ of the simulation from directly coupled Nd2Fe14B grains (no-GB).Figure 10
Comparison of the measured demagnetization curve of the MQP-B+ melt-spun ribbon with calculated curves for directly coupled Nd2Fe14B grains (no-GB) and grains separated by a weakly soft magnetic GB-phase (sm-GB) with Js=1.1 T and A=6.54 pJ/T for an average grain misorientation of 60°. The average grain size is 35 nm and the average GB thickness is 3 nm.


### 4.1.3. Isotropic Large Grained Nanocomposite withα-Fe and Nb-Containing Granular Phases

The large grained microstructure of the exchange coupled nanocomposite with isotropically orientated Nd-Fe-B grains and a grain size ranging from 30 nm to 150 nm is shown in the TEM-BF image of Figure11(a). The insert in Figure 11(a) is EELS line scan across a GB of two Nd2Fe14B grains with no detected intergranular GB-phase. Besides the hard magnetic 2-14-1 phase the soft ferromagnetic α-Fe and the weakly antiferromagnetic Fe2Nb phase (T<TN≈270 K) [43] are shown in the HRTEM image in Figure 11(b).Figure 11
(a) TEM-BF image of the multiphase large grained nanocomposite. ((a) insert) No change in chemical composition in the EELS line scan across a GB. No separate GB-phase is detected. (b) HRTEM image of three granular phases.
(a)
(b)A large area EDX mapping in the HAADF image in Figure12(b)–12(e) was used to determine the areal fraction of the identified granular phases (Figure 12(a)). Besides the α-Fe phase another soft magnetic Nb6Fe76B18 (Js=1.41 T, HcJ=2.8 mT) phase which was formed by rapid quenching [44] was identified. Table 1 summarizes the lattice parameter, space groups, and prototypes of the analyzed phases which were used to identify the phases in the HRTEM images. The bright areas in the Fe-K map (Figure 12(c)) correspond to the α-Fe phase. The Fe2Nb phase is located at the high intensities of the Nb-K map (Figure 12(d)) and the Nb6Fe76B18 phase at the more dull yellow regions. The location of the 2-14-1 phase is clearly visible in the bright areas in the Nd-L map (Figure 12(e)).Table 1
Crystal structure and lattice parameters of identified phases in the large grained nanocomposite Nd-Fe-B melt-spun ribbon.
Crystal structure
Lattice parameter
Space group
Prototype
Reference
a [nm]
c [nm]
Nd2Fe14B
0.8803
1.2196
P
4
2
/
m
n
m
136
Nd2Fe14B
[46]
α-Fe
0.2865
—
I
m
3
-
m
229
W
[47]
Nb6Fe76B18
1.0819
—
F
m
3
-
m
225
NaCl
[44]
Fe2Nb
0.4835
0.7881
P
6
3
/
m
m
c
194
MgZn2
[48]Figure 12
(a) Morphological map of the four identified granular phases obtained from TEM analysis. (b) HAADF image (cl=200 mm). (c–e) elemental (Fe, Nb, and Nd) EDX maps of sample area as shown in (b). Nd2Fe14B (grey), α-Fe (red), Nb6Fe76B18 (blue), and Fe2Nb (yellow).
(a)
(b)
(c)
(d)
(e)A Voronoi model structure with 29 directly coupled grains (Figure2) with an average size of 60 nm was used to simulate the hysteretic properties. Corresponding to the analyzed volume distribution of the phases we assumed 21 (72%) Nd2Fe14B grains, 4 (14%) α-Fe grains, and 4 (14%) Nb6Fe76B18 grains. The magnetic properties of the phases are summarized in Table 2. All K1 values were set to zero except in the hard magnetic Nd2Fe14B phase.Table 2
Areal fraction and magnetic properties of the four identified granular phases used in the micromagnetic simulations.
