France



Alloy systems of the past tend towards single principal component alloy systems. In present research, the stoichiometry of alloy systems with large number of alloying components (&amp;gt;4) can be adjusted to stabilise near-ideal solid solution phases (termed High-entropy alloys, HEAs due to their high configurational entropy), or to possess some mixture of ordered intermetallic phases and the near-ideal solid solution phase (termed Complex Concentrated Alloys, CCAs). HEA and CCA possess many design degree-of-freedoms. Precise control over stoichiometry and thermomechanical history lead to exciting magnetic properties; &lt;i&gt;e.g.&lt;/i&gt; through the formation of nanocomposite microstructures [1] in CCAs can achieve good magnetic softness by allowing exchange averaging of the magnetic anisotropy. A major challenge to general application is the vast compositional design space; if ignoring stoichiometry: restricting the number of elements to 1) 3d transition metals, and 2) Si and B, there are 10C5 = 792 [RRR1] possible equimolar combinations. Millions more are possible if stoichiometry is relaxed. Appropriate strategies to filter out good candidate compositional families for study are thus essential.&lt;br/&gt;&lt;br/&gt;Alloy design can be generalised to two approaches: data-driven discovery (DDD) and functionality-driven discovery (FDD). For DDD experimental data obtained from exploratory and characterisation frameworks are extrapolated for design and prediction; in FDD search and optimisation methods are used to achieve targeted properties. Prediction models (&lt;i&gt;e.g. ab-initio&lt;/i&gt;) are used in conjunction with FDD to determine microscopic parameters that govern material properties. FDD is useful in exploring materials with large numbers of degree-of-freedoms such as HEA/CCA systems as extrapolation from experimental data is not a good predictor of quantum mechanical behaviour (&lt;i&gt;i.e. &lt;/i&gt;electronic structure interactions). &lt;i&gt;Ab-initio &lt;/i&gt;models can calculate potential properties of new compositions, iterating over shedloads[RRR2] of stoichiometries using search and optimisation methods. Although computationally efficient, significant computational power is still required. Applying reasonably accurate low-fidelity pre-filters derived from quantum principles reduces the computational resources required. This work uses two such low-fidelity pre-filters using a parametric semi-empirical approach for determining the saturation magnetisation and mean Curie temperature of HEA/CCA systems.&lt;br/&gt;&lt;br/&gt;The Curie temperature can be expressed as a function alloyed system (&lt;i&gt;i.e.&lt;/i&gt; the number of impurity atoms). At the electronic level these changes are due to 1) Variations of the local moments, and/or 2) Changes in interaction strength between moments represented by the molecular field coefficient (dependent on interatomic distances and local environment effects) [2]. Since the uniaxial pressure experienced by the valence electrons upon interatomic distance changes leads to electronic density compression [3], the rectangular band model [4] can be used to explore the onset of ferromagnetism by evaluating the bulk modulus, B with respect to the Stoner criterion. From this, the ratio B/E&lt;sub&gt;F&lt;/sub&gt; (where the Fermi energy E&lt;sub&gt;F&lt;/sub&gt; is approximated by the Mulliken electronegativity, X&lt;sub&gt;M&lt;/sub&gt;) is used to predict the Curie temperature in HEAs and CCAs (&lt;i&gt;cf. &lt;/i&gt;Fig. 1). The predictions are validated through synthesised as-cast HEA/CCA compositions that are characterised on a SQUID-VSM and are found to be dependent on the amount of antiferromagnetic Cr alloying in the system.&lt;br/&gt;&lt;br/&gt;The Bethe-Slater curve forms part of the early understanding of magnetism and the electronic-structure-driven magnetic ordering of 3d transition metals. Slater Rules [5] are used to evaluate the 4s:3d orbital radius ratio to reconstruct the Bethe-Slater curve (&lt;i&gt;cf.&lt;/i&gt; Fig. 2a) using synthesised HEA/CCA compositions from literature, predictions, and our own experiments. Deviations in the 3d Bethe-Slater curve due to electronic interactions lead to curve shifts and model multiplicities, making predictions non-trivial. Orbital radius changes and valence symmetry-breaking are thus evaluated in a parametric function derived from rule-of-mixtures X&lt;sub&gt;M &lt;/sub&gt;and valence electron values as a supplement to the modified Beth-Slater curve. Plotted using the same dataset, this function in Fig. 2b shows good parameterisation of M&lt;sub&gt;S &lt;/sub&gt;with no model multiplicities making it suitable for design predictions.&lt;br/&gt;&lt;br/&gt;Both models show reasonable accuracies when compared to the experimental data and data from literature. One benefit of both models is that they are derived from common parameters (Bulk modulus, Mulliken electronegativity, atomic number, and d-electron count). This means that the predictive calculations can be obtained by using the rule-of-averages to determine the weighted mean of these parameters for various alloy systems. In order to further test the validity of these models, the models are used with an evolutionary algorithm to design a HEA/CCA with targeted Curie temperature and saturation magnetisation. The results of this prediction are synthesised and characterised through x-ray diffraction and SQUID-VSM and will be presented here.

**References:**

[1] N.A. Morley, B. Lim, J. Xi, A. Quintana-Nedelcos, Z. Leong, Sci. Rep., Vol. 10, 14506 (2020).&lt;br/&gt;[2] J.P. Gavigan, D. Givord, H.S. Li, , in: Concert. Eur. Action Magn. CEAM, p.163–173 (1989).&lt;br/&gt;[3] S.A. Serebrinsky, J.L. Gervasoni, J.P. Abriata, V.H. Ponce, J. Mater. Sci., Vol. 33, 167–171 (1998)&lt;br/&gt;[4] D.G. Pettifor, Bonding and structure of molecules and solids (1995).&lt;br/&gt;[5] J.C. Slater, Phys. Rev., Vol 36, p.57–64 (1930).

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/32b4c926a5a2171a4d869a6d4bfa2874.jpg)
Fig. 1. Plot of a dimensionless number, B/X&lt;sub&gt;M&lt;/sub&gt; against the Curie temperature for experimental values as well as values taken from literature. The lines represent a guide to the eye for the various amounts of Cr addition to the composition.

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/94cdfef7de161c197ef79ff1235b2407.jpg)
Fig. 2. Saturation magnetisation plotted against the 4s:3d ratio calculated using Slater Rules. *New results presented here **Experimental results from literature, ***Simulated results from literature.

INTERMAG 2021

 Parametric Semi-Empirical Design of Magnetic Properties in Complex Concentrated Alloys: Curie Temperature and Saturation Magnetisation

