United States

With the rapid improvement of electromagnetic (EM) equipment, the high-frequency (HF) soft magnetic films have been studied intensively as HF components such as a film type inductor, an electromagnetic noise suppressor sheet, and so on.[1, 2] In particular, the nano-granular films are well-known as one of the best choices as HF components, which can prevent the ensuing plunge in electrical resistivity as ferromagnetic resonance frequency (f&lt;sub&gt;FMR&lt;/sub&gt;) increases. Herein, we select Co-Sr-F nano-granular films as the material of HF components and investigate their structure and magnetic properties in detail.&lt;br/&gt;The structure is nanocomposite, that is, Co nano-granules are evenly dispersed in a ceramic matrix. TEM observations indicate Co nano-granules change from a spherical to a columnar shape as the Co content increases. The electrical resistivity decreases from 10&lt;sup&gt;9&lt;/sup&gt; to 10&lt;sup&gt;4&lt;/sup&gt; μΩ*cm with a steep around 50~55 at.% of Co content as the Co content increases because of the change in the morphology of the film.&lt;br/&gt;In the range of Co content above 50 at.%, their coercivities are obtained and their saturation magnetizations (Ms) increase linearly(Fig.1). These results indicate that the films are ferromagnetic in the range of Co content above 50 at.%. To clarify f&lt;sub&gt;FMR&lt;/sub&gt; of these films, the change in permeability of these films with frequency is measured, and the observed f&lt;sub&gt;FMR&lt;/sub&gt; is summarized in Fig. 2 as a function of Co content. For Co content between 51~55 at.% (stage I), f&lt;sub&gt;FMR&lt;/sub&gt; remains constant around 4.8 GHz, while, for Co content above 55 at.% (stage II), f&lt;sub&gt;FMR&lt;/sub&gt; increases to 12 GHz monotonically. These behaviors can be explained by the change in the morphology of Co nano-granules. Namely, in stage I, as Co nano-granules are spherical, Kittel formula[3] is expressed as f&lt;sub&gt;FMR&lt;/sub&gt;=γH&lt;sub&gt;z&lt;/sub&gt; (γ is the gyromagnetic ratio). In stage II, as Co nano-granules are columnar, Kittel formula is described as f&lt;sub&gt;FMR&lt;/sub&gt;=γ(H&lt;sub&gt;z&lt;/sub&gt;+1/2M&lt;sub&gt;S&lt;/sub&gt;) and f&lt;sub&gt;FMR&lt;/sub&gt; increases linearly with the increase of Ms. Therefore, these results demonstrate f&lt;sub&gt;FMR&lt;/sub&gt; and film morphology correlates each other apparently, and suggest that Co-Sr-F nano-granular films are one of the candidates for HF components.

![](https://assets.underline.io/uploads/markdown_image/1/image/95284d1c80b5b322b200c42bcb5efff8.jpg)

Fig. 1 Magnetization curves of Co-Sr-F nano-granular thin film.


![](https://assets.underline.io/uploads/markdown_image/1/image/bfe412a99934f4776922a184262e4281.jpg)

Fig. 2 The dependence of fFMR on Co content.

2022 Joint MMM-INTERMAG

Relationship between morphology and soft-magnetic properties of Co-Sr-F nano-granular films

The 15th Joint MMM-INTERMAG Conference (2022 Joint) is sponsored jointly by AIP Publishing and the IEEE Magnetics Society. Members of the international scientific and engineering communities interested in recent developments in fundamental and applied magnetism are invited to attend and contribute to the technical sessions. The technical program will include invited and contributed papers in oral and poster sessions, invited symposia, a plenary session, and an evening session, with about 1500 presentations overall. This Conference provides an outstanding opportunity for worldwide participants to meet their colleagues and collaborators and discuss developments in all areas of magnetism research.

The 2022 Joint Conference will offer both in-person and prerecorded on-demand content.

For tickets to the event, please register at the following link: https://magnetism.org/register

Please register for the Joint MMM-Intermag conference to join the event.

This Conference provides an outstanding opportunity for worldwide participants to meet their colleagues and collaborators and discuss developments in all areas of magnetism research.