Phase
Areal fraction [%]
K
1 [MJ/m3]
J
s [T]
A [pJ/m]
Reference
Nd2Fe14B
65
4.9
1.61
7.7
[49, 50]
α-Fe
16
0
2.15
25.0
[51]
Nb6Fe76B18
15
0
1.41
10.8
[44]
Fe2Nb
4
0
0.001
0.01
[43]
1The Néel temperature of the weakly antiferromagnetic Fe2Nb phase is ≈ 270 K and therefore we assumed nonmagnetic properties for the simulation at room temperature.The measured demagnetization curve and the simulated curves of directly coupled grains with an average grain misorientation of 45° and 60° are shown in Figure13. For the realistic phase distribution the calculated coercive field is slightly underestimated in the simulation compared to the measured value. One reason for this discrepancy is relatively small sample area where the areal distribution was acquired, with respect to the whole ribbon volume. A higher quality of the random distribution of the granular phases would be achieved in a model with a larger number of grains. The model with 29 directly coupled Nd2Fe14B grains overestimates both HcJ and Jr significantly. The strong decrease of HcJ in the model structure with the realistic assumption of soft magnetic grains, compared to the case of only hard magnetic Nd2Fe14B grains, was also reported in a detailed micromagnetic study of Nd-Fe-B magnet with soft magnetic granular phases [45].Figure 13
Comparison of the measured demagnetization curve of the Nd-Fe-B nanocomposite melt-spun ribbon with calculated curves for directly coupled only hard magnetic grains (only Nd2Fe14B) and for the model structure with 8 soft ferromagnetic grains and 21 Nd2Fe14B grains (8 sm-G). 45° and 60° denote the average misorientation of the granular model structure. The average grain size is 60 nm.


## 4.1.1. Isotropic RE-Rich Two-Phase Melt-Spun Ribbon (MQU-F)

The polycrystalline microstructure of a rapidly quenched MQU-F ribbon with isotropic orientatedc-axis of hard magnetic Nd-Fe-B grains with a size ranging from 20 nm to over 100 nm is shown in the TEM bright field (BF) and HAADF images of Figure 4. The contrast of the TEM-BF image is originated by the combination of orientation/diffraction contrast and absorption contrast, which depends on the thickness and average density of the TEM specimen leading to the bright contrast of the GB-phase. A HAADF image is generated in the STEM mode and the origin of the images contrast depends on the chosen camera length. At a cameral length (cl) below ≈ 80 mm the intensity distribution in the HAADF image mainly consists of the average atomic number Z1.65 of the probed volume (Z-contrast) and the thickness of the specimen [28]. The GB-phase shows a double contrast with a dark interface to the adjacent grains and a bright center in the HAADF image in Figure 4(b). The HAADF intensity profile along the EELS-1 line scan and Z1.65 dependence (Z-contrast) are shown in the insert in Figure 4(b). The Z-contrast was calculated from the atomic percentage of the elements measured with EELS (Figure 7(a)). The dark interface between the grains and the GB is enriched in “Fe + Co” and contains less “Pr + Nd,” leading to a lower average atomic number. The c-axis of elongated grains was always found to be perpendicular to the longer edge of the grains.Figure 4
(a) TEM-BF image showing several misaligned grains with the marked[001] directions and the framed section of the HRTEM image of Figure 6. (b) HAADF image (cl=30 mm) with the EELS-1 line scan (Figure 7) across GB with a double contrast. Insert in (b) correlates the double contrast of the GB (HAADF signal (red)) and the average Z1.65 (blue) along the EELS-1 line scan.
(a)
(b)The hard magnetic Nd-Fe-B grains are separated by a 3 nm–6 nm thick rare earth- (RE-) rich GB-phase and near GB junctions by the cubicc-(Pr,Nd)2O3 phase, which also has previously been reported in literature [2, 7, 11, 29–32]. The weakly paramagnetic c-(Pr,Nd)2O3 phase has only a negligible influence on the magnetization reversal compared to the soft ferromagnetic GB-phases. Dopants like Al, Ga, and Cu influence the liquid phase during sintering [3]. Ga-atoms were dissolved in the hard magnetic grains and GBs partially replacing the Fe-atoms during rapid quenching, since their amount is too low to form separate phases. The amorphous oxygen containing RE-rich GB-phase, shown in the HRTEM image in Figure 5, has an approximate composition of (Pr,Nd)41(Fe,Co)49O6F4. The RE/Fe ratio is in agreement with the composition of Nd48Fe48Cu4 reported by Sasaki et al. [33]. A combined STEM and three-dimensional atom probe tomography (3D-AP) study of sintered Nd-Fe-B magnets reported a chemical composition of the Nd enriched amorphous GB-phase of Nd30Fe45Cu24.1B0.9 [34]. Sepehri-Amin et al. [35] produced a ferromagnetic Nd30Fe66B3Cu1 thin film, whose chemical composition was derived from a laser assisted 3D-AP investigation of GB-phases of sintered Nd-Fe-B magnets. Woodcock et al. [36] reported of an amorphous oxide containing RE-rich GB-phase in a hot deformed Nd-Fe-Co-B-Ga magnet. The (001), (112), and (101) lattice fringes of the hard magnetic Nd2Fe14B grains are visible in Figure 5.Figure 5
HRTEM image of randomly orientated grains separated by amorphous GBs. The (001), (112), and (101) lattice fringes of three grains are visible.Figure 6
HRTEM image of three grains separated by crystalline GBs showing the (001) lattice fringes of the top right grain, (114) of the left grain, and (111) of the bottom grain are visible; the positions of the EELS line scans 2 and 3 of Figure7 are shown.Figure 7
EELS line scans across GBs showing the asymmetric change of composition depending on the relative orientation of the GBs with respect to the neighbouring hard magnetic grains. (a) EELS-1 transition between001 and 111 orientation (x-z-GB). (b) EELS-2 line scan across the asymmetric y-x-GB (from 100 to 001) and (c) EELS-3 line scan across z-y-GB (from 111 to 100). The change in the chemical composition from the 2-14-1 grain into the GB is steeper in the x-GB compared to z-GB in (a); in the x-GB compared to the y-GB in (b); and in the z-GB compared with the y-GB in (c).