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Alloy systems of the past tend towards single principal component alloy systems. In present research, the stoichiometry of alloy systems with large number of alloying components (&gt;4) can be adjusted to stabilise near-ideal solid solution phases (termed High-entropy alloys, HEAs due to their high configurational entropy), or to possess some mixture of ordered intermetallic phases and the near-ideal solid solution phase (termed Complex Concentrated Alloys, CCAs). HEA and CCA possess many design degree-of-freedoms. Precise control over stoichiometry and thermomechanical history lead to exciting magnetic properties; e.g. through the formation of nanocomposite microstructures [1] in CCAs can achieve good magnetic softness by allowing exchange averaging of the magnetic anisotropy. A major challenge to general application is the vast compositional design space; if ignoring stoichiometry: restricting the number of elements to 1) 3d transition metals, and 2) Si and B, there are 10C5 = 792 [RRR1] possible equimolar combinations. Millions more are possible if stoichiometry is relaxed. Appropriate strategies to filter out good candidate compositional families for study are thus essential. Alloy design can be generalised to two approaches: data-driven discovery (DDD) and functionality-driven discovery (FDD). For DDD experimental data obtained from exploratory and characterisation frameworks are extrapolated for design and prediction; in FDD search and optimisation methods are used to achieve targeted properties. Prediction models (e.g. ab-initio) are used in conjunction with FDD to determine microscopic parameters that govern material properties. FDD is useful in exploring materials with large numbers of degree-of-freedoms such as HEA/CCA systems as extrapolation from experimental data is not a good predictor of quantum mechanical behaviour (i.e. electronic structure interactions). Ab-initio models can calculate potential properties of new compositions, iterating over shedloads[RRR2] of stoichiometries using search and optimisation methods. Although computationally efficient, significant computational power is still required. Applying reasonably accurate low-fidelity pre-filters derived from quantum principles reduces the computational resources required. This work uses two such low-fidelity pre-filters using a parametric semi-empirical approach for determining the saturation magnetisation and mean Curie temperature of HEA/CCA systems. The Curie temperature can be expressed as a function alloyed system (i.e. the number of impurity atoms). At the electronic level these changes are due to 1) Variations of the local moments, and/or 2) Changes in interaction strength between moments represented by the molecular field coefficient (dependent on interatomic distances and local environment effects) [2]. Since the uniaxial pressure experienced by the valence electrons upon interatomic distance changes leads to electronic density compression [3], the rectangular band model [4] can be used to explore the onset of ferromagnetism by evaluating the bulk modulus, B with respect to the Stoner criterion. From this, the ratio B/EF (where the Fermi energy EF is approximated by the Mulliken electronegativity, XM) is used to predict the Curie temperature in HEAs and CCAs (cf. Fig. 1). The predictions are validated through synthesised as-cast HEA/CCA compositions that are characterised on a SQUID-VSM and are found to be dependent on the amount of antiferromagnetic Cr alloying in the system. The Bethe-Slater curve forms part of the early understanding of magnetism and the electronic-structure-driven magnetic ordering of 3d transition metals. Slater Rules [5] are used to evaluate the 4s:3d orbital radius ratio to reconstruct the Bethe-Slater curve (cf. Fig. 2a) using synthesised HEA/CCA compositions from literature, predictions, and our own experiments. Deviations in the 3d Bethe-Slater curve due to electronic interactions lead to curve shifts and model multiplicities, making predictions non-trivial. Orbital radius changes and valence symmetry-breaking are thus evaluated in a parametric function derived from rule-of-mixtures XM and valence electron values as a supplement to the modified Beth-Slater curve. Plotted using the same dataset, this function in Fig. 2b shows good parameterisation of MS with no model multiplicities making it suitable for design predictions. Both models show reasonable accuracies when compared to the experimental data and data from literature. One benefit of both models is that they are derived from common parameters (Bulk modulus, Mulliken electronegativity, atomic number, and d-electron count). This means that the predictive calculations can be obtained by using the rule-of-averages to determine the weighted mean of these parameters for various alloy systems. In order to further test the validity of these models, the models are used with an evolutionary algorithm to design a HEA/CCA with targeted Curie temperature and saturation magnetisation. The results of this prediction are synthesised and characterised through x-ray diffraction and SQUID-VSM and will be presented here.

**References:**

[1] N.A. Morley, B. Lim, J. Xi, A. Quintana-Nedelcos, Z. Leong, Sci. Rep., Vol. 10, 14506 (2020). [2] J.P. Gavigan, D. Givord, H.S. Li, , in: Concert. Eur. Action Magn. CEAM, p.163–173 (1989). [3] S.A. Serebrinsky, J.L. Gervasoni, J.P. Abriata, V.H. Ponce, J. Mater. Sci., Vol. 33, 167–171 (1998) [4] D.G. Pettifor, Bonding and structure of molecules and solids (1995). [5] J.C. Slater, Phys. Rev., Vol 36, p.57–64 (1930).

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/32b4c926a5a2171a4d869a6d4bfa2874.jpg)
Fig. 1. Plot of a dimensionless number, B/XM against the Curie temperature for experimental values as well as values taken from literature. The lines represent a guide to the eye for the various amounts of Cr addition to the composition.

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/94cdfef7de161c197ef79ff1235b2407.jpg)
Fig. 2. Saturation magnetisation plotted against the 4s:3d ratio calculated using Slater Rules. *New results presented here **Experimental results from literature, ***Simulated results from literature.

technical paper

Crystallization from an amorphous precursor has been historically exploited to synthesize metastable soft magnetic nanocomposite systems comprised of transition metal rich ferromagnetic nanocrystals embedded within an intergranular amorphous phase [1,2]. Subsequent thermal processing steps are designed to produce a highly refined microstructure with grain sizes in the nm-range to enable effective exchange averaging and highly reversible magnetization processes as described by the random anisotropy model [3,4]. Successful realization of superior soft magnetic properties results from ubiquitous nucleation and self-limiting growth of nanocrystals due to expulsion of glass formers to the intergranular amorphous matrix, thereby requiring significant amounts of metalloids and early transition metals which reduce the effective saturation magnetization. Recent work has discovered the balance between nucleation and growth can alternatively be optimized through highly controlled thermal processing steps involving extremely rapid heating and subsequent cooling rates on the order of 102-103K/s referred to as “flash annealing”, such that a high density of nucleation sites can be achieved with limited nanocrystal growth even for alloy chemistries which do not produce nm-scale microstructures for conventional annealing [5]. High heating and cooling rates generated during laser radiation have offered great advantages for rapid thermal processing and surface treatment of ferromagnetic amorphous ribbons [6–8]. In this work, we report on pulsed-laser processing of a series of Fe-based and Co-based amorphous ribbons with emphasis being placed on phase transformations within the laser-irradiated regions as well as impacts on surrounding regions due to the detailed thermal effects associated with the laser pulse. Amorphous ribbons with nominal compositions Fe73.5Si13.5Nb3B9Cu1 and Co77.2Fe1.4Mn1.4Nb4B14Si2 were used for laser experiments. Laser annealing has been carried out using a Q-smart pulsed Nd-YAG (wavelength of 1064 nm) and laser beam diameter around 0.6 mm. The laser power was varied from 50-150 mJ and the time delay associated with each laser power has been calculated using the FWHM of the laser output pulse. Microstructure and crystalline phases after laser annealing were characterized using both XRD and SEM. Temperature profiles achieved during laser annealing have been estimated using FEA heat transient analysis. Fig. 1 shows XRD patterns of as-cast and laser annealed Fe- and Co-based ribbons at different laser power. As can be seen, as-cast and samples annealed at 60 mJ are fully amorphous, whereas samples treated at higher laser power (i.e., at 100mJ and above) present a mixture of boride and α-Fe phases with an average grain size of the latter being on the order of 8-10 nm estimated from the FWHM of the corresponding crystalline peak. In conventional annealing methods, the formation of boride phases are typically observed only after reaching secondary crystallization temperatures in these alloy systems. Because the borides are already observed in laser annealed samples with significant volume fraction for the lowest pulse power levels at which crystalline peaks can be detected, a need exists to revisit the crystallization mechanism in light of the detailed thermal histories experienced across and surrounding the irradiated region and the Gaussian distribution of the laser beam across the irradiated surface. Laser energy density decreases exponentially in the radial direction and has a maximum at the center of the laser spot leading to greater temperature values at the center and a temperature gradient from the center towards the edges. In addition, laser beam intensity also produces a stress distribution which can be associated with its Gaussian profile resulting in an inhomogeneous stress across the beam diameter, tensile at the center and compressive at the edges. Such temporally and spatially dependent temperature and stress profiles can alter free volume, nucleation rate, and diffusion kinetics leading to rapid crystallization events and alternative pathways towards the crystalline phase. Temperature as a function of time of a simulated laser-irradiated spot at the top surface and below the top surface of an amorphous ribbon is shown in Fig. 2. The temporal temperature profile suggests temperatures above 2000K at the top surface which is beyond the melting point and most likely results in a local melting at the top surface layer with crystallization possible upon cooling. Temperatures estimated approximately 2 microns below the surface (within the skin penetration depth of Fe at the optical wavelength of Nd-YAG) are on the order of 1000K and likely not to reach melting temperatures, consistent with the surface deformation observed as illustrated in the SEM images of Fig. 2c. These temperatures significantly decrease within the distance from the center towards the edge of the laser spots suggesting diffusion of heat from the centers outwards and therefore different crystallization kinetics are expected.

