France



Amorphous glass-coated microwires are among the excellent material that can be used in sensor and spintronic devices. The magnetization process is realized due to the fast domain wall propagation. The studies on domain wall dynamics showed that additional perpendicular magnetic field changes domain wall velocity [1, 2]. Moreover, after the rotation of the microwire in the perpendicular magnetic field the difference in the domain wall velocity is even more significant [3].&lt;br/&gt;&lt;br/&gt;However, the obtained results are contrary to the expectations based on previous knowledge. Due to the cylindrical shape of the wires, no change in domain wall velocity was expected for different rotations. The results are explained in terms of the gradient of the perpendicular magnetic anisotropy in the cross-section of the wire. The gradient is induced to the microwire during the fabrication process. The water stream causes additional induced stresses due to the cooling of the microwire from one side (Fig. 1a). The direct observation of such stresses in the cross-section of the wire is not possible due to the amorphous structure of the microwires. However, it is clearly visible when the sample is annealed above the crystallization temperature (Fig. 1b).&lt;br/&gt;&lt;br/&gt;In this work, we present the domain wall (DW) dynamics studies on the sample (Fe&lt;sub&gt;76&lt;/sub&gt;Si&lt;sub&gt;9&lt;/sub&gt;B&lt;sub&gt;10&lt;/sub&gt;P&lt;sub&gt;5&lt;/sub&gt;) as-cast and annealed below the crystallization temperature (at 450 °C) (Fig. 2). The DW velocity &lt;i&gt;v&lt;/i&gt; is described by the following relation [4]:&lt;br/&gt;&lt;i&gt;v = S(H - H&lt;sub&gt;0&lt;/sub&gt;)&lt;/i&gt; (1)&lt;br/&gt;where &lt;i&gt;S&lt;/i&gt; is DW mobility, and &lt;i&gt;H&lt;sub&gt;0&lt;/sub&gt;&lt;/i&gt; critical magnetic field.&lt;br/&gt;&lt;br/&gt;The DW velocity of the as cast sample is linearly increasing for different angles of rotation &lt;i&gt;θ&lt;/i&gt; (Fig.2a). For &lt;i&gt;θ&lt;/i&gt; &lt;i&gt;= 180°&lt;/i&gt;, DW velocity increases up to 350 A/m with mobility &lt;i&gt;S = 1.44 m&lt;sup&gt;2&lt;/sup&gt;s&lt;sup&gt;-1&lt;/sup&gt;A&lt;sup&gt;-1&lt;/sup&gt;&lt;/i&gt;. From 350 A/m, the DW mobility is &lt;i&gt;S = 24.9 m&lt;sup&gt;2&lt;/sup&gt;s&lt;sup&gt;-1&lt;/sup&gt;A&lt;sup&gt;-1&lt;/sup&gt;&lt;/i&gt;. However, after annealing, the DW motion is observed &lt;i&gt;from H&lt;sub&gt;axial&lt;/sub&gt; = 550 A/m&lt;/i&gt; with the mobility &lt;i&gt;S = 1.73&lt;/i&gt; &lt;i&gt;m&lt;sup&gt;2&lt;/sup&gt;s&lt;sup&gt;-1&lt;/sup&gt;A&lt;sup&gt;-1&lt;/sup&gt; &lt;/i&gt;up to 700 A/m (Fig.2b). DW mobility from&lt;i&gt; H&lt;sub&gt;axial&lt;/sub&gt; = 700 A/m &lt;/i&gt;is incomparably smaller in comparison to the case before annealing, with the value&lt;i&gt; S = 6.79 m&lt;sup&gt;2&lt;/sup&gt;s&lt;sup&gt;-1&lt;/sup&gt;A&lt;sup&gt;-1&lt;/sup&gt;.&lt;/i&gt;&lt;br/&gt;&lt;br/&gt;When the sample is annealed, it leads to the release of the stresses induced in the cross-section of the microwire. Annealing causes the homogenization of the sample, and as a result, a significant decrease in DW mobility is observed. Thus, an effective mechanism for suppressing the angular dependence of DW mobility in a perpendicular magnetic field is annealing under suitable conditions.&lt;br/&gt;&lt;br/&gt;Acknowledgements:&lt;br/&gt;This work was supported by Slovak Grant Agency VEGA 1/0053/19, VEGA 1/0195/17; Slovak Grant Agency grant number APVV-16-0079, APVV-17-0184, APVV SK-FR-2017-024 and Pavol Jozef Šafárik University internal grant system VVGS-2016-320.

**References:**

[1] R. Varga et al., Physica Status Solidi A, Vol. 213, p. 356–362 (2016).&lt;br/&gt;[2] K. Richter et al., Applied Physics Letters, Vol. 96, 182507 (2010).&lt;br/&gt;[3] L. Fecova, K. Richter, and R. Varga, Acta Physica Polonica A, Vol. 137 (5), p. 849-851 (2020).&lt;br/&gt;[4] V. Zhukova et.al, Journal of Applied Physics, Vol. 111, 07E311-1 (2012).

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/70d8ab1607609771a6973e4fac77b8eb.jpg)
Fig.1 Taylor-Ulitovski method of drawing the glass-coated microwire Fe&lt;sub&gt;76&lt;/sub&gt;Si&lt;sub&gt;9&lt;/sub&gt;B&lt;sub&gt;10&lt;/sub&gt;P&lt;sub&gt;5&lt;/sub&gt;, which is quenched by the water jet from one side in order to obtain the amorphous structure (a), and the stress distribution in the section of the amorphous wire annealed above crystallization temperature (b).

![](https://assets.underline.io/uploads/markdown_image/1/image/d4ca30e3a4acdb9987c890d60d17e064.png)
Fig.2 Domain wall velocity as a function of the axial magnetic field in the perpendicular magnetic field for the as-cast sample (a) and sample annealed below the crystallization temperature (b).

INTERMAG 2021

 The annealing effect on domain wall dynamics in wires with induced gradient of the perpendicular anisotropy

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Amorphous glass-coated microwires are among the excellent material that can be used in sensor and spintronic devices. The magnetization process is realized due to the fast domain wall propagation. The studies on domain wall dynamics showed that additional perpendicular magnetic field changes domain wall velocity [1, 2]. Moreover, after the rotation of the microwire in the perpendicular magnetic field the difference in the domain wall velocity is even more significant [3]. However, the obtained results are contrary to the expectations based on previous knowledge. Due to the cylindrical shape of the wires, no change in domain wall velocity was expected for different rotations. The results are explained in terms of the gradient of the perpendicular magnetic anisotropy in the cross-section of the wire. The gradient is induced to the microwire during the fabrication process. The water stream causes additional induced stresses due to the cooling of the microwire from one side (Fig. 1a). The direct observation of such stresses in the cross-section of the wire is not possible due to the amorphous structure of the microwires. However, it is clearly visible when the sample is annealed above the crystallization temperature (Fig. 1b). In this work, we present the domain wall (DW) dynamics studies on the sample (Fe76Si9B10P5) as-cast and annealed below the crystallization temperature (at 450 °C) (Fig. 2). The DW velocity v is described by the following relation [4]: v = S(H - H0) (1) where S is DW mobility, and H0 critical magnetic field. The DW velocity of the as cast sample is linearly increasing for different angles of rotation θ (Fig.2a). For θ = 180°, DW velocity increases up to 350 A/m with mobility S = 1.44 m2s-1A-1. From 350 A/m, the DW mobility is S = 24.9 m2s-1A-1. However, after annealing, the DW motion is observed from Haxial = 550 A/m with the mobility S = 1.73 m2s-1A-1 up to 700 A/m (Fig.2b). DW mobility from Haxial = 700 A/m is incomparably smaller in comparison to the case before annealing, with the value S = 6.79 m2s-1A-1. When the sample is annealed, it leads to the release of the stresses induced in the cross-section of the microwire. Annealing causes the homogenization of the sample, and as a result, a significant decrease in DW mobility is observed. Thus, an effective mechanism for suppressing the angular dependence of DW mobility in a perpendicular magnetic field is annealing under suitable conditions. Acknowledgements: This work was supported by Slovak Grant Agency VEGA 1/0053/19, VEGA 1/0195/17; Slovak Grant Agency grant number APVV-16-0079, APVV-17-0184, APVV SK-FR-2017-024 and Pavol Jozef Šafárik University internal grant system VVGS-2016-320.