(a)
(b)
(c)Crystalline GBs with a lattice plane spacing of 0.31 nm and 0.34 nm are shown in the HRTEM image in Figure6. The (001), (114), and (111) lattice fringes of the hard magnetic grains are visible. Sasaki et al. [37] reported about a crystalline GB-phase with a RE content of 60 at% in Nd13.5Pr0.2Dy0.2Tb0.2Fe76.0Co1.8B6.6Cu0.1Al0.5Ni0.4O0.5 sintered magnet with a high energy product investigated with STEM methods. Another 3D-AP study [33] of a sintered Nd-Fe-B magnet reported about a crystalline GB with Nd-content of 55 at%. A crystalline 5 nm–10 nm thick Cu enriched cubic c-Nd2O3GB-phase in Nd12.0Dy2.7Fe76.3Cu0.4B6.0M2.6 (M = Al, Co, and Nb) sintered Nd-Fe-B magnet was reported by Kim et al. [38]. A crystalline Nd enriched Nd16.4Fe71.8Co7.8B3.5Ga0.5GB-phase in Nd-Fe-B magnets subjected to a hydrogen-disproportion-desorption-recombination process was reported in 3D-AP study [39].In a previous study we have shown [11] that in an aligned sintered magnet the GBs perpendicular (x-GB) to the alignment direction of the magnet have a higher RE content (up to 60 at%) than the GBs parallel (y-GB) to the alignment direction (RE content below 30 at%). GBs with intermediate misorientation to the alignment direction (z-GB) show a chemical composition corresponding to an average of x- and y-GB. In sintered anisotropic magnets pure x- and y-GBs are common, but in melt-spun isotropic magnet materials the GB is a mix of x- and y-GB in general, due to the strong misalignment of the neighbouring grains. The EELS-1 line scan starts from a 2-14-1 grain into a x-GB, resulting in a strong gradient of the chemical composition, and continues from the z-GB into a grain with approximately 45° misorientation of the c-axis with respect to the surface normal of the GB (Figures 4(b) and 7(a)). This correlates with a gradual change of the chemical composition. The EELS-2 line scan starts in a grain whose c-axis is orientated perpendicular to the surface normal of the GB resulting in a slow change in chemical composition (Figures 6 and 7(b)). Since the c-axis of the second grain is orientated parallel to the surface normal of the GB the change in chemical composition is faster. The faster change in the chemical composition from a z-GB with respect to the y-GB is shown in the EELS-3 line scan (Figures 6 and 7(c)).The average “Fe + Co” concentration of the GB-phase in the investigated MQU-F ribbon is 55 at%, if only “Fe + Co” and “Pr + Nd” elements are considered. According to the magnetic phase diagram of Nd100−xFex which was recently published by Sakuma et al. [40] we assumed for the GB-phase a magnetic saturation polarization Js of 0.43 T and calculated an exchange stiffness constant A of 1.0 pJ/T. The relation A∝ε·Js2 between Js and the exchange constant A was used, as suggested by Kronmüller and Fähnle [41].Using the Voronoi model structure of isotropically orientated Nd2Fe14B grains (Figure 1) with an average grain size of 50 nm and a GB-phase with a thickness of 4 nm–6 nm (Figures 5 and 6) we calculated the demagnetization curves obtained from the numerical finite element micromagnetic simulations depending on the coupling between the grains and the degree of misorientation of the grains. Figure 8 shows a high accordance of the coercive field HcJ between the measured value and the randomly misoriented grains. It should be noted that for the simulated demagnetization curve (sm-GB_60°) the remanence Jr gets underestimated in the simulation with a perfectly isotropic distribution of the c-axes (ϑ0≈60°). In addition Figure 8 shows that the simulations for directly coupled Nd2Fe14B grains (no-GB-phase) underestimate