**References:**

[1] M. E. McHenry, M. A. Willard, and D. E. Laughlin, Progress in Materials Science, vol. 44, no. 4, pp. 291–433, Oct. 1999 [2] A. Talaat, D. W. Greve, M. V. Suraj, and P. R. Ohodnicki, Journal of Alloys and Compounds, vol. 854, p. 156480, Feb. 2021 [3] G. Herzer, Acta Materialia, vol. 61, no. 3, pp. 718–734, Feb. 2013, doi: 10.1016/j.actamat.2012.10.040. [4] Y. Yoshizawa, S. Oguma, and K. Yamauchi, Journal of Applied Physics, vol. 64, no. 10, pp. 6044–6046, Nov. 1988 [5] K. Suzuki et al AIP Advances, vol. 9, no. 3, p. 035311, Mar. 2019, doi: 10.1063/1.5079778. [6] S. Katakam et al., Scripta Materialia, vol. 66, no. 8, pp. 538–541, Apr. 2012 [7] C. Smith et al., Materials Letters, vol. 122, pp. 155–158, May 2014 [8] L. Lanotte and V. Iannotti, Journal of Applied Physics, vol. 78, no. 5, pp. 3531–3533, Sep. 1995

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/b76b25d19ac56909b73662b71acd2ab3.jpg)
Fig. 1 XRD patterns of as-cast and laser-annealed Fe-based (a), and Co-based ribbons (b)

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/428c178d2a796bb0b353dfa63449a262.jpg)
Fig. 2. FEA simulations of temperature as a function of time at a laser power of 100mJ for (a) top surface and (b) below top surface of an amorphous ribbon. Red (0.6 mm), green (0.4 mm), and blue (0.2 mm) lines represent the distance from the center towards the edge of the laser spot. (c) SEM image of the ribbon surface layer showing evidence for local surface melting at the center of the laser irradiated region.

 Laser Processing of Soft Magnetic Metal Amorphous Nanocomposites

Fe-Co-Ni magnetic thin films with continuously varying compositions have been fabricated by the magnetron co-sputtering method. The films were characterized by high-throughput techniques. The results reveal the correlation between a range of compositions and the electrical properties of the films fabricated at various process parameters. Introduction: Soft magnetic materials are essential elements of electro-magnetic energy transformation technologies and they are widely used in various distribution, conversion, generation devices, such as transformers, motors, converters, generators, actuators, sensors etc. However, it usually takes long time for a new material before its acceptance for commercial application. Therefore, it is very crucial to speed up the discovery of new materials and incorporate them into various systems. High-throughput methods are efficient research methods [1-3] to explore this immense search space to identify new or optimized materials. Fe-Co based alloys received great attention due to high saturation magnetization. And what makes them even more fascinating is that their magnetic and electric properties can be tuned by controlling the alloy composition and microstructure. Among these compositions, Fe-Co-Ni films revealed significant induced magnetic anisotropy, low coercivity and high anisotropy of magnetoresistivity, what makes them a good candidate for technical applications. The resistivity is an important parameter to determine power loss in many soft magnetic applications. In this work we studied the effect of process parameters on the structure and resistivity of compositionally graded Fe-Co-Ni films to find process conditions at which optimum properties are obtained. Experimental details: Fe-Co-Ni films with continuously varying alloy compositions were fabricated by the magnetron sputtering method. Two experimental procedures were designed: a) Fe-Co-Ni films were deposited on SiO2/Si substrates by co-sputtering of permalloy and Co target materials using DC sources at different substrate temperatures (Ts): in particular, ambient temperature, 300 °C and 500 °C; b) the film was deposited at ambient temperature and annealed for 2 hours in vacuum at 500 °C. The base pressure in the chamber was controlled at 4 x 10 - 4 Pa. Depositions were performed in argon gas environment while the pressure was kept approximately at 0.3 Pa. For compositional, structural and electrical properties high-throughput Electron Probe Micro-Analysis (EPMA), X-ray Diffraction, four-point probe measurements were performed to determine chemical compositions, structure and resistivities of the films. Results and discussion: Fe-Co-Ni films with continuously varying alloy compositions were fabricated by magnetron sputtering method. The results of high-throughput Electron Probe Micro-Analysis measurements across Fe-Co-Ni films (Fig.1) revealed that atomic composition of Ni was highest, while Co was lowest in the film fabricated at Ts = 300 °C. The ratios of Co and Ni atomic compositions in deposited graded films were calculated as well. We found that Fe-Co-Ni film fabricated at Ts = 300 °C shows the lowest ratio as compared to other films. XRD measurements and analysis of multiple selected areas on Fe-Co-Ni film fabricated at ambient substrate temperature exhibited amorphous structure. As the substrate temperature increased diffraction peaks appeared, showing a clear change in structure. The diffraction patterns showed that only one FCC phase appeared. The peak intensity increased with temperature and the grain sizes became larger. The increase of peak intensity and average grain size indicated that increasing the substrate temperature from room temperature to 500 °C enhances the crystallinity of Fe-Co-Ni films. As for the annealed samples the intensity of the peak was low, and peak shifted towards lower angles indicating crystal lattice expansion. In addition, oxide peaks have been observed. Fig. 2 shows the measured resistivities as a function of composition of various process parameters. Resistivities of the graded film deposited at Ts =300 °C exhibited higher values than resistivities of the films deposited at ambient, 500 °C, and at ambient temperature followed by annealing at 500 °C. These results indicate that Ni plays important role in tuning resistivities of the films. Conclusion: Fe-Co-Ni films with continuously varying compositions have been fabricated by magnetron sputtering and characterized by high-throughput experimentation methods. The results revealed the correlation between continuously varying alloy compositions and selected properties of the films fabricated at various process parameters. Acknowledgement: This work is supported by the AME Programmatic Fund by the Agency for Science, Technology and Research, Singapore under Grant No. A1898b0043

**References:**

[1] Sean W. Fackler, Vasileios Alexandrakis, Dennis König, A. Gilad Kusne, Tieren Gao, Matthew J. Kramer, Drew Stasak, Kenny Lopez, Brad Zayac, Apurva Mehta, Alfred Ludwig and Ichiro Takeuchi, Science and Technology of Advanced Materials 2017, Vol.18, No.1, 231–238 [2] H. Koinuma, I. Takeuchi: Nat. Mater. 3 (2004) 429 –438. [3] Alfred Ludwig, npj Computational Materials (2019) 5:70

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/a7c2b3186ab8ed446ef672dcbe850a63.jpg)
Fig. 1 Elemental compositions of the graded Fe-Co-Ni films

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/dcd0207cd6dc3ac30e5af139256a3be1.jpg)
Fig. 2 Resistivities of Fe-Co-Ni films with continuously varying alloy compositions fabricated at different process parameters

 Effect of process parameters on the properties of compositionally graded FeCoNi films: A High Throughput Strategy

