Scholarly article on topic 'Voltage control of ferromagnetic resonance'

Voltage control of ferromagnetic resonance Academic research paper on "Nano-technology"

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Journal of Advanced Dielectrics
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Academic research paper on topic "Voltage control of ferromagnetic resonance"


JOURNAL OF ADVANCED DIELECTRICS Vol. 6, No. 2 (2016) 1630005 (12 pages) © The Author(s)

DOI: 10.1142/S2010135X1630005X

World Scientific


Voltage control of ferromagnetic resonance

Ziyao Zhou*, Bin Peng*, Mingmin Zhu* and Ming Liu*^ *Electronic Materials Research Laboratory Key Laboratory of the Ministry of Education & International Center for Dielectric Research, Xi'an Jiaotong University Xi' an 710049, P. R. China ^

Received 8 December 2015; Revised 4 April 2016; Accepted 6 April 2016; Published 16 May 2016

Voltage control of magnetism in multiferroics, where the ferromagnetism and ferroelectricity are simultaneously exhibiting, is of great importance to achieve compact, fast and energy efficient voltage controllable magnetic/microwave devices. Particularly, these devices are widely used in radar, aircraft, cell phones and satellites, where volume, response time and energy consumption is critical. Researchers realized electric field tuning of magnetic properties like magnetization, magnetic anisotropy and permeability in varied multiferroic heterostructures such as bulk, thin films and nanostructure by different magnetoelectric (ME) coupling mechanism: strain/stress, interfacial charge, spin-electromagnetic (EM) coupling and exchange coupling, etc. In this review, we focus on voltage control of ferromagnetic resonance (FMR) in multiferroics. ME coupling-induced FMR change is critical in microwave devices, where the electric field tuning of magnetic effective anisotropic field determines the tunability of the performance of microwave devices. Experimentally, FMR measurement technique is also an important method to determine the small effective magnetic field change in small amount of magnetic material precisely due to its high sensitivity and to reveal the deep science of multiferroics, especially, voltage control of magnetism in novel mechanisms like interfacial charge, spin-EM coupling and exchange coupling.

Keywords: Multiferroics; magnetoelectric coupling; ferromagnetic resonance; voltage control; thin films.

1. Introduction

Multiferroic materials1-9 are the materials that combine two or more of the ferroic properties including ferroelectricity, ferromagnetism and ferroelasticity, etc. Both single-phase multiferroic materials and multiferroic composites attract lots of researchers' efforts to obtain magnetic field (H-field) control of electric polarization (direct magnetoelectric (ME) effect), or electric field (E-Field) manipulation of magnetization (converse ME effect) through ME coupling and then lead to varied multiferroic devices. Multiferroic composites, for instance, layered ferromagnetic/ferroelectric and ferromagnetic/piezoelectric multiferroic heterostructures, compared to single-phase multiferroics, has much stronger ME coupling strength that is 1-2 order higher than singlephase multiferroics.

The ever increasing demand of smaller, faster, low energy consumption tunable electronics10,11 such as antennas,12-14 inductors,15-17 voltage tunable RF/microwave signal processing devices,18-21 ME sensors,22,23 energy harvesters,24 filters,25,26 etc., has propelled the discovery of controlling

magnetic properties such as magnetization, magnetic anisot-ropy and permeability through energy conservation between electrical energy and magnetic energy. Controlling magnetic properties through electric field without magnetic field from bulky, noisy and energy consumption electromagnetics (EM) is critical in these devices. For example, data storage devices are recently becoming so small that the local magnetic field that is writing a single bit is easily influencing the neighboring bits, introducing instabilities in the stored data. To overcome the issue is to create new material composites and functionalities while integrating them into nonvolatile, lightweight and energy-efficient memory devices. In addition, the E-field controllable memory devices are much faster due to quicker response of E-field tuning magnetism in multiferroics.

Within state-of-the-art RF/microwave devices, materials-dependent ferromagnetic resonance (FMR) frequencies of magnetic materials can be manipulated by electromagnets; therefore, limiting their deployment in radar, satellite, aircraft, cell phones and portable communication devices in which

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mass, volume and power consumption are considered at a premium. Thus, tuning the FMR of magnetic materials by electric field is of great importance to achieve next generation voltage controllable RF/microwave devices. In this review paper, we will discuss the recent progresses of voltage control of FMR in different multiferroic composites and by different ME coupling mechanisms.