the coercive field by 1.5 T (ϑ0≈60°). The simulation with a smaller degree of misalignment of the hard magnetic grains (ϑ0≈45°) reveals the significant increase of HcJ and Jr with respect to the perfectly isotropically oriented case (ϑ0≈60°). This is in agreement with the Stoner-Wohlfarth model of noninteracting single-domain particles [26], where HcJ is increasing by ≈5% of the anisotropy field HA, which corresponds to ≈0.4 T in Nd2Fe14B, if ϑ0 is reduced from 60° to 45°. The reduction of HcJ with rising value of ϑ0 is attenuated in the simulations with a ferromagnetic GB-phase. The higher Jr value of the simulation with ϑ0≈45° with respect to the simulation with ϑ0≈60° is explained by the higher value of the component of the polarization parallel to the applied field direction (z-direction).Figure 8
Comparison of the measured demagnetization curve of the MQU-F melt-spun ribbon with calculated curves for directly coupled Nd2Fe14B grains (no-GB) and grains separated by a weakly soft magnetic GB-phase (sm-GB) with Js=0.43 T and A=1.0 pJ/T for an average grain misorientation of 45° and 60°. The average grain size is 50 nm and the average GB thickness is 5 nm.


## 4.1.2. Isotropic Fine Grained Melt-Spun Ribbon (MQP-B+)

The small grained microstructure of the sample MQP-B+ is shown in the TEM-BF image of Figure9(a). The isotropic orientation of the c-axes of the Nd-Fe-B grains with a grain size ranging from 15 nm to 50 nm is displayed in the medium angle annular dark field image (MAADF) of Figure 9(b), which is generated at a higher camera length (cl=970 mm) compared to the HAADF image. The MAADF contrast generation is similar to the one of a TEM-BF image. The insert in Figure 9(a) shows EELS line scan across a 3 nm thick “Pr + Nd” enriched GB-phase.Figure 9
(a) TEM bright field (BF) image of small grained MQP-B+ magnet, [(a) insert] EELS line scan across a 3 nm thick “Pr + Nd” enriched GB-phase, and (b) MAADF (cl = 970 mm) image with an isotropic distribution of the (001) lattice plane normal of the 2-14-1 grains and the EELS scan of Figure9(a) (red line).
(a)
(b)Under the assumption that all boron is bound in the Nd2(Fe,Co)14B phase the chemical composition of the intergranular GB-phases has been calculated from the nominal composition Nd12.4(Fe,Co)82.5B5.2 to be Nd17(Fe,Co)83. This corresponds to 12 at% of the total composition. With the approximation of 30 nm large rhombic dodecahedron shaped grains separated by a 2 nm–3 nm thick GB-phase the volume fraction of the GB-phase is 21%. The chemical composition of the GB measured by EELS is Nd20(Fe,Co)77O3. These results are in good agreement with experiments with an Auger Microprobe spectrometer [42].The micromagnetic simulations were carried out with the Voronoi model structure with isotropically orientated grains (Figure1) with an average grain size of 35 nm and a soft magnetic GB-phase with a thickness of 2 nm–4 nm and average values for Js=1.1 T and A=6.54 pJ/m, which is similar as described for the MQU-F sample. The simulated coercive field value is in good agreement with the measured value (Figure 10). Due to the high Js value of the GB the coercive field value (sm-GB) is only slightly increased with respect to HcJ of the simulation from directly coupled Nd2Fe14B grains (no-GB).Figure 10
Comparison of the measured demagnetization curve of the MQP-B+ melt-spun ribbon with calculated curves for directly coupled Nd2Fe14B grains (no-GB) and grains separated by a weakly soft magnetic GB-phase (sm-GB) with Js=1.1 T and A=6.54 pJ/T for an average grain misorientation of 60°. The average grain size is 35 nm and the average GB thickness is 3 nm.