Recently, pearlitic wires, which experienced large drawing strains awoke the interest of material scientists due to their astonishing high strength of up to 7 GPa [1]. Because of the large amount of deformation applied during wire drawing, the grain size refines into the nanocrystalline regime and microstructural sizes of 10 nm and below are reported. The present study focusses on the capabilities to magnetically soften pearlitic steel by this “top-down”, conventional metal-forming process, as these length scales are already below the ferromagnetic exchange length of pure Fe. To do so, volume saturation magnetization and temperature dependent coercivities of wires experiencing high drawing strains (ε &gt; 5) were investigated. The results are compared to the ones of the initial wire, having more than twenty times the diameter and consequently a much coarser microstructure. To investigate the magnetic softening upon wire drawing, SQUID magnetometry and VSM measurements were performed. For the accurate determination of the volume saturation magnetization, the precise determination of the volume of the small samples is necessary. A confocal laser scanning microscope was used – the results allow the 3D reconstruction of the surfaces of the samples, for an example see inlay in Figure 1. From the surface reconstruction the volume can be calculated. It was found that the volume saturation magnetization is higher for the very thin wires in comparison to the initial state. While the thick, non-deformed wire shows a saturation magnetization very close to the one of pure pearlite, the saturation values for the thin wires are close to the one of pure body centred cubic (bcc) Fe (Figure 1). The slightly higher values, even in comparison to pure Fe, can be explained by C being supersaturated in the Fe matrix. The C necessary for supersaturation originates from the dissolution of cementite (Fe3C) during the wire drawing process [1]. Regarding the potential of wire drawing for magnetic softening, a decrease in coercivity was indeed found. The measured coercivities of the thin wires, determined with VSM, are smaller (24µm: 520 A/m, 36µm: 610 A/m) compared to the thick wire (1510 A/m). It is evident from magnetic measurements that there is a small but no substantial further refinement in grain size upon drawing the wire from 36 µm to 24 µm, although this constitutes a large degree of further deformation. Restoration mechanisms, as they are also known from other techniques involving severe deformation, seem to keep the grain size almost constant. For the thin wires, the grain size is calculated from the room temperature coercivity measurements. The grain size is found to be below the ferromagnetic exchange length of pure Fe, thus the random anisotropy model is applied. Using magnetic constants of pure Fe yields a grain size of 11 nm. This is in excellent agreement with atom probe tomography studies on the same material, where a subgrain size of 10 nm and below was found [2]. To further confirm the finding of dissolving cementite, the coercivity was determined as a function of temperature. Figure 2 includes calculated coercivities based on temperature dependent magnetocrystalline anisotropies for pure bcc Fe from [3–5]. Comparison reveals a very good match of measured and literature data; thus it can be safely assumed that the cementite has largely dissolved. Residual stresses, which might prevail from the drawing process would lead to an increased coercivity. Thus, a further softening of the drawn wires can be expected after thermal treatment, as it was the case for severe plastically deformed material, presented in [6]. One of the thin wires was annealed at 150°C for 30 min, which resulted in a decrease in coercivity by about 76 A/m or 12%. This proves the temperature stability of the microstructure at that temperature, as an increase in grain size would result in an increase in coercivity. The decrease in coercivity can be explained by reduced magneto-elastic effects, as residual stresses after wire drawing increase the effective anisotropy. In summary, pearlitic material was drawn to very high strains, resulting in very thin wires with nanocrystalline microstructure. Results of magnetic measurements indicate grain sizes close to 10 nm, the dissolution of cementite and a supersaturation of bcc Fe with C. It was possible to magnetically soften the coarse grained pearlitic steel from ~1500A/m to ~500A/m by this wire drawing process. However, the almost constant coercivity and grain size for very high drawing strains demonstrates that the magnetic softening seems to be maxed out. This project received funding from the European Research Council (ERC) under the European Union’s Horizon 2020 research and innovation programme (Grant No. 757333).

**References:**

[1] Y.J. Li, P. Choi, C. Borchers, et al., Atom probe tomography characterization of heavily cold drawn pearlitic steel wire, Ultramicroscopy. 111 (2011) 628–632. [2] Y. Li, D. Raabe, M. Herbig, et al., Segregation Stabilizes Nanocrystalline Bulk Steel with Near Theoretical Strength, Physical Review Letters. 113 (2014). [3] H.-P. Klein, E. Kneller, Variation of Magnetocrystalline Anisotropy of Iron with Field and Temperature, Phys. Rev. 144 (1966) 372–374. [4] B. Westerstrand, P. Nordblad, L. Nordborg, The Magnetocrystalline Anisotropy Constants of Iron and Iron-silicon Alloys, Phys. Scr. 11 (1975) 383–386. [5] I.M. Puzei, V.V. Sadchikov, Dependence of the magnetic-anisotropy energy in iron on the magnetic field, Sov. Phys. JETP. 70 (1990) 137–139. [6] M. Stückler, L. Weissitsch, S. Wurster, et al., Magnetic dilution by severe plastic deformation, AIP Advances. 10 (2020) 015210.

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/6e4821f573e1bd315f9ff4211724fec7.jpg)
Figure 1: Saturation magnetization for all investigated wires, measured at applied fields ≥ 2 T, taking into account the individual sample volume determined by confocal laser scanning microscopy. The values of pure bcc Fe and pearlite are included. As an inlay, the 3D-reconstruction of the wire surface of a small section of one of the 36µm-wires is shown.

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/885834416e94cd889410edd26013c0ba.jpg)
Figure 2: Measured and corrected temperature-dependent coercivity of one of the 36µm-wire as a function of temperature. Results are compared with coercivities calculated according to literature [3–5] on temperature dependent magneto-crystalline anisotropy. The coercivity of the annealed 36µm-wire is also shown.

 Soft magnetic properties of severely drawn pearlitic-ferritic wires with nanocrystalline microstructure

Organophosphates (OP) have been used to kill insects in many areas such as homes and workplaces, especially in agricultural pest control [1]. In many people, the remains of OP can lead to many health problems to range from paralysis to death. For this reason, it is very important to detect OPs, which is the most important way of passage to the human organism, as a sensitive, fast, and cheap way. Nowadays, conventional OP detection is carried out by techniques such as mass spectroscopy, gas chromatography, and high-performance liquid chromatography. Although these methods give accurate and sensitive results, they require time-consuming processes such as sample preparation, solid-phase extraction, and comparison of sample peaks with references. Moreover, the cost of these methods is quite high. Therefore, the development of an alternative method as sensitive, fast, practical and cheap for detection of OPs was carried out in this study. The system used in the detection of OPs is a magnetoelastic sensor (MES). Magnetoelastic sensors are preferred because of their low cost, disposable application, wireless and easier to use. Magnetoelastic materials begin to vibrate (shorten and elongate) when exposed to a time-varying (AC) magnetic field. The vibration frequency of such samples varies depending on the geometry, elastic coefficient and mass (density) of the sample [2]. In magnetoelastic sensors, the amount of mass usually deposited on the sensor surface causes a shift in the resonance frequency and the shift in the magnetoelastic measurement system is measured. In this way, the mass accumulated on the sensor surface can be measured. It is important that the sensor surface is functionalized according to the type of molecule being detected. The magnetoelastic sensor will be more precise and superior if it measures a very low mass change. Therefore, enlarging the sensor surface area makes a significant contribution to the sensitivity of the sensor. In this context, electrospun nanofibers were coated on the sensor surface in order to increase the surface area of magnetoelastic sensors for the first time within this study. Within the scope of this project, 2826MB (Fe40Ni38Mo4B18) amorphous ferromagnetic ribbons with 35 mm long and 5 mm in width were used as MES. Then, the nanofibers were functionalized with glutaraldehyde (GA) in order to covalently bind acetylcholinesterase (AChE) enzyme to the surface. The resonance frequency of the functionalized amorphous strip was measured to be around 59 000 Hz. OP in the 10% EtOH solution was dripped with a micropipette on the surface of the functionalized MES then allowed drying. It was observed that the EtOH solution evaporate and the remaining OP covalently binds the acetylcholinesterase (AChE) enzyme. When 50 ppm OP in 10% EtOH solution were dropped, a decrease of approximately 22 Hz was observed in the resonance frequency at 500 A/m DC bias magnetic field. Figure 1 shows the measured resonance frequency change when different amounts of OP were dropped onto the MES. As can be seen, MES shows a linear change according to the amount of OP measured in the range of 0-150 ppm in 10% EtOH solution. To determine whether the frequency shift comes only from the OP, only 10% EtOH solution was dripped onto the functionalized MES surface in different amounts and it was found that no shift in the frequency had occurred. Acknowledgment This work was supported by TUBITAK with 119F144 project number.