With the rapid improvement of electromagnetic (EM) equipment, the high-frequency (HF) soft magnetic films have been studied intensively as HF components such as a film type inductor, an electromagnetic noise suppressor sheet, and so on.[1, 2] In particular, the nano-granular films are well-known as one of the best choices as HF components, which can prevent the ensuing plunge in electrical resistivity as ferromagnetic resonance frequency (fFMR) increases. Herein, we select Co-Sr-F nano-granular films as the material of HF components and investigate their structure and magnetic properties in detail. The structure is nanocomposite, that is, Co nano-granules are evenly dispersed in a ceramic matrix. TEM observations indicate Co nano-granules change from a spherical to a columnar shape as the Co content increases. The electrical resistivity decreases from 109 to 104 μΩ*cm with a steep around 50~55 at.% of Co content as the Co content increases because of the change in the morphology of the film. In the range of Co content above 50 at.%, their coercivities are obtained and their saturation magnetizations (Ms) increase linearly(Fig.1). These results indicate that the films are ferromagnetic in the range of Co content above 50 at.%. To clarify fFMR of these films, the change in permeability of these films with frequency is measured, and the observed fFMR is summarized in Fig. 2 as a function of Co content. For Co content between 51~55 at.% (stage I), fFMR remains constant around 4.8 GHz, while, for Co content above 55 at.% (stage II), fFMR increases to 12 GHz monotonically. These behaviors can be explained by the change in the morphology of Co nano-granules. Namely, in stage I, as Co nano-granules are spherical, Kittel formula[3] is expressed as fFMR=γHz (γ is the gyromagnetic ratio). In stage II, as Co nano-granules are columnar, Kittel formula is described as fFMR=γ(Hz+1/2MS) and fFMR increases linearly with the increase of Ms. Therefore, these results demonstrate fFMR and film morphology correlates each other apparently, and suggest that Co-Sr-F nano-granular films are one of the candidates for HF components.

![](https://assets.underline.io/uploads/markdown_image/1/image/95284d1c80b5b322b200c42bcb5efff8.jpg)

Fig. 1 Magnetization curves of Co-Sr-F nano-granular thin film.


![](https://assets.underline.io/uploads/markdown_image/1/image/bfe412a99934f4776922a184262e4281.jpg)

Fig. 2 The dependence of fFMR on Co content.

poster

The anomalous Nernst effect (ANE), one of the long-studied thermomagnetic effects, has been regarded as a promising next-generation energy harvesting technology for large-area and flexible devices. However, since the ANE power is too short for practical use, it is necessary to enhance ANE and many ferromagnetic materials have been widely investigated [1]. We experimentally investigated the anomalous Nernst effect (ANE) in an Fe3Si film whose ANE was predicted to be large, based on the topological band structure [2]. We also measured the Seebeck and anomalous Hall effects to separate the ANE term from the Hall effect of the carrier flow induced by the Seebeck effect. The sample structure and measurement system are shown in Fig. 1. In addition to Fe3Si, Fe2Si, FeSi, and FeSi2 50nm films were fabricated on SiO2 substrate by co-sputtering and annealed in vacuum at 1123K for 1 hour. Figure 2 shows the ANE coefficient as a function of Si composition in Fe-Si compounds. The ANE coefficients were estimated as 1.0 and 0.5 µVK-1 for the Fe3Si and Fe2Si samples, respectively. These values are much larger than the ANE coefficient of film Fe, whereas Fe3Si and Fe2Si both have a smaller saturation magnetization than Fe. In general, the Nernst coefficient can be decomposed into two terms: Syx= ρxxαyx - tanθAHESxx. Here, the first term S1 exhibits the intrinsic ANE term that converts heat flow into a transverse voltage, and the second term S2 reflects the voltage originating from the Hall effect of the carrier flow induced by the Seebeck effect during the anomalous Nernst effect. From Fig. 2, it was found that the first term S1 was dominant in the ANE improvement of Fe3Si, suggesting that the ANE of Fe3Si is enhanced because of its band structure, as expected from the theoretical calculation. Fig.1 Schematics of the sample structure and ANE measurement configuration. Fig.2 Negative value of the ANE coefficient Sxy, the first term S1 , and the second term S2 as a function of Si composition in Fe-Si compounds.