**References:**

[1] R. Varga et al., Physica Status Solidi A, Vol. 213, p. 356–362 (2016). [2] K. Richter et al., Applied Physics Letters, Vol. 96, 182507 (2010). [3] L. Fecova, K. Richter, and R. Varga, Acta Physica Polonica A, Vol. 137 (5), p. 849-851 (2020). [4] V. Zhukova et.al, Journal of Applied Physics, Vol. 111, 07E311-1 (2012).

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/70d8ab1607609771a6973e4fac77b8eb.jpg)
Fig.1 Taylor-Ulitovski method of drawing the glass-coated microwire Fe76Si9B10P5, which is quenched by the water jet from one side in order to obtain the amorphous structure (a), and the stress distribution in the section of the amorphous wire annealed above crystallization temperature (b).

![](https://assets.underline.io/uploads/markdown_image/1/image/d4ca30e3a4acdb9987c890d60d17e064.png)
Fig.2 Domain wall velocity as a function of the axial magnetic field in the perpendicular magnetic field for the as-cast sample (a) and sample annealed below the crystallization temperature (b).

poster

I. INTRODUCTION Magnetorheological (MR) fluids are suspensions of soft-magnetic particles dispersed in a non-magnetic liquid medium, such as silicone oil and mineral oil [1]. Their rheological behaviors can be tuned depending on either the presence or the absence of the applied magnetic field strength. Without an applied magnetic field, they behave like a Newtonian fluid while in the presence of the magnetic field, they become a solid-like a state [2], due to the fact that the dispersed magnetic particles are magnetically polarized and then form a chain structure [3]. When the external magnetic field is removed, they return to an original liquid-like state immediately. Based on this tunable and reversible characteristics, their potential applications cover the areas of robotics, haptic devices, and mechanical systems [4]. As for the MR material, carbonyl iron (CI) microspheres have been widely used because of their high saturation magnetization. However, their high density intrinsically possesses a sedimentation problem [5]. To improve this problem, several methods have been employed such as an introduction of additive particles and coating the CI with either polymers or inorganics [6]. In this work, as an additive material, zinc ferrite nanoparticles were synthesized by a surfactant-assistant solvothermal method and then added into CI-based MR fluid. By adding these particles with high magnetism to MR fluid consisting of fine CI particles, the MR effect is expected to be improved [7]. II. EXPERIMENT The ZnFe2O4 nanoparticles were synthesized by solvothermal synthesis method. Ferric chloride hexahydrate (5.4g) and zinc chloride (1.36g) were put into 200 ml ethylene glycol with stirring using a magnetic bar. After 45 min, the solution turned to be transparent yellow. Both sodium acetate (14.4g) and polyethylene glycol(4g) were then added, and reacted in an autoclave at 200°C for 12 h. The particles were separated using a magnet and washed several times with ethanol. Finally, the synthesized zinc ferrite nanoparticles were dried in a vacuum oven for a day. Morphology of nanoparticles was observed by scanning electron microscope. The CI particles (CM grade, BASF, average particle size: 4.5 m, density: 7.8 g/cm3) were then used as a main component for the MR fluids. The 0.5wt% of was added into 50wt% of CI based MR fluid, while CI-based MR fluid (50 wt%) dispersed in silicone oil (viscosity of 100cS) was also prepared for the comparison. Their MR characteristics were measured using a rotational rheometer under various magnetic field strengths. III. RESULT AND DISCUSSION Figure 1 presents SEM image of the morphology of particles, with a smooth surface and particle size distribution in 300-500nm range. The density of zinc ferrite particles was measured to be 4.8 g/cm3 by a pycnometer. Rheological response of shear stress as a function of shear rate of both MR fluids is presented in Figure 2 under a magnetic field strength range from 0 to 341 kA/m. Without a magnetic field, the MR fluid behaves like a Newtonian fluid. However when magnetic field strength was applied, the shear stress increased as the shear rate increased. MR properties of the CI/ZnFe2O4 based MR fluid (50/0.5wt %) showed a higher shear stress than that of CI-based MR fluid. Under the magnetic field applied, both MR fluids with and without an additive show similarly a wide plateau region which is attributed to the formed columns due to the strong dipole-dipole interaction among the magnetic particles. Additionally, we also measured the sedimentation ratio to confirm the role of zinc ferrite as an additive material for MR fluids through a Turbiscan optical analyser system. The CI-based MR fluid had a faster sedimentation rate than the CI/ZnFe2O4 based MR fluid, indicating that the dispersion stability of CI/ZnFe2O4 based MR fluids increased as compared to the CI based MR fluids. Improved dispersion stability is thought due to the fact that the nanoparticles fill the free space between the CI particles at the same time partially being coated on the surface of the CI particles, contributing to flow resistance. Therefore, in this work, the positive role of zinc ferrite as a proper additive for the CI based MR fluid is confirmed.

**References:**

[1] S. E. Premalatha, R. Chokkalingam and M. Mahendran, Am. J. Polym. Sci, 2, 50 (2012). [2] J. de Vicente, D. J. Klingenberg and R. H.Alvarez, Soft Matter, 7, 3701 (2011) [3] M. J. Hato, H. J. Choi and H. H. Sim, Colloids Surf. A-Physicochem. Eng. Asp, 377, 103 (2011) [4] C. Y. Gao, M. W. Kim, D. H. Bae, Polymer, 125, 21 (2017) [5] J. E. Kim, H. J. Choi, IEEE Trans. Magn, 47, 3173 (2011) [6] Y. Z. Dong, W. J. Han and H. J. Choi, J. Ind. Eng. Chem. 93, 210 (2021) [7] S. H. Piao, H. S. Chae, and H. J. Choi, IEEE Trans. Magn. 51,4600704 (2015)

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/1f91e2fab6913903916978f67ff06c37.jpg)
Fig. 1 SEM images of ZnFe2O4 

![](https://assets.underline.io/uploads/markdown_image/1/image/3b0befb13c37f7fd19f325005c241177.jpg)
Fig. 2 Shear stress curves of both pure CI (closed) and CI/ZnFe2O4 (open) MR fluids at different magnetic field strengths