**References:**

[1] M. Eddleston, M.R. Phillips, BMJ. 328, 42 (2004). [2] C.A. Grimes, P.G. Stoyanov, D. Kouzoudis, K.G. Ong, Rev. Sci. Instrum., 70, 4711 (1999).

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/c1ac49f02f0ff5add6db01a39b73119c.jpg)
Fig.1. Variation of resonance frequency as a function of diazinon organophosphates amount.

 Detection of Diazinon Organophosphates Using Magnetoelastic Sensor

Owing to the augmentation of wireless communication, the development of electromagnetic interference (EMI) shielding structures is an open area for research. The devices working at microwave frequencies are hazardous to human health and can also result in the malfunctioning of various sensitive equipments. Various techniques are reported by the researchers for the development of an efficient EMI shielding structure, some of them are composite materials, nanocomposites, metamaterials, and frequency selective surfaces (FSSs) [1]-[3]. FSSs are an array of periodic slots or apertures having excellent electromagnetic (EM) wave filtering properties. Major challenges across the research community are to create a miniaturized, angular stable, wideband, polarization-insensitive, and flexible EMI shielding structure. Multiband structures are often used by researchers to get a wide bandwidth. Whereas, miniaturization is attained either by techniques like 3-D, convoluted geometries, and lumped capacitances. All these methods of bandwidth improvement and miniaturization result in complex design and therefore fabrication becomes tedious. Almost all reported EMI shielding structures uses pure dielectric substrates like FR4 and Rogers. However, bandwidth and miniaturization can be improved by increasing the overall inductance of the shielding structure. The introduction of lumped inductors can be a solution but it not only increases the fabrication complexities but also may result in unwanted parasitic capacitance. Also introducing active or reactive components limits the conformal applications of shielding structures. One possible solution is to use magnetic substrates, which will increase the overall inductance of the shielding structure. Therefore, in this work electromagnetic properties of two magnetic substrates (Ferrite and magnetic silicon rubber) are measured and investigated to improve the bandwidth and miniaturization of an EMI shielding structure. Further, a polarization-insensitive, angular stable FSS is designed and the equivalent circuit model (ECM) is developed to have a physical insight into the structure. Moreover, a competent deep neural network (DNN) approach is employed for fast and accurate optimization of the shielding structure. At last, a prototype is developed and measured for validation of the proposed technique. The schematic of the proposed shielding structure is depicted in Figure 1(a). It comprises an array of periodic unit cells, a magnetic ferrite substrate, and a silicon rubber sheet. Figure 1(b) demonstrates an FSS unit cell with corresponding geometrical design variables. Here, ro is the radius of the outer circle and ri corresponds to the radius of the inner circle. d is the length of the patch, w is the width, and periodicity of the unit cell is represented by p. The electromagnetic properties of magnetic substrates are measured using a waveguide-based microwave measurement technique. Figure 1(c) depicts the measured relative permittivity (εr) and permeability (μr) of both the substrates. The real part of μr varies between 2.10 and 1.49 and the imaginary part varies between 0.34 and 0.0025 for magnetic silicon rubber when the frequency changes from 8.2 to 12.4 GHz. The real part of εr is 5.50 and the imaginary part varies between 0.20 and 0.005. On the other hand, the ferrite substrate real part of μr changes varies between 1.17 and 1.13 and the imaginary part varies between 0.04 and 0.001. Moving a step further, ECM of the FSS backed substrates is developed and the overall impedance is calculated. A huge database is created using the ECM and a deep neural network is trained using the Levenberg-Marquardt algorithm. The entire dataset is divided into three sections randomly for training, validation, and testing in the proportion of 70%, 15%, and 15%. Once the training, testing, and validation of the network is done, the shielding structure is optimized for resonant frequency and bandwidth. A prototype is then fabricated from the optimized parameters using the printed circuit board (PCB) technique. Figure 2(a) shows the image of the fabricated prototype. Meanwhile, the effect of the magnetic properties of the substrates on the transmission performance of the shielding structure is investigated. When the permittivity of the substrates dominates, a bandwidth of 2.75 GHz is obtained with resonant frequency at 10.42 GHz as shown in Figure 2(b). The bandwidth of surfaces with quite high impedance is directly proportional to the square root of overall inductance. To increase the bandwidth and to achieve miniaturization substrates with dominant magnetic properties are used. The overall inductance of the structure is increased by using substrates with dominant μr. Figure 2(b) depicts when substrates with dominant permeability are used in place of permittivity dominant substrates resonance shifts to lower value as the overall inductance of the structure increased. Also, the bandwidth obtained from such magnetic substrate increased to 3.37 GHz from 2.75 GHz. Therefore, it can be concluded that using magnetic substrates bandwidth enhancement and miniaturization of the shielding structure can be achieved.

**References:**

[1] M. Sonehara, T. Sato, M. Takasaki, H. Konishi, K. Yamasawa and Y. Miura, "Preparation and Characterization of Nanofiber Nonwoven Textile for Electromagnetic Wave Shielding," IEEE Transactions on Magnetics, vol. 44, no. 11, pp. 3107-3110, Nov. 2008. [2] J. Lee, B. M. Jung, S. B. Lee, S. Lee and K. H. Kim, "FeCoNi-Coated Glass Fabric/Polycarbonate Composite Sheets for Electromagnetic Absorption and Shielding," IEEE Transactions on Magnetics, vol. 53, no. 11, pp. 1-4, Nov. 2017. [3] R. Panwar, S. Puthucheri, D. Singh and V. Agarwala, "Design of Ferrite–Graphene-Based Thin Broadband Radar Wave Absorber for Stealth Application," IEEE Transactions on Magnetics, vol. 51, no. 11, pp. 1-4, Nov. 2015.

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/cfe4cd73e62b6f4782155911aa08359e.jpg)
 
Figure 1. Proposed shielding structure (a) Schematic and FSS unit cell, and (b) Fabricated prototype

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/2627666b73e7db1a89ce3751c93f1ac6.jpg)
Figure 2. EMI shielding characteristics (a) Frequency-dependent electromagnetic characteristics of silicon rubber and ferrite substrates, and (b) Transmission performance for different configurations of FSS and substrates.

 Magnetic Substrate Coupled Broadband and Miniaturized Electromagnetic Interference Shielding Structure Using Deep Neural Network