![](https://assets.underline.io/uploads/markdown_image/1/image/1a38d99e3e16bb20f0ad9211f86d83f3.jpg)

Fig.1 Schematics of the sample structure and ANE measurement configuration.

![](https://assets.underline.io/uploads/markdown_image/1/image/2ec8641a0197aa716c6bbd15067d45b9.jpg)

Fig.2 Negative value of the ANE coefficient Sxy, the first term S1 , and the second term S2 as a function of Si composition in Fe-Si compounds.

Anomalous Nernst effect in Fe-Si alloy films

Introduction The Spheroidal graphite cast iron is used for high-strength parts of large heavy machinery. The cementite (Fe3C) may be contained in cast iron during the casting process. Since the strength is reduced if the cemenite is contained in the cast iron, the evaluation of the cementite content is important. The permeability and conductivity of the cementite domain are less than that of the domain in the cast iron without cementite. It is possible to evaluate the cemenite content using an electromagnetic field. However, the flux density is also influenced by the changing distance (lift-off: Lo) between the cast iron and the inspection sensor. Since the surface of the cast iron may be coated with rust preventive, it may not be possible to determine the exact Lo. In this paper, the inspection method for estimating the cementite content and Lo at the same time is proposed. Inspection model and tesults Fig.1 shows the inspection model. The sensor is composed of an AC excition coil with 10 kHz and 2A, a mangetic yoke and a detection coil. The B-H curves of the cast iron with and without cementite are shown in Fig.2. The conductivities of the cast iron with and without cementite are 1.9 x 106 S/m and 1.63 x 106 S/m, respectively. The permeability and conductivity of the cast iron with cementite are smaller than those of cast iron without cementite. Fig.3 shows a complex plane of the output voltage in a detection coil by changing the Lo and the cementite content. This figure shows the real VRe and imaginary VIm components of the output voltage. The output voltage due to the changes of the Lo and the cementite content is distinguished even if the ampulitude output voltage is the same value. In this resarch, when both cementite content and Lo are unknown, these values are estimated by the linear interpolation using this complex plane in Fig.3. Table 1 shows the estimation results of both unknown cementite content and Lo. This table shows that the actual cementite content and Lo are mostly estimated.

![](https://assets.underline.io/uploads/markdown_image/1/image/7c4ac47e52cadcb350db65ae15c0003e.jpg)

![](https://assets.underline.io/uploads/markdown_image/1/image/2d75af51f1a00b068de99c28bbed5634.jpg)

Electromagnetic evaluation method for both air-gap distance of non-contact sensor and cementite content inside spheroidal graphite cast iron

Electromagnetic evaluation method for both air-gap distance of non-contact sensor and cementite content inside spheroidal graphite cast iron