 Enhanced Magnetorheological Response of Particle Added Carbonyl Iron Suspension

I. INTRODUCTION Actively tunable smart magnetorheological (MR) fluids consisting of soft-magnetic particles suspended in nonmagnetic liquids like mineral oil or silicone oil [1], [2], have drawn extensive attentions with their many potential applications in mechanical engineering, biomedicine, pigments, and even in aerospace devices due to their controllable capability. They exhibit reverse and tunable rheological properties from Newtonian fluid-like to solid-like through applied magnetic field strengths employed within milliseconds order. Among extensive potential magnetic particles for their MR applications, soft-magnetic carbonyl iron (CI) microspheres possessing a large saturation magnetization value, proper size, and large permeability have brought lots of interests [3], [4]. However, CI particles are known to intrinsically possess the limitation of their usage with their much higher particle density than of the non-magnetic fluids, which may easily cause the sedimentation in the MR fluids. In this study, poly(2-methylaniline)(PMAN)-CI core-shell structured particles were synthesized by a chemical grafting method with dopamine hydrochloride as a grafting agent to enhance repulsive interaction or to decrease distance among CI microspheres. Dopamine was coordinated on the surface of magnetic particles by electro-donating bidentate enediol, combined with magnetic particles through a bidentate ligand reaction [5]. At this point, the amine groups of dopamine-modified CI particles can be further modified as functional groups. The morphology of the fabricated core-shell structured particles was examined by transmission electron microscopy and scanning electron microscopy. In addition, the rheological properties of MR fluids were measured by using a rotational rheometer under various magnetic field strengths. II. EXPERIMENT Before PMAN coating, the surface of CI particles was modified with dopamine hydrochloride to improve the affinity between magnetic CI particles and PMAN coated shell. At first, CI particles were dispersed in DI-water, and dopamine hydrochloride was mixed with ultrasonic stirring reaction solution for 12 h to promote dopamine coating. The unattached dopamine was then flushed with excess deionized water and hexane. The CI particles of the surface coating were dried in vacuum for 24 h. The dopamine-modified CI particles were dispersed in deionized water under ultrasonication for 30 min. PMAN was coated by polymerizing 2-methylaniline via a chemical oxidation process induced by ammonia peroxide in an acidic environment. We then added the mixture to poly(vinyl alcohol) dissolved in di-water, transfered the reaction solution to the reactor, and cooled it down. Aniline and ammonia peroxide were added to the reactor. The reaction was kept for 24 h and stirred at 300 rpm. When the reaction was complete, the resulting product was separated using a magnet and dried in a vacuum for 24 h. III. RESULTS AND DISCUSSION The SEM images of CI/PMAN core-shell particles are shown in Figure 1, in which the CI/PMAN particles exhibit a larger particle size because of the PMAN coated shell, compared to a smooth surface of the pristine CI particles. The MR behaviors of CI/PMAN based MR suspension were carried out using a rotational rheometer in a controlled shear rate mode under a series of applied magnetic field strengths from 0 to 342 kA/m. The shear stress increases with increasing shear rate, which implies that the MR fluid exhibits a Newtonian fluid-like behaviour without an external magnetic field as shown in Fig. 2. When the magnetic field was applied, the shear stress demonstrated a significant improvement because of the change from a liquid-like to solid-like behaviour of the MR fluid, followed by stepwise growth with the increase of magnetic field. For each magnetic field strength, the shear stress of MR suspension displayed a wide plateau region over the entire shear rate range. In addition, the shear stress with the external magnetic field of MR suspensions was also fitted with the Herschel-Bulkley model [6], [7] as follows: τ=τ0+KÝn where τ is the shear stress, τ0 represents the dynamic yield stress, is the shear rate, K and n represent the consistency index and power-law exponent, respectively. The relationship between the dynamic yield stressof PANI/CI and the magnetic field strength was observed by measuring the universal yield stress. Even though the saturation magnetization and density ofthe PMAN/CI particles were reduced by the introduction of a non-magnetic PMAN shell, their dispersion stability was observed to be improved according to the Turbiscan test by synthesizing the PMAN-coated CI particles. These results were attributed to the rough surface and low density of the core-shell structure PMAN/CI particles.

**References:**

[1] M. Mrlik, M. Ilcikova and V. Pavlinek, J. Colloid Interf. Sci., 396, 146 (2013). [2] D. J. Klingenberg and J. C. Ulicny, Int. J. Mod. Phys. B, 25, 911 (2011). [3] I. Bica, E. M. Anitas and L. Chirigiu, J. Ind. Eng. Chem. 56, 407 (2017). [4] F. F. Fang, Y. D. Liu and H. J. Choi, ACS Appl. Mater. Inter. 3, 3487 (2011). [5] C. J. Xu, K. M. Xu and H. W. Gu, J. Am. Chem. Soc. 126, 9938 (2004). [6] K. J. Son, Korea-Austral. Rheol. J. 30, 29 (2018). [7] Y. Seo and H. J. Choi, Korea-Austral. Rheol. J. 30, 317 (2018).

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/bec31a3e9edbef50d5575e1aa353a6e2.jpg)
Fig.1 SEM images of CI (inset) and CI/PMAN core-shell particles

![](https://assets.underline.io/uploads/markdown_image/1/image/221c24a25d3c5b897f0ef4474fbb4ef1.jpg)
Fig.2 Flow curve of shear stress for CI-PMAN MR fluid under various magnetic field strengths as a function of shear rate

 Fabrication and Magnetorheological Characteristics of Core-shell Typed Poly(2-methylaniline)/Carbonyl Iron Microspheres

Transcranial magnetic stimulation (TMS) is a neuromodulation therapy that can be used to treat neurological and psychiatric conditions and has been approved by the FDA for certain disorders [1]–[4]. Since TMS trials with humans are not always feasible, brain phantoms have been developed as ways of testing without actually stimulating the patient. Although a brain phantom has been developed for humans, a comparable brain phantom for rats or mice has not been created specifically for TMS or other neuromodulation techniques. An individualized brain phantom for rats is needed to accelerate the study of neuromodulation techniques, especially the measurement of induced electric field and voltages in the brain regions when stimulated by a time-varying magnetic field. The main objective of this paper is to develop an individualized, anatomically-accurate rat brain model for finite element simulation and a physical model for experimental measurement of stimulation strengths. We initially obtained magnetic resonance images (MRIs) from public databases to create the anatomically accurate brain models. The Waxholm Space Atlas of the Sprague Dawley rat brain was chosen as the MRI to be created into the preliminary phantom. Using the Skull Stripping tool from the BrainSuite software package, the brain was separated from the surrounding skull and skin. Both the original and skull-stripped brain NIFTI files were downsampled using AFNI software tools. The skull-stripped brain was then inputted as a reference mask into the Skull Stripper Python program, along with the downsampled original MRI [5]. The output was the final file, containing 3D information of the chosen rat brain. Using the 3D Slicer program, the final brain file was converted into a 3-dimensional STL file. The program Meshmixer was then used to reduce the file size and fix any model errors. The anatomically accurate individualized brain model was combined with a TMS coil designed for small animals in SolidWorks. An enclosure was also made that surrounded the coil and brain (serving as air in the simulation). The Maxwell 3D module in ANSYS finite element simulation software was then used to simulate the magnetic flux density and induced electric fields in the rat brain models. Fig. 1 inset shows the orientation of the brain and coil in the simulation. Fig. 1 and Fig. 2 show preliminary results of what is predicted for the physical phantom, with all the layers (skin, skull, and other tissues) hidden except the brain. We had assigned uniform conductivity of 0.2 S/m for the entire brain, a relative permeability of 1, and a relative permittivity of 12,000. A figure of eight coil was used on the top of the rat’s head with 1000A current supplied to the coil. The peak magnetic field of 1.22 T and 2.5 ×10-6A/m2 occurs on the surface of the brain below the center of the coil. We are currently in the process of developing a physical individualized, anatomically-accurate physical brain phantom using the above computation models. Work to consider white an grey matter separately in the model is currently in progress. We will use similar techniques as used in the development of our existing human brain phantoms [6], [7]. Using the phantom, we will systematically measure the stimulations strengths in different regions of the brain using several coils types. Acknowledgement: Authors would like to thank funding from Dean's Early Researcher Initiative (DERI) program at College of Engineering of Virginia Commonwealth University, Richmond, VA, USA.