## 4.1.3. Isotropic Large Grained Nanocomposite withα-Fe and Nb-Containing Granular Phases

The large grained microstructure of the exchange coupled nanocomposite with isotropically orientated Nd-Fe-B grains and a grain size ranging from 30 nm to 150 nm is shown in the TEM-BF image of Figure11(a). The insert in Figure 11(a) is EELS line scan across a GB of two Nd2Fe14B grains with no detected intergranular GB-phase. Besides the hard magnetic 2-14-1 phase the soft ferromagnetic α-Fe and the weakly antiferromagnetic Fe2Nb phase (T<TN≈270 K) [43] are shown in the HRTEM image in Figure 11(b).Figure 11
(a) TEM-BF image of the multiphase large grained nanocomposite. ((a) insert) No change in chemical composition in the EELS line scan across a GB. No separate GB-phase is detected. (b) HRTEM image of three granular phases.
(a)
(b)A large area EDX mapping in the HAADF image in Figure12(b)–12(e) was used to determine the areal fraction of the identified granular phases (Figure 12(a)). Besides the α-Fe phase another soft magnetic Nb6Fe76B18 (Js=1.41 T, HcJ=2.8 mT) phase which was formed by rapid quenching [44] was identified. Table 1 summarizes the lattice parameter, space groups, and prototypes of the analyzed phases which were used to identify the phases in the HRTEM images. The bright areas in the Fe-K map (Figure 12(c)) correspond to the α-Fe phase. The Fe2Nb phase is located at the high intensities of the Nb-K map (Figure 12(d)) and the Nb6Fe76B18 phase at the more dull yellow regions. The location of the 2-14-1 phase is clearly visible in the bright areas in the Nd-L map (Figure 12(e)).Table 1
Crystal structure and lattice parameters of identified phases in the large grained nanocomposite Nd-Fe-B melt-spun ribbon.
Crystal structure
Lattice parameter
Space group
Prototype
Reference
a [nm]
c [nm]
Nd2Fe14B
0.8803
1.2196
P
4
2
/
m
n
m
136
Nd2Fe14B
[46]
α-Fe
0.2865
—
I
m
3
-
m
229
W
[47]
Nb6Fe76B18
1.0819
—
F
m
3
-
m
225
NaCl
[44]
Fe2Nb
0.4835
0.7881
P
6
3
/
m
m
c
194
MgZn2
[48]Figure 12
(a) Morphological map of the four identified granular phases obtained from TEM analysis. (b) HAADF image (cl=200 mm). (c–e) elemental (Fe, Nb, and Nd) EDX maps of sample area as shown in (b). Nd2Fe14B (grey), α-Fe (red), Nb6Fe76B18 (blue), and Fe2Nb (yellow).
(a)
(b)
(c)
(d)
(e)A Voronoi model structure with 29 directly coupled grains (Figure2) with an average size of 60 nm was used to simulate the hysteretic properties. Corresponding to the analyzed volume distribution of the phases we assumed 21 (72%) Nd2Fe14B grains, 4 (14%) α-Fe grains, and 4 (14%) Nb6Fe76B18 grains. The magnetic properties of the phases are summarized in Table 2. All K1 values were set to zero except in the hard magnetic Nd2Fe14B phase.Table 2
Areal fraction and magnetic properties of the four identified granular phases used in the micromagnetic simulations.
Phase
Areal fraction [%]
K
1 [MJ/m3]
J
s [T]
A [pJ/m]
Reference
Nd2Fe14B
65
4.9
1.61
7.7
[49, 50]
α-Fe
16
0
2.15
25.0
[51]
Nb6Fe76B18
15
0
1.41
10.8
[44]
Fe2Nb
4
0
0.001
0.01
[43]
1The Néel temperature of the weakly antiferromagnetic Fe2Nb phase is ≈ 270 K and therefore we assumed nonmagnetic properties for the simulation at room temperature.The measured demagnetization curve and the simulated curves of directly coupled grains with an average grain misorientation of 45° and 60° are shown in Figure13. For the realistic phase distribution the calculated coercive field is slightly underestimated in the simulation compared to the measured value. One reason for this discrepancy is relatively small sample area where the areal distribution was acquired, with respect to the whole ribbon volume. A higher quality of the random distribution of the granular phases would be achieved in a model with a larger number of grains. The model with 29 directly coupled Nd2Fe14B grains overestimates both HcJ and Jr significantly. The strong decrease of HcJ in the model structure with the realistic assumption of soft magnetic grains, compared to the case of only hard magnetic Nd2Fe14B grains, was also reported in a detailed micromagnetic study of Nd-Fe-B magnet with soft magnetic granular phases [45].Figure 13
Comparison of the measured demagnetization curve of the Nd-Fe-B nanocomposite melt-spun ribbon with calculated curves for directly coupled only hard magnetic grains (only Nd2Fe14B) and for the model structure with 8 soft ferromagnetic grains and 21 Nd2Fe14B grains (8 sm-G). 45° and 60° denote the average misorientation of the granular model structure. The average grain size is 60 nm.