Recently, studies on the Y-type hexaferrites are being actively conducted because they exhibit multiferroic properties. Y-type hexaferrite is being used to high-density memories, wireless communication devices, etc. Therefore, to utilize it in these various fields, research on various characteristic changes through ion substitution is attracting attention [1]. Sr substituted Y-type Barium hexaferrite increased the saturation magnetization (Ms) and coercivity (Hc ) [2]. Nonmagnetic Al ion substitution at BaSrCo2Fe12O22 stabilized the spin structure [3]. This study, we have investigated the various effect of nonmagnetic Mg ion doping at Ba2Co2Fe12O22. Polycrystaline Ba2Co2-xMgxFe12O22 (x = 0.0, 0.1, 0.3, 0.5) was synthesized by solid state reaction method. We used XRD to analyze the crystal structure of the sample and analyzed the patterns with Rietveld refinement using the Fullprof. To measure magnetic properties, we used VSM and Mössbauer spectroscopy. We measured M-T and M-H values using VSM. The M-T experiments and Mössbauer experiments were conducted from 4.2 to 295 K. The Mössbauer spectra were fitted the six Lorentzian sextets. The Ba2Co2-xMgxFe12O22 were analyzed as hexagonal in the R-3m space group. We observed that the lattice constants a0 and c0 decreased as the concentration of Mg increased. This is because the ionic radius Mg (0.72 Å) is smaller than that of Co (0.745 Å). In the result of M-T experiment, we found the spin reorientation temperature (Ts). Ts were 215, 212, 209 and 202 K at x = 0.0, 0.1, 0.3 and 0.5, respectively. The Mössbauer spectra were analyzed by six sites of Fe. Each lines represented the six different sites of Fe (3bVI, 6c*IV, 6cVI, 18hVI, 6cIV, and 3aVI). The result of the analysis, the magnetic hyperfine field (Hhf) of 3bVI site was largest. Hhf and the quadrupole splitting values showed abrupt changes at Ts. The isomer shift values were maintained between 0.1 ~ 0.4 mm/s, indicating that Fe exhibited the Fe3+ ion state at all temperatures. The Hhf values decreased with increasing Mg doping. Along with the decrease of Ms and Hc in the M-H experiment, these results can be explained by the substitution of nonmagnetic Mg ion for magnetic Co ion.

Investigation of Mg doped Y-type Barium hexaferrite using Mössbauer spectroscopy

Microwave spin resonance behaviour of these mixed ferrites are of key consideration for various applications.Mixed ferrites based magnetic nanofluids have a potential candidature in various biomedical and spintronics filed like magnetic fluid hyperthermia, MRI ,optical sensor,switches and targeted drug delivery.In this work, a series of zinc doped Fe3O4magnetic nano-fluids with different Zn concentrations represented as ZnxFe3-xO4 (x=0,0.1,0.2,0.3 & 0.4)were synthesized by the wet chemical co-precipitated techniqueand oleic acid is used as surfactant to prevent the agglomeration of magnetic nanoparticles.Structural, optical, elastic and spin dynamics properties of these ferrofluids have been investigated using different sophisticated characterization techniques such as XRD, HRTEM, SEM, FTIR,UV and EPR etc. The structural and Rietveld refinement was carried out by the XRD data and the result confirms that single cubic spinel phase belongs to Fd3m (227) space group and the average crystallite size calculated from the XRD data varies from 12 to 15 nm. HRTEMstudies revealed that the particles are spherical in nature and mean particle size varies from 15 to 20 nm and all samples are polycrystalline in nature. SEM result was also demonstrated the surface morphology of magnetic particle is spherical in shape with slight agglomeration. FTIR spectroscopy showed the molecular dynamics and the formation of cubic spinel phase of frequency peaks at 535 cm-1and 420 cm-1respectively and also other different functional group which gives the evidences that oleic acid are present on the surface of MNPs.The UV-Visible measurement gives the estimate of the band gap of the materials which lies between(2.2 to 2.8, 3.1 and 3.8 e V) of the all the sample obtained from optical absorption spectra fitting by Tauc plot method. The room temperature microwave spins resonance studies was carried out by using X-band (9.8GHz) EPR spectrometer and calculated various spin resonance parameters[1,2]. In sample compositions the broad resonance signal is observed and enhancement of peak to peak line width is perceived due to the strong super-exchange interaction between the magnetic ions through oxygen ions[1-3].

![](https://assets.underline.io/uploads/markdown_image/1/image/8b32fddf83acb76352c659c6c766fe84.jpg)

Finite size effect on Structural, optical, elastic and spin resonance properties of oleic acid coated ZnxFe3-xO4 (0.4≤x≤0) ferrite nanofluids