**References:**

[1] E. M. Wassermann and S. H. Lisanby, “Therapeutic application of repetitive transcranial magnetic stimulation: a review,” Clin. Neurophysiol., vol. 112, no. 8, pp. 1367–1377, Aug. 2001, doi: 10.1016/S1388-2457(01)00585-5. [2] L. Carmi, U. Alyagon, N. Barnea-Ygael, J. Zohar, R. Dar, and A. Zangen, “Clinical and electrophysiological outcomes of deep TMS over the medial prefrontal and anterior cingulate cortices in OCD patients.,” Brain Stimulat., vol. 11, no. 1, pp. 158–165, Sep. 2017, doi: 10.1016/j.brs.2017.09.004. [3] R. B. Lipton et al., “Single-pulse transcranial magnetic stimulation for acute treatment of migraine with aura: a randomised, double-blind, parallel-group, sham-controlled trial.,” Lancet Neurol., vol. 9, no. 4, pp. 373–80, Apr. 2010, doi: 10.1016/S1474-4422(10)70054-5. [4] M. S. George and R. H. Belmaker, Transcranial Magnetic Stimulation in Clinical Psychiatry. American Psychiatric Pub, 2007. [5] A. Delora et al., “A simple rapid process for semi-automated brain extraction from magnetic resonance images of the whole mouse head,” J. Neurosci. Methods, vol. 257, pp. 185–193, Jan. 2016, doi: 10.1016/j.jneumeth.2015.09.031. [6] H. Magsood and R. L. Hadimani, “Development of anatomically accurate brain phantom for experimental validation of stimulation strengths during TMS,” Mater. Sci. Eng. C, p. 111705, Nov. 2020, doi: 10.1016/j.msec.2020.111705. [7] H. Magsood, F. Syeda, K. Holloway, I. C. Carmona, and R. L. Hadimani, “Safety Study of Combination Treatment: Deep Brain Stimulation and Transcranial Magnetic Stimulation,” Front. Hum. Neurosci., vol. 14, p. 123, Apr. 2020, doi: 10.3389/FNHUM.2020.00123.

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/3c260949a0c73b00d1141a7be71b9817.jpg)
Figure 1. Magnetic flux density (B) plot of rat brain surface. Inset: Coil and rat brain orientation (scalp, skull and cerebrospinal fluid layers are hidden)

![](https://assets.underline.io/uploads/markdown_image/1/image/eb56630d580e5595f2d0ddbe23bac3d2.jpg)
Figure 2. Electric current density (J) plot of rat brain surface. Inset: Coil and rat brain orientation (scalp, skull and cerebrospinal fluid layers are hidden)

 Development of individualized brain model and physical phantom of small animals for experimental verification of transcranial magnetic stimulation

In recent years, magnetic nanoparticles based on iron oxides have found increasing interest in practical applications in the field of biotechnology and biomedicine. Surface modified magnetic nanoparticles can be used for selective isolation of certain biomolecules, such as nucleic acids and proteins. The method, commonly known as "magnetic separation", has gained popularity in performing tests for diagnostic purposes. The aim of this work was to develop a nanomagnetic construction based on iron oxide nanoparticles for efficient separation of DNA molecules and subsequent investigation by polymerase chain reaction. The magnetic particles were prepared by coprecipitation from a solution of FeCl3 and FeCl2 salts in a molar ratio of 2:1 at room temperature. With constant stirring, an NH4OH solution (25%) was injected into the solution of iron salts until pH = 10 was reached. At the end of the reaction, the magnetic nanoparticles were collected using a magnet and washed several times in distilled water until pH = 7.0. To use nanoparticles in magnetic separation of DNA, we treated them with a solution containing 1.25 M sodium chloride and 10% PEG 6000 to inhibit free radical oxidation. For biomedical applications of magnetic nanoparticles, an important role is played by the blocking temperature - the temperature separating the hysteresis and hysteresis-free responses of an ensemble of particles. For applications such as bio-separation, blocking temperatures close to ambient (body temperature) are considered optimal. This choice is due to a compromise between the better colloidal stability of an ensemble of superparamagnetic particles (hysteresis-free behavior) and the high magnetic susceptibility of blocked nanoparticles (response with hysteresis). For magnetic characterization of our particles, we performed measurements of magnetization curves at various temperatures (Fig. 1). According to Fig. 1, the magnetic hysteresis disappears at temperatures above 100 K. The distribution of particles by size and by the magnitude of magnetic anisotropy can lead to inhomogeneity of the blocking temperature in the ensemble of particles. To quantify this inhomogeneity (blocking temperature distribution), we calculated the data in Fig. 1 by different methods. The temperature behavior of the coercive force in Fig. 2 does not follow the power-law dependence Hc(T)=Hc(0)*(1-(T/TB)α), (1) usually discussed for single-domain non-interacting nanoparticles at temperatures below the blocking temperature (TB) [1,2]. The power exponent α, in this case, is in the range from 0.67 to 1.00 [3,4]. This deviation may be due to the inhomogeneity of the blocking temperature in the system of the studied nanoparticles. Therefore, to describe the coercive force, we used averaging [5]: Hc(T)=Hc(0)*(∫Hc(T)*f(TB)dTB)/(∫(TB)*dTB) (2) where the parameter Hc(0) is the average coercive force at T = 0 K. Describing the experimental behavior of the coercive force by expression (2), we can determine the parameters of the distribution function f (TB) corresponding to the best description of the experiment. The best agreement is achieved using the lognormal distribution function: f(TB)=1/(TBσ√2π)*exp(-ln2(TB/TB0)/2σ2) with the parameters TB0 = 80 K, σ = 0.77. The study of the nanoparticles ability to isolate nucleic acids was carried out as follows. Leukocyte lysate from a blood sample obtained from a patient with chronic myeloproliferative disease was added to the nanoparticle suspension. Then, the nanoparticles bound to DNA molecules were separated using a magnet. Subsequent washing of DNA from nanoparticles was carried out with 70% ethanol at room temperature, then elution was carried out in 50 μl of TE buffer for 5 minutes at 65 °C. Real-time PCR reaction was performed using the resulting eluate to detect the JAK2 gene. As a comparison, a parallel reaction was carried out with DNA samples isolated by the sorption method using a commercial kit "DNA-Sorb-B" (Amplisens, Russia). The comparative concentration of the isolated DNA was 3.9 ng/μl with standard isolation and 2.4 ng/μl with isolation using magnetic nanoparticles. It follows from the PCR results that the proposed method for isolating DNA from human blood samples is not inferior in efficiency to the standard isolation method and does not affect the efficiency of PCR amplification. This work was supported by Russian Foundation for Basic Research, Government of Krasnoyarsk Territory, Krasnoyarsk Region Science and Technology Support Fund to the research projects No. 20-42-242902 and by the Council of the President of the Russian Federation for State Support of Young Scientists and Leading Scientific Schools (project no. MK-1263.2020.3). We are grateful to the Center of collective use of FRC KSC SB RAS for the provided equipment.

