<![CDATA[ IEEE Magnetics Letters - new TOC ]]>
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TOC Alert for Publication# 5165412 2016September29<![CDATA[Demagnetizing Factors for a Hollow Sphere]]>m decreases from 1/3 when χ > 0 and increases from 1/3 when χ <; 0. In the limit a/b = 1, N_{m} decreases from 1 to 0 as χ increases from -1 to ∞. As a/b increases from 0 to 1, the fluxmetric demagnetizing factor N_{f} decreases from 1/3 and has a negative minimum when χ <; -3/4. These features are explained conceptually and quantitatively. As an application, magnetic shielding by a spherical shell is quantitatively analyzed.]]>714237<![CDATA[Transportation of Static Magnetic Fields by a Practically Realizable Magnetic Hose]]>714295<![CDATA[Calculation of Magnetization and Permeability Tensor of a Partially Magnetized Cylindrical Ferrite Resonator]]>111 mode. We also show that the mode-splitting behavior depends on a single magnetization value of the ferrite. The magnetization and permeability tensor components are computed from the measured resonant frequencies of the resonator. We present an analysis of cylindrical ferrite resonator and its experimental results.]]>714512<![CDATA[Steinmetz Equation for Gapped Magnetic Cores]]>714416<![CDATA[Scaling Law for AC Susceptibility of a Conducting Strip With a Power-Law Dependence of Electric Field on Sheet Current Density]]>c = (K/K_{c})|K/K_{c}|^{n-1} with n ≥ 1 is calculated as a function of the field amplitude H_{m} and frequency ω. A scaling law is deduced which states that χ/χ_{0}, χ_{0} being the negative of diamagnetic limit of χ, is invariant after ωaK_{c}/E_{c} and H_{m}π/K_{c} are multiplied by a constant C and C^{1/(n-1}), respectively.]]>714408<![CDATA[Calculation of Torque Performance of a Novel Magnetic Planetary Gear]]>7152140<![CDATA[Scaling Law for AC Susceptibility of a Superconducting Strip with a Power-Law Dependence of Electric Field on a Magnetic-Field-Dependent Sheet Current Density]]> $chi=chi^{prime}-jchi^{primeprime}$ of a superconducting thin strip of width $2a$ obeying a power-law dependence of electric field on sheet current density $E/E_c=(K/K_c)vert K/K_cvert^{n-1}$ with a Kim-model $K_c(H)=K_0[1+p_K^2vert Hvert/(K_0/pi)]^{-1}$ and average critical sheet current density $K_{c,mathrm{av}}$ is calculated as a function of the field amplitude $H_m$ and frequency $omega$. A scaling law is deduced which states that if $omega$ and $H_m$ are normalized as $thetaequiv mu_0 omega a K_{c,mathrm{av}}/2E_c$ and $h_mequiv H_mpi/K_{c,mathrm{av}}$, then for the $h_m$ at which $chi^{primeprime}$ takes its maximum, $h_m(chi_m^{primeprime},theta)=h_m(chi_m^{primeprime},1)theta^{1/(n-1)-beta}$ occurs with $chi_m^{primeprime}(theta)=chi_m^{primeprime}(1)theta^alpha$, positive numbers $-
alpha$ and $beta$ being functions of $n$ and $p_K$ only.]]>714559<![CDATA[Large Magnetic Entropy Change in La<sub>0.6</sub>Ce<sub>0.4</sub>Fe<sub>11.5</sub>Si<sub>1.5</sub> Alloy Exhibiting First- and Second-Order Phase Transitions]]>0.6Ce_{0.4}Fe_{11.5}Si_{1.5} was prepared by an arc-melting method. Magnetic measurements of magnetization M as a function of field H and temperature T show a ferromagnetic-paramagnetic phase transition at a Curie temperature TC = 170 K. Interestingly, curves of H/M versus M^{2} have a positive slope at low field (H ≤ 10 kOe), which corresponds to a second-order phase transition (SOPT), but a negative slope at high field (H > 10 kOe), which corresponds to a first-order phase transition (FOPT). The magnetic entropy change ΔS_{m}(T) under different ranges of field change ΔH, calculated from M(H) isotherms, has a maximum IΔS_{max}I around TC that increases in magnitude with increasing ΔH. Refrigerant capacity (RC), indicative of magnetic cooling efficiency, also increases with increasing ΔH. Curves of ΔS_{m}(T)/ΔS_{max} versus θ = (T - TC)/(Tr - TC), where Tr is the reference temperature, collapse into a universal curve when ΔH ≤ 10 kOe. In contrast, curves of ΔS_{m}(T)/ΔS_{max} versus θ do not reduce to a universal curve when ΔH > 10 kOe. These suggest a coexistence of FOPT and SOPT properties in the alloy.]]