Ferrofluids that are colloidal suspensions of ferromagnetic particles suspended in oil or water can be manipulated by an external magnetic field. The ferrofluid droplet would break up into numerous subscale droplets, which is referred to as Rosensweig instability, whose pattern depends on the field conditions. Fig. 1 shows an oil-based ferrofluid (EMG905) droplet breaks up into various patterns of subdroplets in the different field strengths. Fig.1(a) shows a ferrofluid droplet splits up into a few subdroplets under a field strength of 17428 A/m. When an EM wave generated by a 200 mw power laser pointer transmits to the surface of a ferrofluid droplet with an incident angle of θi=30°, the reflection of the EM wave remains significant. When the incident angle increases to of θi=45° and θi=60°, the reflection energy of the EM wave are eliminated and diminished, respectively, due to the scattering effect. The same scenario is seen in the case shown in Fig.1(b), when the field strength is increased to 34300A/m, which results in more numbers of subdroples. It is noted that all the reflections of EW wave are weakened. Fig.1(c) shows the reflection waves for the incident angle of θi=30° and θi=60° decay when the field strength is increased to 45360 A/m and much more subdroples are created. However, the reflection energy of EM wave for the θi=45° increases slightly compared to the cases shown in Figs. 1(a) and 1(b). The experimental results show that ferrofluid droplet subjected to an external magnetic field is applicable to be a smart shield that can absorb and scatter the energy of EM wave and reduce the EM pollution effectively. The effects of roughness, diameter, and composition of ferrofluid droplets on the EM wave energy loss will be discussed in the full manuscript. The quantitative measurement of the reflection loss will be demonstrated as well.

![](https://assets.underline.io/uploads/markdown_image/1/image/e3f005ec18a07689d9cb3111ad1e71c6.jpg)

Fig.1 Magnetic-field-induced ferrofluid droplet breaks up into various numbers of subdroplets under a magnetic field strength of (a) H=17428 A/m (b)H=34300 A/m (c)H=45360 A/m. The number of the ferrofluid subdroplets increases with the field strength. The reflection energy of the EM wave varies with the patterns of the ferrofluid subdroplets and the incident angles.

The Effect of Rosensweig Instability of a Ferrofluid Droplet on the Electromagnetic Wave Scattering

Polycrystalline lanthanum strontium manganese oxide (LSMO), La1-xSrxMnO3 (x = 0.1–0.4) nanoparticles (NPs) exhibit interesting size dependent structural and magnetic. They find interesting applications in catalysis, biomedicine and data storage [1]. LSMO NPs have attracted considerable attention in recent years because of their tunable novel magnetic properties [2], single domain superparamagnetic structure with near room temperature Curie point (Tc) [3]. Properties of LSMO NPs are strongly correlated with the extent of Sr-doping at La site, their particle size and extent to which different crystallographic phases (rhombohedral / orthorhombic) present. The aim of this study is to understand the effect of Sr-doping on structural and magnetic properties of LSMO NPs synthesized via sol-gel auto combustion route. Their structural and magnetic properties were investigated by X-Ray diffraction coupled with Rietveld refinement and vibrating sample magnetometer. The Rietveld refinement of diffractograms revealed that irrespective of Sr-doping, LSMO NPs were crystallized in rhombohedral (R-3c) and orthorhombic (Pbnm) mixed phases. The rhombohedral phase appears to be the dominant crystalline phase. VSM of Sr-doping LSMO NPs exhibits single domain superparamagnetic structure. With the decrease in Sr-doping, the saturation magnetization (Ms) of LSMO NPs also decreases (Fig. 1), while their Tc remained constant at 360 + 10 K. In order to establish the correlation between the structural and magnetic properties of LSMO NPs, M-H curves were fitted with the modified Langevin function [4, 5]. From the best fits, Ms, dm (magnetic particle size) and s (polydispersity index) were determined. It was observed that with decrease in Sr-doping, both dm, and s decreased also resulting in reduction in their Ms. The changes in their magnetic properties are in good correlation with the relative changes in the rhombohedral and orthorhombic phases. Thus, through Sr-doping, magnetic properties of LSMO NPs can be tuned by controlling the crystallographic phase fractions.