**References:**

[1] R.S. Iskhakov, S.V. Komogortsev, S.V. Stolyar et al. Met. Metallogr., 88, 261–269 (1999) [2] S. V. Komogortsev, R.S. Iskhakov, A.D. Balaev et al. Phys. Solid State. 49, 734–738 (2007) [3] H. Pfeiffer, Phys. Status Solidi. 118, 295–306 (1990) [4] I.S. Poperechny, Y.L. Raikher, V.I. Stepanov, Phys. B Condens. Matter., 435, 58–61 (2014) [5] S. V. Komogortsev, R.S. Iskhakov, A.D. Balaev et al., Phys. Solid State. 51, 2286–2291 (2009)

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/a142de32b117ade09ea1fdcd4dd6355f.jpg)
Fig. 1 Magnetization curves

![](https://assets.underline.io/uploads/markdown_image/1/image/a2a097a3f7750bc29552695db104a0b8.jpg)
Fig. 2. The temperature behavior of the coercive force (red symbols) is not described by equation (1) - dashed lines, but is described by equation (2) - solid line.

 Structure and Magnetic Properties of Maghemite Nanoparticles for DNA Extraction

To separate magnetically coupled particles on lab-on-a-chip devices, microfluidic magnetophoresis plays a pivotal role [1]. It can be useful for biomedical applications like cancer detection, drug delivery, screening, clinical diagnostics [2, 3]. When subjected to a non-uniform magnetic field, small-sized (μm-nm) particles suspended in a fluidic medium will translate toward either the maxima or minima of the gradient of the magnetic field. However, it is very difficult to produce high-gradient magnetic field at micro-scale due to several issues such as non-availability of integratable, high energy product permanent magnets and the detrimental effect of strong demagnetization field of the thin film magnets. Therefore, patterning the magnetic surface is required to produce high flux density with micro-scale resolution over large areas. The efficient design and optimization of such micro-magnetic structures along with their magnetic interaction play an important role in the development of the devices for microfluidic magnetophoresis applications. In our work, comparative FEM analysis is performed to show the advantages of using micro-patterned magnets over bulk rectangular magnet for microfluidic magnetophoresis applications, which is also validated using an analytical framework. The width (x-axis) and height (y-axis) of microfluidic channel were considered 1200 µm and 100 µm respectively with varying gap distance from the permanent magnetic structures (Fig. 1(a)). We have considered bulk rectangular magnetic structure of 1000 µm width and a variation in the height from 100 to 500 µm. Micro patterned rectangular magnets, with 50 µm fixed gap distance between succesive patterns, across the width of microfluidic channel are also analyzed to study the advantage of micro-patterned magnets over bulk rectangular magnet as shown comparatively in Fig. 1(b) and (c). All proposed magnetic structures were concocted using a nano-composite of NdFeB magnetic powder embedded in Polydimethylsiloxane (PDMS) matrix. Geometric optimization of the entire structure including the separation size, height, and width of the separate features are explored using FEM and analytical models to efficiently control the particle trajectories within the microfluidic channel. Effect of different geometries (rectangle, square, triangular etc.) of the micro-patterned magnets are also determined by a factor (H●▽) H, which is proportional to the magnetic force and describe the range of impact of magnets [4]. At the various height (wg=50μm, 80μm, 110μm) from the micro-magnet structure, the magnetic flux densities Hx and Hy were extracted and subsequently used in an customized MATLAB code to determine the force Fx and Fy for describing the motional behavior of magnetic particles in the channel with the help of Newton’s second law. A wide magnet comparable to the microfluidic channel can yield a pseudo magnetic field which can magnetize the micro/nano particles in the channel but does not cause cumulative forces, being exerted on them which can be greatly enhanced by using optimized micro-patterns as shown in Fig. 2. Proof-of-concept prototype of the proposed device is being fabricated using standard micro-fabrication processes. Overall, an effective design methodology for developing highly efficient micro-magnetic flux sources is described which can be useful in many micro-scale applications including biological particle separation and mixing.

**References:**

1. R. Zhou, Q. Yang, F. Bai, J. A. Werner, H. Shi, Y. Ma, C. Wang, Microfluid. Nanofluid., 20, 110 (2016). 2. R. Zhou, A. N. Surendran, M. Mejulu, Y. Lin, Micromachines, 11,129. 25 (2019). 3. F. Alnaimat, S. Karam, B. Mathew, B. Mathew, IEEE Nanotech. Mag., 14(3), 24-41 (2020). 3. E. P. Furlani, J. Appl. Phys., 99, 024912 (2006).

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/c7e9be793ad6286fdc706ad5898f152d.jpg)
Fig. 1: (a) Proposed device architecture. FEM simulation results of the y component of magnetic flux density in the microfluidic channel due to rectangular magnet of size (b) 1000×100 µm2 (bulk magnet) and (c) 100×100 µm2 (micro-patterned magnets) with 50 µm pattern gap. A thin film (b) produces magnetic field only at the edges whereas the magnetic flux density vis-à-vis the magnetic flux gradient can be significantly improved through micro-patterning (c) of the magnetic surface.

![](https://assets.underline.io/uploads/markdown_image/1/image/32ee19bb927965e9321dee559a17f72e.jpg)
Fig. 2: The Y component of (a) magnetic field intensity (Hy) and (b) Force (Fy) exerted on the particles inside the microfluidic channel at different height (ht.) due to single bulk and patterned micro-magnets.

 Design and Analysis of High-gradient Magnetic Field Source at Micro-scale for Microfluidic Magnetophoresis Applications

Magnetic nanostructures attract considerable scientific and technological efforts in diverse applications, such as magnetic recording, magnetic sensors, biomedicine, etc.[1,2] Whereas patterned nanomagnets are mostly 2D planar structures, recently research has been expanded into 3D aspect. In 3D nanomagnets, more delicate and complicated magnetic configurations, with novel properties, become possible. [3,4] Imaging and understanding the magnetic configurations in 3D nanomagnets is an increasingly important issue for a wide range of modern applications. Here, aligned, isolated iron nanocuboids [Fig. 1 (a)] have been fabricated by taking advantage of epitaxial, three-dimensional-island growth on GaAs(001) during electrodeposition at low deposition rates.[5] The nanoparticles exhibit lateral size between 10 and 250 nm and heights below 80 nm. Surface {100} facets predominate with a thin crystalline oxide shell that protects the nanoparticles during prolonged storage in air [Fig. 1 (b)]. The magnetic configurations inside the cuboids are systematically investigated by combining quantitative magnetic force microscopy (qMFM) with micromagnetic simulations [Fig. 1 (c, d)]. Experimental results and micromagnetic simulations give evidence for a transition from single-domain state to vortex state, and even to Landau pattern with increasing the size of the cuboids, demonstrating the key importance of nanometric size control of magnetic nanoparticles. The simulated and experimental magnetic charge profiles are compared and show good agreement [Fig. 1 (e-h)]. Such measurements open the door to fine tuning the magnetic configuration of nano-objects that will find applications in fields of sensor, magnetic recording, and biomedicine.