>714587<![CDATA[Dose–Response Bioconversion and Toxicity Analysis of Magnetite Nanoparticles]]>715480<![CDATA[Charge Relaxation in Biological Tissues with Extremely High Permittivity]]>6) may coexist. This situation is very peculiar and is not treated in textbooks. The model is used to study an open issue in electromagnetic dosimetry, namely the effect of charge relaxation on the motion-induced electric fields in the bodies of the operators working in magnetic resonance imaging environments.]]>715370<![CDATA[Control of Iron Oxide Nanoparticle Clustering Using Dual Solvent Exchange]]>2 relaxivity can be increased using this approach, while the specific absorption rate (SAR) is decreased. These results demonstrate a new, simple method for triggering the self-assembly of SPIO clusters using commercially available and biocompatible phospholipid-poly(ethylene glycol) (PEG) conjugates.]]>714443<![CDATA[Linear Control of Magneto-Electric Effect With Small Electric Fields]]>715447<![CDATA[Interface-Induced Spin Polarization in Graphene on Chromia]]>714463<![CDATA[Modulation of the Spectral Characteristics of a Nano-Contact Spin-Torque Oscillator via Spin Waves in an Adjacent Yttrium-Iron Garnet Film]]>714373<![CDATA[Low-Power, High-Density Spintronic Programmable Logic With Voltage-Gated Spin Hall Effect in Magnetic Tunnel Junctions]]>7151123<![CDATA[Dependence of Voltage and Size on Write Error Rates in Spin-Transfer Torque Magnetic Random-Access Memory]]>-6 error level for 655 devices, ranging in diameter from 50 nm to 11 nm, to make a statistically significant demonstration that a specific magnetic tunnel junction stack with perpendicular magnetic anisotropy is capable of delivering good write performance in junction diameters range from 50 to 11 nm. Furthermore, write-error-rate data on one 11 nm device down to an error rate of 7×10^{-10} was demonstrated at 10 ns with a write current of 7.5 μA, corresponding to a record low switching energy below 100 fJ.]]>714948<![CDATA[Oxygen Scavenging by Ta Spacers in Double-MgO Free Layers for Perpendicular Spin-Transfer Torque Magnetic Random-Access Memory]]>714921<![CDATA[Source Line Sensing in Magneto-Electric Random-Access Memory to Reduce Read Disturbance and Improve Sensing Margin]]>7151563<![CDATA[Non-Local Lateral Spin-Valve Devices Fabricated With a Versatile Top-Down Fabrication Process]]>714357<![CDATA[Magnetization Reversal by Field and Current Pulses in Elliptic CoFeB/MgO Tunnel Junctions With Perpendicular Easy Axis]]>714430<![CDATA[Perpendicular Magnetic Tunnel Junctions With Low Resistance-Area Product: High Output Voltage and Bias Dependence of Magnetoresistance]]>2. We obtain a maximum TMR ratio of 248% among the examined devices. The bias-voltage dependence of the TMR ratio for these junctions is almost the same as that for junctions with RA products of about 10-1000 Ω · μm^{2} in the positive voltage region, while a fast drop in the TMR ratio is observed in the negative bias region. An output voltage of more than 200 mV is obtained for these p-MTJs.]]>714486<![CDATA[Magnonic Holographic Read-Only Memory]]>2 at wavelength λ = 100 nm. We discuss the physical limitations and physical constrains associated with the spin-wave interference. The development of MH-ROMs opens a new horizon for building scalable holographic devices compatible with conventional electronic devices.]]>714381<![CDATA[High-Resolution Magneto-Optical Kerr-Effect Spectroscopy of Magnon Bose–Einstein Condensate]]>3. The measured linewidth is close to, but larger than, the lower limit estimated from previous indirect experiments based on the measurements of the condensate lifetime. Additionally, the technique enables a determination of the wavevector of the condensate k_{BEC} = 5×10^{4} cm^{-1}, which is in agreement with previous studies.]]>715626<![CDATA[Depinning of Domain Walls by Magnetic Fields and Current Pulses in Tapered Nanowires With Anti-Notches]]>12 A/m^{2} to 10 × 10^{12} A/m^{2} in the simulations, with a strong dependence on the domain wall type, but the experiment yielded higher critical current densities of 6 × 10^{12} A/m^{2} to 25 × 10^{12} A/m^{2}.]]