## 4.2. Micromagnetic Simulations of the Switching Field of Randomly Orientated Grains

The orientation relation of grain boundaries of adjacent grains and their composition close to their grain surfaces with respect to the alignment direction of the magnet and external field direction influence the resulting magnetic switching field and coercive field, respectively. Using the two-grain (2-G) model structure of Figure3 we compare in Figure 14 three different configurations which possibly occur in anisotropically and isotropically oriented magnets. The first and second case in Figure 14 show a pure x-GB and pure y-GB, commonly found in anisotropic aligned sintered Nd-Fe-B magnets. The external field is parallel to [001] direction in both cases. The third case shows x-GB facing the lower grain and y-GB facing the upper grain and Hext is parallel to [111], typically found in isotropically oriented melt-spun Nd-Fe-B magnets.Figure 14
Three different configurations with the orientation of the GB parallel and normal toHext and the c-axis of the grain perpendicular to the GB (x-GB) and parallel to the GB (y-GB).J
s values for x- and y-GB were calculated from the chemical composition obtained from TEM/EELS measurements of GBs in anisotropic sintered Nd-Fe-B magnets [11]. The measured “Fe + Co” concentrations of the GBs in melt-spun magnets (Figures 7 and 9(a)) and the corresponding Js and A values are summarized in Table 3.Table 3
Measured Fe + Co content in GBs in sintered and melt-spun Nd-Fe-B magnets and resulting magnetic properties.
Measured Fe + Co [at%]
J
s [T]1
A [pJ/m]2
x-GB (sintered)
403
0.15
0.12
y-GB (sintered)
753
1.00
5.41
MQU-F
55
0.43
1.00
MQP-B+
79
1.10
6.54
1After Sakuma et al. [40], 2A is proportional to Js2 [41]. 3[11].The micromagnetic simulations show that the switching fieldHsw depends on both, the GB thickness and Js value of the GB layer (Figure 15(a)). For small Js value of the x-GB (<0.2 T) Hsw slightly increases with rising GB thickness (x-GB). For high Js value of the y-GB (1.0 T) Hsw is significantly lower with rising GB thickness (y-GB). In both cases the external field is parallel to [001] direction. This behaviour is typical for anisotropic magnets with perfectly aligned grains. In the isotropic case (xy-GB), with Hext∥[111], the switching field value slightly decreases with rising GB thickness (Figure 15(a)). For a GB thickness > 5 nm the anisotropic y-GB (Hext∥[001]) has a lower Hsw compared to the isotropic xy-GB (Hext∥[111]). This is an explanation for the trend of higher Hsw values of magnets with higher misorientation degree, which contradicts the results formulated by Stoner and Wohlfarth [26] for noninteracting grains or particles but agrees with experimental results [52] and previous simulations [11]. In comparison, the dependence of the switching field of a 2-G model structure with averaged homogeneous magnetic properties in the GB layer Js=0.43 T and A=1.00 pJ/m and Js=1.1 T and A=6.54 pJ/m, respectively, is shown in Figure 15(a) (dotted lines). With a low Js value (0.43 T) of the GB layer and Hext∥[111]  Hsw is above the value of the anisotropic y-GB (Hext∥[001]). The switching field value of the averaged GB (Hext∥[111]) with a Js of 1.10 T is below Hsw of the y-GB (Hext∥[001]) for all GB thicknesses. At a GB thickness of about 4 nm the xy-GB and the homogeneous GB with a Js of 0.43 T have approximately the same switching field values. Therefore it is justified to use a single phased GB with homogeneous magnetic properties in isotropic multigrain finite element model structures. Figure 15(b) shows that the switching field constantly decreases from 0.44 HA to 0.33 HA for GB thickness ranging from 2 nm to 20 nm with rising Js value of the GB layer, as shown in the results of the simulations of the 2-G model structure with an averaged homogeneous GB composition (Hext∥[111]). It should be noted that the switching field values of the isotropic cases xy-GB [111], GB (0.43 T) [111], and GB(1.10 T) [111] (Figure 15(a)) and 2, 8, and 20 nm GB (Figure 15(b)) are more or less independent of the GB layer thickness.Figure 15
(a) Influence of the GB thickness onHsw: for the three different 2-G model structures of Figure 14 (solid lines). In comparison the GB with averaged homogeneous magnetic properties of Js=0.43 T  Js=1.10 T are shown (dotted line). (b) Influence of the averaged homogeneous saturation polarization of the GB-phase on Hsw in the 2-G model structure for different GB thickness, Hext∥[111]. The 2-G model structure with a GB thickness of 20 nm has a size of 60×60×60 nm.