![](https://assets.underline.io/uploads/markdown_image/1/image/a1b32c80db8f54417e667cf808300c7f.jpg)

Fig. 1 Effect of Sr-doping on the Ms of La1-xSrxMnO3 (x = 0.1 -0.4) nanoparticles

![](https://assets.underline.io/uploads/markdown_image/1/image/0807e7c978d5ad55d841ac4b29bd0d21.jpg)

Fig. 2 Ms–H of La1-xSrxMnO3 (x = 0.1 -0.4) nanoparticles fitted with modified Langevin function

Effect of Sr-doping on Structural and Magnetic Properties of LSMO nanoparticles Prepared by Sol-Gel Auto Combustion Method

Yttrium iron garnet ferrites, Y3Fe5O12 (YIG), have been attracted considerable attention due to its technological importance in various applications such as high quality filters and magneto-optical devices [1]. It is well known that the nanoferrites may exhibit unique structural, magnetic and optical properties far different from those of their bulk counterparts because of low dimensionality and quantum confinement effect [2]. In addition, the correlation of the doping and grain size effects on functional behavior of YIG system has not yet been completely established. In this work, therefore, we prepare a series of Y3Fe5-xGaxO12 (0 ≤ x ≤ 2) nanoparticles by the sol-gel method to systematically study the effect of Ga-substitution on their magnetic and dielectric properties. The crystallographic phase of each sample was confirmed by observing the XRD patterns. Ga substitutions slightly modify the value of the lattice parameters. This could be ascribed to the smaller ionic radius of Ga3+ than that of Fe3+, which confirms that the Ga is successfully substituted in the lattice of YIG. The grain size of these samples was found in the nano regime. In addition, the non-linear change of structure parameters for Y3Fe3.5Ga1.5O12 sample has been observed. This behavior may be due to the existence of oxygen vacancies in garnet structure. The oxygen vacancies would induce Fe2+ ions then give rising on the value of the lattice constants. It was also found that the dielectric constant increases with increasing Ga-content. Furthermore, the saturation magnetization was decreased whereas coercivity increased with the Ga substitution in YIG nanoferrite. The magnetization decreased at the lattice sites and this is due to Ga3+ substitution instead of Fe3+ in the tetrahedral position. Another reason for the decrease in magnetization is due to the substitution of smaller ionic radius of Ga in nanosized YIG. It is noticed that the coercivity increased with Ga substitution in YIG nanoferrite. This characteristic could be attributed to the decrease in the grain size close to single domain. The soft character of the Ga-substituted YIG nanoferrites with moderate magnetization suggested the use of these nanoferrites for future applications.

Effect of Ga-substitution on magnetic and dielectric properties of nanosized yttrium iron garnet ferrites

Due to the high permeability and low iron loss properties of Grain-Oriented(GO) silicon steel along the rolling direction, many researchers have tried to optimize traction motors by using this materials[1]. It is known that during the work process of the motor, there is a rotating magnetic field in the yoke and a pulsating magnetic field in the tooth of the stator, so that a segmented structure could be applied to take advantage of the GO material[2]. The rolling direction of the GO material is consistent with the direction of the applied magnetic field. Most of the magnetic domains in the GO sheet are in the same direction as magnetic field. The expansion of the magnetic domain will cause the increase of flux density, but because there are fewer non-zero magnetic domains, the magnetic domains rotate. The increment of flux density caused is small, and the energy consumed is not much. It will eventually rotate to the rolling direction and reach the saturation state, thereby reaching the maximum magnetic induction value [3]. However, even if the magnetic field in the tooth part is pulsating, the flux is not always along the rolling direction of the GO material strictly throughout the work process, which will affect the design and the final performance of the motor fabricated. So the magnetic properties of the GO material along the direction different from the rolling direction are still needed to be studied. In our experiment, we test the magnetic properties of the GO material B23R080 with different deflection angle along the rolling direction by Epstein method [4]. And a strange behavior of the BH curves we obtained appeared. This paper will consist of 5 parts: part I is the introduction; in part II we will present our test results of B23R080; part III will be the explanation of the strange performance of the test results; part IV will introduce the influence and our advices to the motor design and the part V will be the conclusion.