>7152037<![CDATA[Effective Damping Constant and Current Induced Magnetization Switching of GdFeCo/TbFe Exchange-Coupled Bilayers]]>$alpha$ and effective perpendicular magnetic anisotropies $K_{{rm eff}}$ of amorphous GdFeCo ($10 - {x}$ nm)/TbFe ($x$ nm) exchange-coupled bilayers with various TbFe layer thicknesses $x$ were measured. The products $alpha times K_{{rm eff}}$ of the bilayers were compared with the critical current densities $J_{{rm c}}$ for current-induced magnetization switching (CIMS) in giant magnetoresistance nanopillars with a GdFeCo/TbFe memory layer. The damping constant $alpha$ of the bilayers, estimated from time-resolved magneto-optical Kerr effect measurements, was 0.051 for ${x} = 0$, and was significantly enhanced to 0.23 for ${x} = 1$ . The anisotropy constant $K_{{rm eff}}$ and the product of saturation magnetization times anisotropy field M_{ s}H_{k} also increased with increasing TbFe thickness $x$. The CIMS of the GdFeCo (9 nm)/TbFe (1 nm) bilayer exhibited 1.6 times larger J_{c} than that of GdFeCo (10 nm), while -
he product $alpha times K_{{rm eff}}$ increased by a factor of 10.]]>715367<![CDATA[Compact Beam Steering Antenna With Low-Loss Co<inline-formula><tex-math notation="LaTeX">$_2$</tex-math> </inline-formula>Y-Type Hexagonal Ferrite Elements for Wireless Multiple-Input Multiple-Output (MIMO) Antenna Applications]]>2Co_{1.9}Zn_{0.1}Fe_{12}O_{22}) has been developed for miniaturization and performance improvement of wireless multiple-input multiple-output (MIMO) antennas. The ferrite material has permittivity and permeability of 6.7 and 2.1, respectively, with dielectric loss tangent less than 0.007 and magnetic loss tangent less than 0.034 below 2.5 GHz. A beam steering antenna operating at 2.4 GHz band was designed and fabricated using the ferrite elements having a total volume of 18 mm × 18 mm × 100 mm, which has compact size, low loss, and good radiation characteristics. The antenna offers three modes with nine radiation beam patterns at the frequencies of 2.4 GHz band. The measured peak gain of all beam patterns ranges from 4.0 to 6.8 dBi.]]>715780<![CDATA[Monte Carlo Modeling of Mixed-Anisotropy [Co/Ni]<sub>2</sub>/NiFe Multilayers]]>2/NiFe multilayer have been studied as a function of the NiFe thickness by using Monte Carlo modeling and compared with experimental results of [Co/Ni]_{4}/Co/NiFe multilayers. Both modeling and experiment showed that the NiFe thickness controls the effective anisotropy. The direction of the easy axis is determined by a competition between the perpendicular crystalline anisotropy of the Co/Ni and the shape anisotropy of the multilayer. As the thickness of the NiFe layer increases, the reversal mechanism of the thin film changes from the nucleation of reverse domains to vortex propagation. Therefore, our results reveal the magnetic configurations and the easy axis reorientation of mixed-anisotropy multilayers.]]>715437<![CDATA[Ferromagnetic FePt/Au Core/Shell Nanoparticles Prepared by Solvothermal Annealing]]>0 phase with a coercivity up to 2.8 kOe at room temperature.]]>715603<![CDATA[An Intertrack Interference Subtraction Scheme for a Rate-4/5 Modulation Code for Two-Dimensional Magnetic Recording]]>715596<![CDATA[Analysis of Multilayered Co-Zr-Nb Film On-Chip Noise Suppressor as a Function of Resistivity and Permeability]]>714471<![CDATA[Simultaneous Detection of Giant Magnetoimpedance and Fast Domain Wall Propagation in Co-Based Glass-Coated Microwires]]>50.69Fe_{8.13}Ni_{17.55}B_{13.29}Si_{10.34} and glass-coated microwires produced by the Taylor-Ulitovsky technique are investigated systematically. Magnetic-field frequency dependences of magnetoimpedance (MI), domain-wall (DW) velocity, and hysteresis loops were measured. At certain annealing conditions, high MI and fast DW propagation simultaneously coexist. The results suggest criteria for the selection of materials for high-performance magnetic sensors.]]>714651<![CDATA[Preparation and Characterization of Fe-Pt and Fe-Pt-(B, Si) Microwires]]>3 (A1) disordered phase in the as-prepared state. We obtained microwires with coercivities from 4 to 140 Oe, which can be explained considering different metallic nucleus microstructures.]]