Microwave absorbers are advanced electromagnetic structures that can competently deplete the incident electromagnetic (EM) wave, and widely utilized for stealth and electromagnetic interference mitigation applications. There have been enormous strides in the broadening of absorption bandwidth (BW) using thin and lightweight functional materials. Apart from functional materials, the shape and loading of the absorber are equally responsible for attenuating the EM wave. There are various potential structures capable of altering the equivalent EM properties of the material to achieve excellent absorption BW [1]-[2]. The simultaneous achievement of wide absorption bandwidth and lower coating thickness of the absorber layer is a very challenging task. In this work, an effort is made towards the design of thin and broadband triple-layer absorber by incorporating gradient air perforation into the absorbing sheets constituted of iron (Fe)-silicon carbide (SiC) composites synthesized by robust top-down fabrication technique. The gradient air perforation prompts viable absorption BW if the period and diameter of perforations are equivalent to the wavelength. Fe-SiC composites in distinct compositions (i.e., FS1, FS2, FS3, FS4, FS5, FS6, and FS7) have been utilized in the development of microwave absorber. The composites have been developed using a top-down fabrication technique accomplished via a high-energy planetary ball mill (Model: Insmart device, MBM-07, India). The milling process has been initiated by loading stainless steel containers with hard 20 mm and 10 mm diameter steel balls. The powder to ball weight ratio (PBR) of 1:10 was taken with the rotor speed to 400rpm. The EM properties of the composite were measured in the range of 8.2 to 12.4 GHz (i.e., X-band) using a waveguide-based microwave measurement technique. Further, Jaya’s-Grey Wolf based hybrid multiobjective optimization technique has been utilized for the modelling of a perforated multi-layered absorber using the measured EM parameters. The mathematical model of air perforation is integrated with the transmission line equations such that the developed structure appears like a gradient perforated triple-layer structure. The fitness function of maximum BW below -10dB with minimum thickness is organized in the hybrid optimization algorithm. An optimal sample has been fabricated using epoxy coating and drilling techniques based on the optimal design variables obtained using the algorithm. The schematic of 3D topology and fabricated porotype of perforated absorber constituted of Fe-SiC composites is shown in Figs. 1 (a) and (b), respectively. Fig. 2 shows the reflection coefficient curve (RC) of single-layer absorber at their optimal thicknesses. Among all Fe-SiC composite database, FS-7 composite achieves a minimum RC value of -24.7dB at 11.1 GHz at an optimal thickness of 1.7mm, covering an absorption BW of 3.1 GHz below -10dB threshold in X-band. Furthermore, FS-4 composite exhibits an absorption BW of 1.7GHz with a minimum RC value of -10.9 dB at 9.3 GHz at an optimal thickness of 1.7 mm. However, FS-3 composite achieves a minimum RC value of -9dB at 8.2 GHz demonstrating no absorption BW. In the proposed gradient structure, the hybrid optimization algorithm chooses composite FS-4 for layer 1 with an optimal thickness of 0.4 mm backed with a perfect electrical conductor. Consecutively, layers 2 and 3 (i.e., air absorber interface) are structured using FS-7 and FS-3 composites with an optimal thickness of 0.9 mm and 0.3 mm, respectively. The optimum air perforation diameter is 6 mm, 5mm, 4mm for FS-3, FS-7, and FS-4, respectively with a period of 20 mm. The magneto-dielectric properties of composite FS-3 are high as compared to FS-4 and FS-7 composites. Due to the larger diameter of air perforation, the effective magneto-dielectric properties are supervised to act as an impedance matching layer. A 1.6 mm multilayer structure (without hole) is compared with the proposed structure as shown in Fig. 2 (b). Due to gradient air perforation in the layered structure, the EM parameters are altered, which leads to the shift of resonance frequency. The obtained result reveals a better -10 dB absorption BW of 3.4 GHz with a minimum RC of -19.9 dB at 10.8 GHz. An exceptional microwave absorption is achieved in terms of peak RC and BW with a substantial reduction in the total coating thickness of 1.6 mm in comparison to a single-layer absorber. Moreover, due to perforation, the weight of the structure is also reduced. The gradient impedance alignment within the structure improves the other mechanisms of absorption, such as phase cancellation, internal reflection, and frequency dispersion within the structure which results in improved absorption BW.

**References:**

1. R. Panwar, S. Puthucheri, D. Singh and V. Agarwala, IEEE Transactions on Magnetics., vol. 51, no. 11, pp. 1-4 (2015). 2. L. Zhang, P. Zhou, H. Zhang, L. Lu, G. Zhang, H. Chen, H. Lu, J. Xie, and L. Deng, IEEE transactions on magnetics., vol. 50, no. 5, pp. 1-5 (2013).

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/a36d6e6475b0a7c1c80560119035c751.jpg)
Fig. 1. Schematic of perforated absorber (a) 3D topology and (b) fabricated porotype.

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/53df4f47bbf29bb3232a59d3911a61b0.jpg)
Fig. 2. Frequency-dependent RC curve of the absorber (a) single layer and (b) gradient perforated multilayered absorber in X-band.

 Fe-SiC Composite Constituted Multilayer Gradient Perforated Microwave Absorbing Structure for Stealth Applications

The μm-thick steels made by the rolling process may be promising magnetic materials for inductor and transformer cores utilized in power applications at high frequency [1]. From [2],[3], the annealing process can be used to enhance the magnetic characteristics of electrical steels, but the characteristics at high frequency of the annealed μm-thick steels have not yet been considered. To try reducing the core loss and improving the permeability of the 1 μm-thick steel significantly, we are researching and implementing a suitable annealing process for this thin steel. This abstract is the first work to investigate advantages of the annealed 1 μm-thick steel compared to the non-annealed 1 μm-thick steel of the same material in terms of the core loss and relative permeability in experiments where the excitation frequency is up to 1 MHz. Moreover, a measurement method for determining the core loss and relative permeability of the non-annealed and annealed steel parts attached in ring cores under test are concisely described in this study. The composition of the considered 1 μm-thick steel is 99.63% Fe, 0.003% C, 0.35% Mn, 0.009% P, and 0.007% S. The annealing process is performed at 450 °C in the atmosphere of Ar. The temperature was raised from the room temperature to 450 °C within one hour, and then held for one hour; last, the material was cooled in a furnace. For evaluation, there are three separate ring cores made and measured in this research. The first ring core is with the annealed 1 μm-thick steel part, the second ring core is with the non-annealed 1 μm-thick steel part, and the third one is a plastic core without a steel part for reference aim. All the ring cores have the same dimension and number of turns of copper coils as given in Fig. 1. The B-H analyzer Iwatsu SY-8219 [4] is utilized for measurement with the sinusoidal excitation method. The primary current I1 and secondary open-circuit voltage V2 of a ring core are measured to compute the magnetic field strength H and flux density B as shown in (1) and (2), respectively; then, the core loss per weight Pcm is calculated by (3). H = (N1.I1)/L (1) B = (∫V2.dt)/(N2.S) (2) Pcm = f.(∫H.dB)/(ρ.Wm) (3) Where N1 = N2 = 23 is the number of coil turns, L = 0.05 m is the average magnetic path length, S is the ring cross section area (and SRing1 = SRing2 = SRing3), ρ = 7874 kg/m3 is the steel density and Wm is the weight of steel part. The measurement method has four key steps as follows. STEP 1: The first ring core with the annealed 1 μm-thick steel part is connected to the B-H analyzer for measurement, where the excitation frequency is altered from f = 10, 50, 100, 200 kHz and up to 1 MHz. STEP 2: The third ring core without a steel part is connected to the B-H analyzer for another measurement. In this step, the maximum magnetic field strength HRing3,m of the third ring core is chosen to be equal to HRing1,m of the first ring core in Step 1 at each frequency. STEP 3: From the six known parameters BRing1,m, HRing1,m, SRing1, BRing3,m, HRing3,m and SRing3, where HRing1,m = HRing3,m, the maximum flux density thorough the annealed steel part BFe,Ring1,m and its relative permeability μFe,Ring1,r in the first ring core at each frequency are estimated by (4) and (5). We note that HRing1,m is suitably set in Step 1 to force BFe,Ring1,m to be fixed at 0.3 T in all the frequencies. STEP 4: Repeat Step 1 with the second ring core including the non-annealed 1 μm-thick steel part, and then repeat Step 2 with the third ring core where HRing3,m = HRing2,m. Similar to Step 3, the maximum flux density thorough the non-annealed steel part BFe,Ring2,m and its relative permeability μFe,Ring2,r in the second ring core are estimated by (4) and (5). HRing2,m is suitably chosen to cause BFe,Ring2,m to be fixed at 0.3 T. BFe,Ring[i],m ≈ (BRing[i],m.SRing[i] - BRing3,m.SRing3)/SFe,Ring[i] (4) μFe,Ring[i] = BFe,Ring[i],m/(μ0.HRing[i],m) (5) Where μ0 = 4π×10-7 H/m, SRing[i] = SRing3, and index i = 1 for the first ring core in Step 3, or i = 2 for the second ring core in Step 4. As depicted in Fig. 2(a), at the frequency f = 700 kHz, the core losses per weight Pcm of the non-annealed and annealed 1 μm-thick steels are 55.41 W/g and 28.71 W/g, respectively; furthermore, at f = 1 MHz, Pcm of the annealed steel is 43.95 W/g, while the core loss of the non-annealed steel maybe around 80 W/g as forecasted in the red dashed line. In addition, at f = 700 kHz, the relative permeability values μFe,r of the non-annealed and annealed steels are 216 and 401, respectively, as shown in Fig. 2(b); besides, at f = 1 MHz, μFe,r of the annealed steel is slightly reduced to 375. This research has assessed the magnetic properties of the annealed 1 μm-thick steel, where the excitation frequency is varied from f = 10, 50, 100 kHz and up to 1 MHz. In details, the core loss per weight Pcm and relative permeability μFe,r of the annealed and non-annealed steels at the maximum flux density of BFe,m = 0.3 T were measured and compared. The measured results showed that Pcm of the annealed 1 μm-thick steel is around 48.2% smaller than that of the non-annealed steel, and μFe,r of the annealed steel is around 185.6% larger than that of the non-annealed one. Thus, the 1 μm-thick steel implemented in an appropriate annealing process, which has the much better magnetic characteristics than that of the non-annealed steel, is potentially used for inductor cores in power electronic applications at high frequency.