![](https://assets.underline.io/uploads/markdown_image/1/image/a11d72882c293ba819f7aee14153ea3a.jpg)

B-H Curve

![](https://assets.underline.io/uploads/markdown_image/1/image/c65076693181e1737aeacc2709000402.jpg)

Iron Loss - Flux Density - Angle

Investigation of the Influence of the Anisotropic Magnetic Performance of the Grain-Oriented Silicon Steel on the Motor Design

Magnetocaloric refrigeration has emerged as an attractive candidate to replace conventional compression-based refrigeration systems in virtue of its higher Carnot efficiency and eco-friendlier refrigeration thereby replacing potent CFCs. This solid-state refrigeration can be exploited mainly for compact devices such as micro refrigerators, thermal diodes, regulators, and electronics where heat extraction is challenging. To facilitate the usage of magnetocalorics for such applications, 2D printing of magnetocaloric nanoparticle inks is versatile approach to generate custom structures. Among magnetocaloric materials, the FeRh alloy system demonstrates the largest magnetocaloric effect at first order (AFM-FM) phase transition at near-to-equimolar composition. Previous studies reveal that the synthesis of FeRh nanoparticles using conventional processes leads to undesired Fe/Rh core-shell structures and for a magnetocaloric response, a uniform near-to-equiatomic distribution of Fe and Rh within nanoparticles is critical. Here, we demonstrate a laser-based approach for the synthesis of FeRh nanoparticles1 and 2D sintering of a developed ink2. A Fe50Rh50 bulk target was ablated using an infrared picosecond-pulsed laser in organic solvents (acetone, acetonitrile, and ethanol) leading to the formation of paramagnetic solid solution Fe50Rh50 nanoparticles with reduced oxygen content (up to 5 at. %).1 The generated nanoparticles were used to formulate an ink (up to 1 wt.%) in ethanol and dispersed on PVP-coated glass substrates and were patterned using 532 nm CW laser. The 2D laser sintering facilitates the formation of pore-free custom structures and induces ultrafast partial phase transition from paramagnetic to ferromagnetic and antiferromagnetic phases.2

Synthesis and printing of Fe50Rh50 nanoparticle inks– a laser-based route to generate magnetocaloric structures

The development of the electric vehicle makes a higher requirement to the torque/power density of the traction motors. It has been difficult to meet the requirements by using conventional silicon steels. Therefore, the application of “new” materials could become a breakthrough. In this paper, we research the properties and the application in traction motors of the Fe-Co-V alloy 1J22. Compared with conventional silicon steels, 1J22 has a higher saturation flux density, which enables the motor to have a higher torque density. However, the impact of stamping and shear stress during the processing progress greatly reduces the magnetic properties, which means the annealing processes is necessary and will change the magnetic performance significantly[1]. According to the Fe-Co binary alloy phase diagram[2], it can be seen that the annealing temperature cannot be higher than 910 degrees. For our experiment, the annealing temperature of 850 degrees is adopted. At the same time, hydrogen protection is applied to avoid the oxidation reaction. R. S. Sundar found that the magnetic performance with a holding time of 4 hours can reach an excellent level and when the temperature is above 750 degrees during cooling, slowly lower the temperature at a rate of 50 degrees/hour. At 730 degrees, an ordered phase will be produced [3], the short-range order in the disordered phase will grow up to form a long-range order which makes the dislocations difficult and leads to the poor ductility and the brittleness of the alloy. The saturated flux density (Bs) of Fe-Co binary alloy increases with the increase of Co content. When the Co content is 35%, Bs is 2.45T. When the Fe-Co atom ratio is close to 1:1, the magnetocrystalline anisotropy constant is about 0, which has the highest magnetic permeability. Dr. White’s team [2] added 2% V to the alloy to improve its brittleness. We use 1J22 material to develop a prototype with a rated power of 6kW and a rated speed of 4500rpm. The torque density of the prototype is increased by 14% compared with the conventional motor used silicon steel. This paper is divided into 4 parts: Magnetic properties test and metallographic observation; Motor design; Prototype manufacturing and test and conclusion.

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![](https://assets.underline.io/uploads/markdown_image/1/image/f0e907f6b5e4ded7acbe9650d566bc60.jpg)

Relationship between morphology and soft-magnetic properties of Co-Sr-F nano-granular films

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Anomalous Nernst effect in Fe-Si alloy films

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