**References:**

1. C. Gatel, F. J. Bonilla, A. Meffre, et al. Nano Lett. 2015, 15, 6952−6957. 2. M. Bode, A. Wachowiak, J. Wiebe, et al. Appl. Phys. Lett. 2004, 84, 948−950. 3. L. A. Fomin, I. V. Malikov, S. V. Pyatkin, et al. J. Magn. Magn. Mater. 2010, 322, 851−857. 4. F. J. Bonilla, L.-M. Lacroix, T. Blon, J. Magn. Magn. Mater. 2017, 428, 394−400. 5. K. Leistner, M. Yang, C. Damm, et al. Nanoscale, 2017, 9, 5315–5322.

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/5a71d36f584e8493e8281fc8b8ff7eca.jpg)
Fig.1 (a) SEM image showing isolated iron cuboids with different size distribution. (b) EELS mapping of Ga, Fe and O elements in iron cuboid. (c) qMFM scan of one cuboid with a lateral size of 54 nm, and the related micromagnetic simulation showing vortex state (d). Experimental MFM phase of one cuboid with a lateral size of 170 nm (e) and the calculated MFM phase (f). (g) Extracted profiles from (e) and (f), (h) Simulation of (e) showing Landau pattern.

 Size-specific magnetic configurations in epitaxial iron nano-cuboids

We aim to prepare a multifunctional application-ready material, which could be used as a sensing and simultaneous actuating device driven by shape memory processes. One of the most promising ways to expand the application possibilities of a well-known material is the down-sizing. Therefore, we have prepared Ni2FeGa Heusler-based nanowires and studied their magnetic properties. The Ni2FeGa Heusler alloy has a L21 structure and undergoes a martensitic transformation [1]. The martensitic transformation temperature of the Ni2FeGa Heusler alloy can be tuned by changing its chemical composition [2]. It also shows a shape memory and a multi-caloric behaviour. The nanowires that we have studied were prepared by a galvanostatic electrochemical deposition, using the anodized aluminium oxide (AAO) membrane with the nanopores diameter of 60 nm. The deposition time was adjusted to obtain nanowires of an appropriate length, which was 7.5 μm. The chemical composition of the prepared nanowires is Ni55Fe43Ga2. The deviation from the X2YZ Heusler chemical composition is probably due to the difficult determination of the effective deposition area of the AAO membrane. During the isothermal magnetization measurement (Fig. 1), a magnetic shape memory temperature region was defined. Between the temperatures of 290 and 360 K, an unusual magnetization increase was observed within each magnetization isotherm. The magnetization increase within the isothermal measurement or within the measurement of the hysteresis loops was ascribed to the magnetic shape memory behaviour within previous research of shape memory materials, such as the Ni2MnGa or Ni2MnSn [3, 4]. The observed magnetization increase occurs at different values of the applied transformation magnetic field. A deeper analysis shows that the transformation fields are temperature dependent. The temperature dependence of the transformation magnetic field can be described according to the Clausius-Clapeyron equation and a fitting model of the experimental data shows that the transformation temperature is ≈285 K and is also dependent on the system pressure. The shape memory behaviour of the prepared nanowires made them interesting for further analysis. Therefore, we have performed the First-Order Reversal Curve (FORC) analysis of the magnetic shape memory nanowires. The measurements of the individual FORCs were performed at four different temperatures, following the cooling behaviour of the isothermal magnetization measurement. The FORC measurements were performed at 395, 300, 200 and 100 K (Fig. 2). Each measurement shows a diverging FORC distribution, which was defined by Pike, et al. [5]. The contours within such diagram diverge from the Hu axis and intersect the Hc = 0 axis. The FORC distribution with the diverging shape shows that the nanowires array is a multi-domain and highly interacting system, as stated by Muxworthy, et al. [6]. In the hysteresis loops measurements, we show that the main contribution to the nanowires array magnetization process consists of the magnetostatic interactions of the neighbouring nanowires. The vertical spread of the FORC distribution is a function of the internal demagnetization field (magnetostatic interactions within the neighbouring nanowires), but it depends on several domain properties (domain cancelation, domain shape and domain wall interactions) [7]. However, the vertical spread of the diverging FORC distribution should increase with the system volume, which points to the shape changes that occur within the Ni55Fe43Ga2 nanowires. This was shown in the case of multi-domain magnetic nanoparticles with a strong domain wall pinning. During the investigation of a structure transformation of CoNi alloy nanowires, the structural change from hcp to fcc was accompanied by a change of the FORC distribution shape, where it became more symmetric [8]. Therefore, to describe the changes within the FORC investigation of the Ni55Fe43Ga2 nanowires, a detailed analysis of the obtained results is necessary. We have shown that the Ni55Fe43Ga2 nanowires show a magnetic shape memory behaviour. The magnetization increase within the isothermal measurement is temperature- and magnetic field dependent. The diverging FORC distribution shows that the nanowires array behaves as a multi-domain and highly interacting system and the vertical spread of the divergence narrows with respect to the Hc axis of the FORC density contour plot. To determine the origin of the FORC distribution change at different temperatures, further analysis of the FORC measurements is necessary. However, the current results show that the Ni55Fe43Ga2 nanowires show an elongation within the low-temperature measurements, below the transformation temperature region that was determined during the isothermal magnetization measurements. Acknowledgement: This work was supported by Slovak Grant Agency VEGA 1/0053/19, Slovak Grant Agency grant number APVV-16-0079, VVGS-2019-1231 and VVGS-PF-2020-1420.

**References:**

[1] Y. Li, D. Zhao, and J. Liu, Sci. Rep., vol. 6, pp. 1–11 (2016) [2] M. Hennel, L. Galdun, T. Ryba, J. Magn. Magn. Mater., vol. 511, p. 166973 (2020) [3] P. Cejpek et al., J. Alloys Compd., vol. 775, pp. 533–541 (2019) [4] B. Hernando et al., Appl. Phys. Lett., vol. 92, pp. 12–14 (2008) [5] C. R. Pike, et al., Phys. Earth Planet. Inter., vol. 126, pp. 11–25 (2001) [6] A. R. Muxworthy, A. P. Roberts, Encycl. Geomagn. Paleomagn., pp. 266–272 (2007) [7] A. P. Roberts, D. Heslop, X. Zhao, Rev. Geophys., vol. 52, pp. 557–602 (2014) [8] A. S. Samardak et al., J. Alloys Compd., vol. 732, pp. 683–693 (2018)

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/13d044c3864a26387342bf9f3f7b6fe9.jpg)
Fig. 1: Isothermal magnetization measurements at different temperatures

![](https://assets.underline.io/uploads/markdown_image/1/image/cf8ea57120a09f5c7343b6d90adee253.png)
Fig. 2: FORC density distribution of the Ni55Fe43Ga2 nanowires at different temperatures

 Temperature-dependent FORC Investigation of Electrodeposited Magnetic Shape Memory Nanowires Array