**References:**

[1] M. Komatsubara, K. Sadahiro, O. Kondo, et al., “Newly Developed Electrical Steel for High-Frequency Use”, J. of Magnetism & Magnetic Materials, Vol. 242–245, Part 1, pp. 212-215 (2002). [2] M. C. Guimaraes, F. L. Alcantara, R. U. C. Moreira, et al., “Improvement of Magnetic Properties of a Reversible Hot Rolled Grain-oriented Electrical Steel,” IEEE Trans. on Magnetics, Vol. 52, No. 5, ID: 2002704 (2016). [3] J.-Y. Soh, K.-Y. Shin, H. Jung and S.-B. Kim, “Iron Loss Influenced by Magnetic Annealing in 0.1-mm-Thick Grain-Oriented High-Silicon Steels,” IEEE Trans. on Magnetics, Vol. 47, No. 10, pp. 3208-3211 (2011). [4] B-H Analyzer SY-8219, Iwatsu Electric Co., Ltd., www.iti.iwatsu.co.jp/en/pdf/BH_catalog14055E-108.pdf .

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/057bbf0542c33e34df6c5500185dca03.jpg)
Fig.1: Dimension of 1 μm-thick steel and ring core

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/b54c0a8cb837cfe33c5d9946799e6ade.jpg)
Fig.2: Measured results; (a) Core loss, (b) Relative permeability

 Experimental Investigation and Comparison of Magnetic Properties at High Frequency between Non-annealed and Annealed 1 µm-thick Steels

Yttrium Iron Garnet (YIG) is the benchmark material for ferromagnetic resonance; it is up to today the only magnetic material that is being integrated in on-shell electronic devices for its radiofrequency properties that combine high resonance quality factor (104) and frequency tunability. It is the goal of YIG magnonics to utilize this potential for a large variety of applications ranging from beyond complementary metal-oxide semiconductor (CMOS) computation to radiofrequency front-end and back-end analogue signal processing. YIG devices have however a severe drawback that is that they should include thermal stabilization. This is a necessity since YIG has a relatively low Curie temperature (∼550K) which results in a high sensitivity of its magnetization to temperature (∼4 Gauss/Kelvin). Here, we present a novel approach to solve this long standing issue by engineering the magnetic anisotropy in Bi substituted YIG. We evidence for those films that a vanishing effective magnetization yields high thermal stability over very wide temperature range: from 260K to 400K, where the frequency thermal drift is 50 times smaller than that of YIG. These types of properties can be leveraged for new applications where the temperature dependence of YIG is detrimental, while keeping the extremely low damping and insulating character of YIG[1]. For instance, this was key for the excitation of coherent spin-waves using SOT[2]. We anticipate that fabricating a material whose FMR frequency is temperature independent open new opportunities for the field of spintronics. In his seminal article[3] of 1948 Charles Kittel established the Ferromagnetic resonance (FMR) conditions of magnetic samples with arbitrary shapes stressing the importance of correcting the effective magnetic field that sets the Larmor frequency by taking into account the demagnetization field and the effect of uniaxial anisotropy. In today notations the FMR frequency can hence be written for a thin film in the in-plane magnetization configuration as: f=γ*(Ha*(Ha+(MS-Hu)))1/2. Where γ is the gyromagnetic factor, Ha is the applied magnetic field, MS is the saturation magnetization and Hu is the out-of-plane magnetization and the effective magnetization is defined as Meff = MS - Hu. It arises from this equation that the only temperature dependent terms are MS(T) and Hu(T). For most ferromagnetic materials Hu depends on MS with power law dependence defined by Callen and Callen theory[4]. Nonetheless, by engineering the magnetic anisotropy in Bi-YIG films, we were able to balance the saturation magnetization with the uniaxial anisotropy between 260K and 400K. These measurements were done on thin Bi1Y2Fe5O12 films of 21nm grown on (111)-oriented sGGG substrates with Pulsed Laser Deposition. We varied the substrate growth temperature within a range of 100°C and probed the films effective magnetization using FMR: we evidenced a magnetization state transition from in-plane to out-of-plane as the substrate growth temperature decreases from 500°C to 400°C. To ensure the nominal Bi content as well as the magneto-elastic anisotropy were maintained over all the growth temperature range, X-Ray Diffraction measurements were done and evidenced a perfect structural match between thin Bi1Y2IG films. Magneto-Optical Kerr Effect (MOKE) measurements were performed complementary to visualize not only the magnetic domains but also the magnetic anisotropy transition. With room temperature FMR measurements, we obtained the optimal substrate growth temperature range to be 420°C to 430°C: temperatures for which the effective magnetization Meff ≈ 0G. Interestingly, for thin films closest to the compensation, FMR measurements performed at lower temperatures evidenced that effective magnetization stay constant in a range of 140K: suggesting Hu(T)=Ms(T) contradictory with Callen and Callen theory[4]. Finally we measured the frequency thermal drift was about 1mT between 260K and 400K for films close to the compensation, FMR frequency is temperature independent.

**References:**

[1] L. Soumah, N. Beaulieu, L. Qassym, Nature Communication 9, 3355 (2018) [2] M. Evelt, L. Soumah, A.B. Rinkevich, Physical Review Applied 10, 041002 (2018) [3] C. Kittel, Physical Review 73, 155 (1948) [4] H. B. Callen and E. Callen, Journal of Physics and Chemistry of Solids 27, 1271 (1966).

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/e5e1e60b717ac1a92c59f4a6cb88abd2.jpg)
Fig. 1 Polar Magneto-Optical Kerr Effect (MOKE) measurement for a Bi-YIG thin film close to the compensation evidences the presence of magnetic domains.

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/7befc984861421507db377f3d886061b.jpg)
Fig. 2 Variation of the effective magnetization Meff(T) for Bi1YIG thin films within a range of 140K probed by Ferromagnetic Resonance (FMR) measurement.