(a)
(b)During the magnetization reversal processes different types of domain wall (DW) types, such as Bloch and Néel DWs, are formed in perfectly aligned magnets depending on the orientation of the GB with respect to thec-axis of the adjacent grains and the direction of the external field. The calculated demagnetization curves for the pure x-GB with Hext // [001] and Js=0.15 T (Table 3) and for the pure y-GB with Hext // [001] and Js=1.0 T and a GB thickness of 8 nm are shown in Figure 16. As a result of the large difference in Js and A values the coercive field for x- and y-GB varies from 2.7 T to 6.5 T. The x-GB shows a 12% higher coercive field, if the magnetic properties of x- and y-GB are the same. This difference is originated by the different total energies for the formation of a Bloch domain wall (DW) (y-GB) and a Néel DW (x-GB) with an additional stray field contribution.Figure 16
Calculated demagnetization curves forx-GB with Hext // [001] and y-GB with Hext // [001] and a GB thickness of 8 nm. The details of the magnetic states ①–④ are shown in Figures 17 and 18.Figure 17
Calculated magnetization states of thex-GB with Hext // [001]: ① the magnetization of the GB is in plane and ② the magnetization of the GB is parallel to the external field and antiparallel to the adjacent grains forming two Néel DWs close to the grain surfaces.Figure 18
Magnetization states of they-GB [001]: ③ the magnetization of the GB is perpendicular to Hext and the adjacent grains and ④ the magnetization of the GB is parallel to the external field and antiparallel to the adjacent grains forming a Bloch DW.The magnetization of thex-GB rotates in the perpendicular direction with respect to the adjacent grains at a relatively small external field of 0.95 T (Figure 17①). Two Néel DWs are formed, whereby the magnetization within the center of the GB is antiparallel to one of the adjacent grains, until being at a high external field value of 6.45 T (Figure 17②). The high value of the necessary external field is originated by the large formation energy of a Néel DW due to the strong stray field occurring along the whole interfaces between the GB and the neighbouring grains.The magnetization reversal state ③ is typical for a Bloch DW nucleated in they-GB (Figure 18③). Since the magnetization vector has a degree of freedom to rotate along the y-axis with relatively low activation energy, the y-GB switches at a lower external field of 3.78 T and finally forms two Bloch DWs at the interfaces with the hard magnetic grains (Figure 18④). The formation energy of the stray-field-free Bloch DWs is smaller than the one of the Néel DWs. In general the DWs are complex magnetization transitions between neighbouring magnetic domains. Their energy, thickness, and shape depend on various parameters such as the intrinsic magnetic properties and the shape of the magnetic material. The complex structure of DWs can only be calculated numerically by means of micromagnetic simulations [53].The saturation polarization and the thickness of the GB layer have been varied using the isotropic Voronoi model structure of Figure1 in order to verify the results of the 2-G model structure of Figure 15 with a realistic model structure with averaged homogeneous magnetic properties. At a small value of Js and A the GB magnetically decouples the isotropically orientated hard magnetic grains leading to an increase of HcJ with respect to direct coupled Nd2Fe14B grains (Figure 19(a)). This behaviour is strongly pronounced in the MQU-F magnet material and also present in the MQP-B+ ribbon. As Js and A of the GB-phase rise, HcJ decreases linearly due to stronger coupling of the hard magnetic grains and the higher probability of a nucleation of a reverse magnetic domain in the GB. Simultaneously the remanence increases because of the stronger remanence enhancement effect of the coupled Nd-Fe-B grains [54]. At a GB thickness of 5 nm and grain size of 50 nm the coercive fields for the model structures with and without a GB-phase are equal at Js≈1.40 T (A=10.60 pJ/m) and equal at Js≈1.34 T (A=9.71 pJ/m) for a GB thickness of 3 nm and a grain size of 30 nm (Figure 19(a)). The further