The study of 1D-nanostructures has been intensified in the last few decades due to the development of fabrication methods of metallic, semiconductors and insulator materials aiming applications in several areas [1]. In particular, multi-segmented magnetic nanowire (NW) arrays are prospective candidates for an extensive range of applications such as racetrack memory devices, spintronic, and drug delivery [1, 2, 3]. These possibilities are due to the number of degrees of freedom related to the intrinsic shape anisotropy combined with the potential to introduce different materials along the NW’s length. Concerning practical applications, understanding the role of layers with distinct structural and magnetic properties can be a path to avoid some issues such as system overheating and Walker breakdown in racetrack devices. For instance, micromagnetic simulations revealed that the combination of Co segments with different structures, bcc and hcp, promotes a faster way of writing information in 3D racetrack memory devices [2]. This observation results from the high magnetocrystalline anisotropy along the wire length induced by the Co-hcp structure. Although these evaluations seem promising, thorough experimental research of multi-segmented NWs with low and high anisotropy components still needs to be performed. Here, we present the FeCo layer properties’ evaluation onto multi-segmented NW arrays produced through DC electrodeposition into ordered porous alumina templates with 40 nm of pore diameter and 60 µm of length. For each layer’s deposition, a Pt electrode was used as the counter electrode, Ag/AgCl as the reference electrode, and an Au layer as the working electrode [5]. Two samples were prepared: 1) Au [200 nm] / Fe33Co67 [24 µm] / Au [10 nm] and 2) Au [200 nm] / Ni90Cu10 [1 µm] / (Fe33Co67 [13 µm] / Au [10 nm])x3, where the indicated length was obtained from scanning electron microscopy (SEM) images and the alloy’s stoichiometry from energy dispersive spectroscopy (EDS). X-ray diffraction (XRD) measurements at room temperature revealed the formation of bcc structure of FeCo with the (110) preferential orientation for both samples and an additional hcp phase with the (110) preferential orientation for FeCo tri-segmented NWs (Figure 1). The magnetic hysteresis loops acquired at room temperature for the Au/FeCo/Au arrays present the easy magnetization axis along the parallel direction, evidencing a typical strong shape anisotropy [5]. Distinctly, when three FeCo segments of 13 µm are deposited along the NW’s length, the arrays present an isotropic magnetic behavior with an increase of the coercive field when applying the magnetic field perpendicular to the nanowires’ axis (Figure 2). This change in magnetic behavior for the segmented NWs might be related to the presence of an hcp phase that induces a perpendicular magnetocrystalline anisotropy. However, further research should be performed to better comprehend the interplay between the NiCu and FeCo layers into the NW arrays. In summary, multi-segmented NWs of FeCo alloys were successfully achieved through the electrodeposition process into porous templates. The growth of FeCo segments leads to the formation of hcp structures and the observation of an isotropic magnetic behavior. This can be related not only to the structural properties but also to the interplay between FeCo segments along the NW’s length. A more complete evaluation of the magnetic properties of the produced samples should be performed to fully understand the role of the different layers in the magnetocrystalline anisotropy of the arrays. This work was financially supported by projects POCI-01-0145-FEDER-028676 and UIDB/04968/2020 from Portuguese FCT and COMPETE 2020 (FEDER) and IF/01159/2015, POCI-01-0145-FEDER-031302/PTDC/FIS-MAC/31302/2017. .

**References:**

References:: [1] C. T. Sousa et al., Appl. Phys. Rev., vol.1 , p. 031102 (2014); [2] J. Rial and M. P. Proenca, Nanomaterials, vol. 10, p. 2403 (2020); [3] D. Wang et al., Materials, vol. 12, p. 3908 (2019); [4] C. Bran et al., J. Phys. D: Appl. Phys., vol. 48, p. 145304 (2015); [5] E. M. Palmero et al., Nano Research, vol. 12, p. 1547 (2019).

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/419fc130f5d8af612615b50ad0e953e0.jpg)
Figure 1: XRD patterns for Au/FeCo/Au and Au/NiCu/[FeCo/Au]3 segmented nanowires with the Bragg peak positions for bcc (green) and hcp (red) structures.

![](https://assets.underline.io/uploads/markdown_image/1/image/59bc97224bca21ea1066106778e1c21d.jpg)
Figure 2: Hysteresis loops obtained by applying the magnetic field perpendicular to the NWs’ length

 Isotropic magnetic behavior of multi-segmented FeCo nanowire arrays

Striving for create ultrafast electronics led to the development of three-dimensional compact architectures in many disciplines including magnetism. Coercivity, squareness, and magnetic anisotropy can be tailored by varying the geometry and/or spatial distribution of the magnetic functional units [1, 2]. Elongated elements (nanowires and nanotubes) have been used in the number of technologies. The problems concerned with the complicated dipole-dipole interactions in arrays of such elements motivates in researching new designs for these elements. Two-phase nanowires with a coaxially combined or varied along axis phases could generate additional applied advances. In this work, we describe experimental results concerning the bi-segmented and coaxial Co/Ni rods in porous of track etched polycarbonate membranes (PCTE) and focus on the comparison of their magnetic properties. The 3D coaxial nanostructures investigated consist of a cylindrical cobalt core that is completely surrounded by a shell of nickel layer. The bi-segmented (BS) rods contain two coupled rods of nickel and cobalt. The magnetic anisotropy of the bi-segmented and core-shell rods electroless deposited to the pores of PCTE was studied. The Co and Ni deposition into the PCTE membranes pores is carried out by electroless reduction of metal-salt solution with sodium hypophosphite as reducing agent. In a first step in the case of coaxial rods, the inner pore walls were treated with paladium chloride used as a nucleating agent. In the next step the pores are coated with nickel by electroless deposition. The deposited Ni tubes are shown in Fig.1a. Then the Ni tubes were filled with cobalt by electroless deposition. The coaxial rods are shown in Fig. 1b. The cobalt core has a diameter of about 200 nm, which is determined by the PCTE pore diameter and the thickness of the Ni shell layers. The reference tube and rod samples consisting of ‘‘shell only’’ or ‘‘core only’’ was prepared using the same technique. For the synthesis of bi-segmented rods one side of the membrane was coated by a thin layer of thermal-sputtered cooper to create an electrochemical potential that promotes the metal deposition inside PCTE channels along the pore axis. Then Co/Ni rods (along-axis) were prepared by electroless deposition. The employed rods growth method allows for tuning both the composition and crystalline structure of each individual Co and Ni segments. The magnetic properties and structure of the rods are characterized by scanning electron microscopy, X-ray diffraction, ferromagnetic resonance (FMR) and vibrating sample magnetometer. Information on local magnetic anisotropy is obtained using the approach to magnetic saturation curves. The X-ray powder diffraction shows that the Ni and Co alloys for the rods of the both types were crystalline with fcc structure. The local magnetic anisotropy field of Co/Ni rods was estimated to be in the range from 0.9 to 2 kOe. The core/shell geometry of Co@Ni rods transpires in their physical properties. A staggering difference is observed between the FMR spectra measured on arrays of Co/Ni core/shell rods, Co/Ni BS rods and the ‘‘parent’’ samples, namely, Ni tubes without core and Co rods without Ni shell (fig.2). The FMR spectrum for Co core and Ni tube consists of a single absorption line. For Co/Ni and Co@Ni rods the FMR spectrum consists of two wide absorption lines corresponding to different layers. The presence of graded Co or Ni content at layer boundaries could give rise to graded anisotropy effects (that is, local variations of the effective magnetic anisotropy along the rod axis). Such variations in magnetic anisotropy could manifest in variations of resonance fields for different rod segments and could increase FMR linewidth. The measurements of FMR spectrum and magnetization curves at different orientations of an external field allow us to obtained data about macroscopic magnetic anisotropy of synthesized rods. It was found that for Co rods easy magnetization axis lying along the long axis of the rod, and its value is close to magnetic shape anisotropy of elongated column pMs. The overall magnetic anisotropy of the array is mainly determined by the following three contributions: the anisotropy results from the shape effect of the individual rods , which will induce a magnetic easy axis parallel to the wire axis; magnetostatic coupling among the rods, which tends to develop a magnetic easy axis perpendicular to the rod axis; and the local anisotropy field, which consists of magnetocrystalline anisotropy and anisotropy of intrinsic strain. In the case of BS rods for distribution density of rods more than 20% the contribution from dipole-dipole interaction was comparable to those for shape anisotropy. The room temperature magnetic behavior of the core-shell Co/Ni nanorod arrays is also studied and correlated with their structural and morphological properties. The successful synthesis of the bi-segmented rods with coaxial (Co@Ni) and along-axis (Co/Ni) segmentation was demonstrated. The magnetic anisotropy field, ferromagnetic resonance field, linewidth and the coercivity are mainly determined by the artificially created interface boundaries for two types of bi-segmented rods with coaxial (Co@Ni) and along-axis (Co/Ni) segmentation. This work was funded by the RFBR, the Government of the Krasnoyarsk Territory, the KRFS (project no. 20-43-240003)