>714475<![CDATA[Microstructure and Magnetic Properties of Melt-Spun Nd-Rich Nd-Fe Alloys]]>714457<![CDATA[Photoinduced Ultrafast Magnetization Dynamics in Yttrium-Iron Garnet and Ultrathin Co Films]]>714344<![CDATA[Magnetic Properties of Nd and Sm Rare-Earth Metals After Severe Plastic Deformation]]>7141036<![CDATA[Electronic Structure of La–Co Substituted Strontium Hexaferrite (Sr<sub>1 - x</sub>La<sub>x</sub>Fe<sub>12 - x</sub>Co<sub>x</sub>O<sub>19</sub>) Permanent Magnet]]>12O_{19} and La^{3+} - Co^{2+} pair substituted Sr_{1-x}La_{x}Fe_{1-x}Co_{x}O_{19} ferrites (x = 0.1 - 0.5). First-principles calculations were performed on the ferrites to calculate electronic structures. The substitution of La^{3+} - Co^{2+} in the 2d and 2a sites decreased the lattice constants and total magnetic moment per unit cell. The moments at 2b, 12k, 4 f1, and 4 f2 sites are not affected by the substitution. Nonsubstituted SrFe_{12}O_{19} is a semiconductor, but becomes half-metallic when La^{3+} and Co^{2+} are substituted in the 2d and 2a sites, respectively.]]>713524<![CDATA[Corrosion Losses in Sintered (Nd, Dy)–Fe–B Magnets for Different Geometries]]>714568<![CDATA[Magnetic Characteristics of Single-Block and Multi-Block Nd-Fe-B Permanent Magnets at Low Temperature]]>715730<![CDATA[Nonlinear Energy Harvesting Using Electromagnetic Transduction for Wide Bandwidth]]>714442<![CDATA[A New Method for Determining the Curie Temperature From Magnetocaloric Measurements]]>714328<![CDATA[Optimum Annealing Conditions for the Magnetocaloric Effect in Mn-Fe-P-Ge Alloys]]>1.1Fe_{0.9}P_{0.75}Ge_{0.25} powder samples were determined for various annealing conditions. The MCE was significantly influenced by annealing. The optimum annealing temperature and time for maximum relative cooling power (~303 J kg^{-1}) were 1123 K and 9 h, respectively. The maximum magnetic entropy change (~25 J kg^{-1}K^{-1}) was obtained after annealing at 1223 K for 9 h, but this was accompanied by maximum thermal hysteresis.]]>7141709<![CDATA[Sub-Millimeter Pitch Multipole Magnetization in a Sintered Nd-Fe-B Magnet Utilizing Laser Heating]]>7141607<![CDATA[Synthesized Magnetic Field Focusing Using a Current-Controlled Coil Array]]>714538<![CDATA[High-Time-Resolution Nuclear Magnetic Resonance With Nitrogen-Vacancy Centers]]>715758<![CDATA[Characteristics of a Magnetostrictive Composite Stress Sensor]]>0.3Dy_{0.7}Fe_{2}), and epoxy resin has been used to fabricate mechanical stress sensors that are electrically isolated and based on the Villari effect (or inverse magnetostriction). Under an external mechanical stress, magnetic domains in the MCM rotate and expand proportionally, modifying the magnetic properties due to the Villari effect. We designed a probe consisting of a toroidal, laminated, air-gapped silicon steel core with a tightly wound coil that facilitated monitoring the change in the magnetic susceptibility of the MCM. Since the coil is wound around the core and the air gap is partially filled with the MCM, the change in magnetic susceptibility of the MCM can be estimated by performing inductance measurements. We investigated the effect of the angle between the stress and magnetic susceptibility measurement axes on the response of MCM sensors mounted at different angles onto 6061-T6 aluminum substrates. This sensing technique can be used for non-destructive evaluation and monitoring the integrity of various mechanical and civil engineering structures. This wireless technique might also be extendable to measure the stress vector.]]>714578<![CDATA[First-Order Reversal Curve (FORC) Analysis of Magnetocaloric Heusler-Type Alloys]]> Heusler-type alloy exhibiting inverse magnetocaloric effect were studied with the help of first-order reversal curves (FORC). These have been measured using two different protocols (either upon heating or cooling the sample) and using different applied magnetic fields. For proper comparison, FORC distributions were shifted according to the field dependent center of the hysteresis loop, which follows a linear trend. The qualitative behavior of FORC distributions remains the same, allowing their use for fingerprinting the transition, while there is a shift of their maxima along the hysteretic temperature axis and their distributions also get broader along the interaction temperature axis with increasing magnetic field. This was evidence that FORC distributions are dependent on the intensive variables temperature and field. As a consequence, it is necessary to obtain them for different temperatures and fields in order to accurately model the transition.]]>714501