increase in Js and A leads to a reduction of HcJ with respect to directly coupled Nd2Fe14B grains. In these simulations the ratio between the grain size and the GB thickness was kept constant. This accredits the significant difference in HcJ of the 30 nm G_3 nm GB and 50 nm G_5 nm GB simulations. This influence of the grain size is approximately equal to the difference of the calculated HcJ values of the simulations of the model structure of directly coupled grains without a GB-phase (dotted lines in Figure 19(a)). Bance et al. [55] showed that the decrease of HcJ with increasing grain size in hard magnets is caused by the nonuniform magnetostatic field in the polyhedral grains. In summary the results from the 2-G model structure that HcJ is mostly independent of the GB thickness in isotropically oriented Nd-Fe-B magnets were also verified with the realistic Voronoi model structure calculations.Figure 19
Influence of the averaged magnetic properties, the grain size and GB thickness on the coercive field. (a) Isotropically oriented grains. (b) Isotropically oriented grains.
(a)
(b)The dependence ofHcJ on the GB properties is more strongly pronounced in aligned Nd-Fe-B magnets. Figure 19(b) compares the results of simulations using the Voronoi model structure of Figure 1 with an average grain misalignment ϑ0≈7°. We observed that the decrease of HcJ with rising grain size is less pronounced in the simulations of anisotropically oriented directly coupled Nd-Fe-B grains (dotted lines in Figure 19(b)). Secondly, the GB thickness has a stronger influence on the reduction of HcJ in anisotropic magnets, which is shown in the greater difference in the HcJ values of the 30 nm G_3 nm GB and 50 nm G_5 nm GB simulations compared to the directly coupled simulations (no-GB). This is in accordance with our recently published results of the strong decrease of HcJ with rising GB thickness in anisotropic Nd-Fe-B magnets [11]. It should be emphasized that the presence of a soft magnetic GB layer always leads to a reduction of the coercive field in aligned magnet, if the saturation polarization of the GB is >0.1 T (A=0.05 pJ/m). The decrease of HcJ with rising Js of the GB layer shows a nonlinear behaviour in anisotropically oriented grains, compared to the linear decrease in the isotropic case.


## 5. Conclusion

The TEM/EELS analysis of nanocrystalline Nd-Fe-B based magnet materials revealed an asymmetric composition profile of the Fe- and the Nd-content across the grain boundary phase in isotropically oriented melt-spun magnets. We found an enrichment of iron up to 60 at% in the Nd-containing grain boundaries close to the prismatic Nd2Fe14B grain surfaces and a reduced iron content up to 35% close to basal grain surfaces perpendicular to the c-axis. Numerical micromagnetic simulations based on granular Voronoi model structures showed that the coercive field strongly depends on the average Fe-content and the saturation polarization and exchange stiffness constant of the GB-phase as well as on the GB thickness and grain orientation. In general, the coercive field is significantly increased, if the Fe-content of the GBs, especially parallel to the c-direction of the hard magnetic 2-14-1 grains, is reduced. Our simulations predicted an increase of the coercive field of isotropically oriented magnets with a soft magnetic GB-phase independently of the grain boundary thickness between 2 nm and 20 nm for Js<1.2 T compared to directly coupled 2-14-1 grains with no-GB-phase. Contrary to this result we have demonstrated that the coercive field of anisotropic, aligned magnets significantly decreases for soft magnetic GB-phases with Js>0.2 T and GB thickness of 3 nm–5 nm compared to directly coupled 2-14-1 grains. Moreover a rising GB thickness > 4 nm further leads to a significant reduction in coercive field in anisotropic aligned magnets.We have demonstrated that numerical micromagnetic simulations perfectly predict the hysteretic properties of Nd2Fe14B based magnets compared to measured properties, if their microstructure has been quantitatively analyzed by TEM/EELS investigations.



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