**References:**

1. R. Streubel, J. Lee, D. Makarov et al, J. Phys. D, 49, 363001, (2016) 2. E. Y. Vedmedenko, R. K. Kawakami, D. D. Sheka et al., J. Phys. D. Appl. Phys. 53, 453001 (2020)

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/522d7e8b1522ae40fd8dc8d80470c462.jpg)
Fig.1 SEM image of Ni tube (a) and Co@Ni core/shell rods (b).

![](https://assets.underline.io/uploads/markdown_image/1/image/646e08d194d1a030767c7cfdcace80d9.jpg)
Fig.2 a - FMR spectra for Co/Ni core-shell rods (1) and BS rods (2); b- Co rods (1), Ni tubes (2).

 Core-shell and Bi-segmented Cobalt-Nickel Nanorods Prepared by Electroless Deposition

Properties of two-dimensional spatially periodic nanostructures formed by a corrugated 2D structured as substrate which covered by gold and Ce:YIG films were studied by magneto-optical spectroscopy techniques. It was shown that the structures exhibit a considerable magneto optical response to longitudinal Kerr effect at wavelength of 450 nm and this enhancement seems to be related to excitation of localized surface plasmon-polaritons(LSPR) in the array of nanorods created in this structure. Recent achievements in photonics and optoelectronic require the advanced magneto-photonic microdevice with ability of control the magneto-optical response in micron and submicron scales. The Advanced magneto-optical devices tend to miniature the components, which requires strong magneto-optical effect in small scale. Combination of magnetic and plasmonic materials with different functionalities into a magneto-plasmonic structure is considered as a promising route to enhance the magneto-optical activity [1]. On the one hand, plasmonics allows for extreme electromagnetic field enhancement and subwavelength localization. On the other hand, MO materials bring optical non-reciprocity properties in the presence of magnetic field. Early studies on magneto-plasmonic structures addressed propagating surface plasmon-polariton (SPP) along the smooth surface of a metallic film [2]. In parallel to the studies on SPPs, the rapid developments in nanofabrication, enable extending studies of optics in nanoscale with nanostructures also supporting localized surface plasmon (LSPR) [3,4]. In the recent work, we investigate the magneto-optical response of a 2D magnetoplasmonic nanostructure which can support LSPR. A two-dimensional 2D magneto-plasmonic nanostructure was prepared by nanoimprint lithography method. For this purpose, a 2D charge coupled device (CCD) separated from a camera was used as stamp and the poly-dimethylsiloxane (PDMS) substrate was patterned as 2D substrate. First, the substrate was covered by gold layer of 30 nm thickness as plasmonic material by using a PVD coating device. Then it was coated by a Ce:YIG layer with an approximate thickness about 100 nm as magnetic material by using of pulsed laser deposition method. Actually this structure composed of 2D array of cubic holes with width and length of 3 µm and depth of 500 nm. these cubic holes were arranged in 2D with a distance about 170 nm. The Schematic of this structure is shown in Fig. 1a. Also, the periodicity of the sample and its surface has been examined by scanning electron microscopy (SEM) and shown in Fig. 1b. The nanometric distance between holes well creates nanorods which can support LSPR in the structure and this surface lattice resonance. Investigation of MO activity of the prepaid sample was carried out by a home-made longitudinal spectral Kerr effect set up with applying a DC magnetic field in the plan of sample and parallel to the incidence plane. The linear polarized light was incident on the sample at incidence angle of 30°. In our set up, the linear poliarized light was achieved by passing the unpolarized broadband light from a polaroid sheet which can linearly polarized the light in the wavelength range of 400-700 nm. Thereafter, the reflected spectra of the sample were recorded for positive and negative directions of magnetic field in rotational analyzer method. Finally, the recorded spectra were analyzed by a Labview program. The longitudinal Kerr effect spectrum showed a sharp peak at the wavelength of 450 nm which is related to Ce:YIG magneto-optical response.

**References:**

[1] Maccaferri, N., Zubritskaya, I., Razdolski, I., Chioar, I. A., Belotelov, V., Kapaklis, V., & Dmitriev, A. 2020. J. Appl. Phys,127, 8, 080903. [2] D. Martin-Becerra, J.B. Gonzalez-Díaz, V.V. Temnov, A. Cebollada, G. Armelles, T. Thomay, A. Garcia-Martín and M. Ujue Gonzalez, 2010, Appl. Phys. Lett. 97, 183114. [3] V. I. Belotelov, I. A. Akimov, M. Pohl, V. A. Kotov, S. Kasture, A. S. Vengurlekar, Achanta Venu Gopal, D. R. Yakovlev, A. K. Zvezdin, M. Bayer (2011), Nature Nanotechnol, 6, 370. [4] B. Sepúlveda, J. B. Gonzalez-Díaz, A. Garcia-Martín, L. M. Lechuga, and G. Armelles, 2010, Phys. Rev. Lett. 104, 147401.

**Images:**

![](https://assets.underline.io/uploads/markdown_image/1/image/a2bf0ac2c504a3ad8ec1b3e56b5fa519.jpg)
Fig1. (a) schematic of 2D magneto-plasmonic structure composed of PDMS corrugated substrate covered by gold layer with thickness of 30 nm and Ce:YIG layer with approximate thickness of 100 nm. (b) SEM image of prepaid magneto-plasmonic structure.

![](https://assets.underline.io/uploads/markdown_image/1/image/63662f9edd1974d5d788347bf635aa74.jpg)
Fig.2: MO spectrum of the 2D grating sample composed of Gold and Ce:YIG layer measured at incident angle of 30° by home-made spectral longitudinal Kerr set up.

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