 Fine tuning of the Magnetic Anisotropy results in Temperature Independent Ferromagnetic Resonance Frequency for Bi-YIG thin films grown by Pulsed Laser Deposition

The typical timescale for material discovery is remarkably long, taking between 10 – 20 years to propagate through idea conception, experimentation, optimisation, and deployment1. Existing global challenges such as the climate emergency require rapid development of new materials on timescales that are incompatible with the traditional linear material discovery approach. High-throughput approaches can be applied as a parallel material discovery methodology, for which a single sample contains a library of different material compositions that can be rapidly screened for the realisation of new magnetic materials. We apply the high-throughput material discovery approach to the new class of materials known as High Entropy Alloys (HEAs). HEAs often consist of five or more constituent elements mixed in near equal quantities. The name is owed to the resulting high configurational entropy of the alloy, which contributes to suppressing the formation of intermetallic phases and stabilises simple FCC and BCC solid solutions. HEAs occupy the unexplored central regions of phase diagrams, and as such, have potential to provide disruptive materials. Already HEAs have exhibited promising soft magnetic properties such as high saturation magnetisation alongside high electrical resistivity, as well as obtaining nanocrystalline textures2,3. However, the number of constituent elements and the various chemical compositions mean HEAs can be found in a very broad parameter space making it difficult to localise the search for useful compositions. This work has used combinatorial sputtering, to fabricate sample libraries containing composition variations of up to 35 at.% on a single Silicon wafer (Figure 1a). We investigate the (CoFeNi)1-x-yAxBy series, where A and B are 3d/4d transition metals (with the addition of Si and Al). Systems studied include CoFeNiMnAl, CoFeNiMnSi, and CoFeNiMnV. We implement a program to model the composition variation across a 3” Silicon wafer with three sputter sources at different incidence angles with concurrent deposition (Figure 1b). The resulting sample library is characterised using a high-throughput magneto-optical Kerr effect (MOKE) magnetometer which has been developed to automatically map the Kerr voltage (which is proportional to the magnetic moment) and coercive field across this sample library as function of HEA composition (Figure 1c). These can then be combined to achieve magnetic property mapping within the chemical composition space (Figure 1d). Following this, XRD, SQUID magnetometry, FMR and magneto-transport are used to generate a complete structural and functional property description of selected compositions. The resulting methodology not only provides a scalable process for magnetic HEA fabrication and characterisation, but can also be paired with data driven machine learning material discovery strategies such as Materials 4.04. The large datasets necessary for machine learning are costly to procure and so far lacking in functional magnetic properties (e.g. Ms, Hc) for which these high-throughput methods could provide.

**References:**

1. Y. Liu, T. Zhao, W. Ju and S. Shi, J. Materiomics 3, 159–177 (2017). 2. Y. Zhang, T. Zuo, Y. Cheng and P. K. Liaw, Sci. Rep. 3, 1455 (2013). 3. T. Zuo et al., Acta Mater. 130, 10–18 (2017). 4. R. Jose and S. Ramakrishna, Appl. Mater. Today 10, 127–132 (2018).

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/646e3021d243cac1b425ee3cb6de2f04.jpg)
Schematic representation of the high-throughput thin film methodology applied to magnetic material discovery, including (a) combinatorial sputtering, (b) modelling the composition across the wafer, (c) a measured Kerr Voltage map, and (d) mapping of magnetic properties as a function of chemical composition.

 High-throughput studies of magnetic High Entropy Alloys

The accelerated development of new soft magnetic materials is urgently required to address the challenges of next generation high frequency rotating electrical machines. We used high-throughput experimental and characterization techniques as well as thermodynamic modeling and machine learning (ML) to develop novel soft magnetic materials based on the Fe-Co-Ni alloy system. The experimental methods include (i) Direct energy deposition based additive manufacturing of compositionally graded bulk materials, (ii) Magnetic thin films with a range of compositions, (iii) Chemical flow synthesis of magnetic nanoparticles, (iv) Spark plasma sintered compositionally graded magnetic alloys. The structural, magnetic, mechanical, and electrical properties were determined. The feasibility of our strategy to develop new soft magnetic alloys has been demonstrated. Introduction: Soft magnetic materials are the key component for various applications such as electric motors and generators, magnetic shielding, robotics, electromagnets, sensors, etc[1, 2]. Such systems utilize a significant fraction of the total energy consumption of the world, hence increasing their efficiency will have a significant impact on the urgent need for energy conservation. High frequency rotating electrical machines require magnetic materials with a balance of magnetic, mechanical, and electrical properties. The traditional methods of developing such materials are costly and time consuming, limiting the opportunity to discover new excellent materials. Hence, high throughput methods are of high demand for accelerated discovery of novel materials and to improve the properties of existing materials. We present experimental and computational high throughput approaches to design new magnetic materials. Methods: Compositionally graded Fe-xNi[3], Fe-xCo, Fe-xNi-yMo, Fe-xCo-yNi samples were prepared by a DED process. High purity spherical Fe, Co, Ni, Mo powders with sizes ranging from 50 to 150 mm were employed. Thin film libraries of Fe-Co-Ni were prepared by co-sputtering of Ni-21Fe and Co targets using magnetron sputtering at a base pressure of 10-8 torr. Thermodynamic modeling was found to be very helpful to identify the heat treatment conditions [4]. The following characterization methods were employed: XRD for crystal structure and phase fraction, EPMA-WBS and EDX for composition, PPMS and magnetic field assisted TGA for magnetic properties, four-point probe for electrical resistivities, and nono(micro)-indentation for mechanical properties. A neural network model was trained on the data to predict the magnetic, mechanical and electric properties. Figure 1 shows the methods and the properties of our interest. Results and discussion: Additive manufacturing was utilized to explore a range of compositions. Iron rich ternary Fe-Co-Ni (Fe&gt; 75%, Co&lt;20%, Ni&lt;25%) alloys exhibit saturation magnetization (Ms), coercivity (Hc), Curie temperature (Tc) and hardness values ranging from 167 to 218.4 emu/g, 19.6 to 10.2 Oe, 534 to 940 °C, 185 to 359 Hv, respectively. Fe-8Co-9.1Ni and Fe-7.4Co-11.3Ni were found to have optimum magnetic and mechanical properties with Ms of 218.4 and 217 emu/g, Hc of 10.2 and 13 Oe, Tc of 765 and 741 °C, hardness of 334 and 359 Hv, respectively. In spark plasma sintered compositionally graded Ni-21Fe-xCo alloys, the largest Ms, Hc, Tc and HV were observed in Co rich samples while the resistivity was found to be larger in Ni rich samples. As an example, the compositions along the diameter of 7.6 cm sample of a co-sputtered thin film is shown in figure 2. Thus, the feasibility to accelerate the development of novel soft magnets has been demonstrated in the Fe-Co-Ni system. Acknowledgement: This work is supported by the AME Programmatic Fund by the Agency for Science, Technology and Research, Singapore under Grant No. A1898b0043.

**References:**

[1] V. Chaudhary, S.A. Mantri, R.V. Ramanujan, R. Banerjee, Progress in Materials Science 114 (2020) 100688. [2] J.M. Silveyra, E. Ferrara, D.L. Huber, T.C. Monson, Science 362 (2018) eaao0195. [3] V. Chaudhary, N.M. Sai Kiran Kumar Yadav, S.A. Mantri, S. Dasari, A. Jagetia, R.V. Ramanujan, R. Banerjee, Journal of Alloys and Compounds 823 (2020) 153817. [4] S. Dasari, V. Chaudhary, B. Gwalani, A. Jagetia, V. Soni, S. Gorsse, R.V. Ramanujan, R. Banerjee, Materialia 12 (2020) 100755.

**Images:**

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/920fbe1f51f6d92c3fa7416eceac2a0c.jpg)
Fig. 1 Soft magnetic materials development using accelerated (a) experimental, (b) computational and (c) characterization techniques, (d) measured/predicted properties

![](https://s3.eu-west-1.amazonaws.com/underline.prod/uploads/markdown_image/1/image/6b04517d314f4b720e708815ed8b0002.jpg)
Fig. 2 Change in composition across the diameter of circular graded thin film

Parametric Semi-Empirical Design of Magnetic Properties in Complex Concentrated Alloys: Curie Temperature and Saturation Magnetisation

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Parametric Semi-Empirical Design of Magnetic Properties in Complex Concentrated Alloys: Curie Temperature and Saturation Magnetisation

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