Conventional ME coupling in multiferroic hetero-structures were realized through strain/stress interaction between ferromagnetic phase and ferroelectric phase.27-49 Lots of layered strain/stress dominated multiferroic hetero-structures such as bulk/bulk,27-31 thin film/bulk32-45 and thin film/thin film47 magnetic/ferroelectric or magnetic/piezoelectric heterostructures were demonstrated in this paper. By applying voltage across the ferroelectric/piezoelectric layer, the ferroelectric/piezoelectric layer generates a large strain/stress energy change that influence the magnetic layer, therefore, change the effective magnetic anisotropy energy which lead to an effective FMR field or frequency change. The pioneering work began with YIG/PZT,27 Terfenol-D/ PMN-PT30 layered bonding layered magnetic/ferroelectric multiferroic devices. Nevertheless, the FMR tunability (< 200MHz)25-27 is limited by bulky magnetic slab and bonding interface. Further, researchers deposited nanoscale magnetic thin film onto well-polished ferroelectric/piezoelectric slab such as Ni/PMN-PT,32 FeGaB/PZT,36 FeGaB/ PZN-PT,42 Terfenol-D/PZN-PT,43 etc. The well-established interface and magnetic thin film allows the strain/stress energy transferred and affected magnetic energy efficiently. As a result, giant FMR tunability (> 3500 Oe, > 13 GHz)42,43 was achieved in these heterostructures. For real Si-based integrated circuit, piezoelectric thin films (ZnO)46,47 with lower fabrication temperature (< 90 °C) are considered and thin film multiferroic heterostructure of Fe3O4/ZnO47 was studied. The tunability was also limited by sample clamping effect.

To conquer the limitation of thin film multiferroic het-erostructure, other mechanisms like EM-spin wave coupling, interfacial charge and exchange coupling were developed and studied.49 50 In YIG/BSTO thin film heterostructure, - 5-6 Oe small FMR field change was observed by EM-spin wave coupling.49 Interfacial charge-induced ME coupling in ul-trathin magnetic film (—1nm) also do not suffer from sample clamping effect,51-59 for example, — 60 Oe (NiFe/SrTiO3)58 and — 200 Oe (NiFe/PMN-PT)59 FMR field tunability was demonstrated. FMR tunability was also shown in MgO ultrathin film magnetic tunneling junctions (MTJ).60,61 Recently, a reversible, nonvolatile FMR field switch of 60 Oe from CoFe/BiFeO3 (BFO) system62-73 was shown and all these achievements pave a way to voltage controllable RF/microwave military/civilian devices. Beyond voltage control of FMR, in contrast, the FMR measurement technique, for example, electron spin resonance (ESR)73 method is a unique way to determine very small the E-field control of magnetic anisotropic field change in small amount of magnetic material in multiferroic heterostructures.

2. Voltage Control of FMR through Strain/Stress-Induced ME Coupling in Different Multiferroic Heterostructures

In many researches, controlling of strain/stress of piezoelectric/ferroelectric substrates is the ideal way to change magnetic properties of magnetic components that are coupled to piezoelectric/ferroelectric substrates.32-48 The E-field was applied across substrate and the magnetic field was applied along the in-plane (IP) direction, vertical to the microwave propagation. As an E-field is applied, the piezoelectric substrate undergoes a tensile or compressive deformation and that strain can be coherently transferred to magnetic films resulting in an effective magnetic field Heff through the magnetoelastic effect. Heff can be written as:

Heff = 3ASYdE/M0MS,

where As is the magnetostriction constant of magnetic materials, Y is Young's modulus, d is the piezoelectric coefficient of ferroelectric substrate and MS is the magnetization.33,34 To obtain strong ME coupling, large AS, d and small MS are needed. By using Kittel equation, FMR frequency can be calculated as33,34:

f(Hr + Heff )(Hr + Heff + 4-kMs) ,

where Hr is the resonance field, f is microwave frequency and 7 =2.8 MHz/Oe is gyromagnetic ratio. By controlling the effective field Heff, the FMR frequency, as a consequence, can be easily manipulated.

2.1. FMR tuning in bulk multiferroic heterostructures

High permeability and high permittivity multiferroic composites with strong ME coupling at RF/microwave frequencies provide great opportunities for future compact, lightweight and power efficient voltage tunable RF/ microwave devices. Numerous multiferroic devices such as

antennas,12-14 inductors,15-17 voltage tunable RF/microwave signal processing devices,18-21 ME sensors,22,23 energy harvesters,24 filters,25,26 etc., are developed. For example, the microstrip bandpass filter is based on FMR of ferrite component. The device operating at 5-10 GHz can be tuned over a wide frequency band by a bias magnetic field and over a narrow band with a voltage applied across piezoelectric component. The voltage tuning of the device is possible through ME interactions that are mediated by mechanical deformation and manifests as a shift in FMR. Data on tuning range, insertion loss and device characteristics are presented for filters with single- and double-ME resonators.

Figure 1 shows a dual H-field and E-field controllable Ni-ferrite/PMN-PT multiferroic bandpass filter.19 H-field bias of 0, 75 and 100 Oe were applied along the y-axis of the bandpass filter and E-field from 1 to 9 kV/cm is applied along the thickness direction of the PMT-PT slab in bandpass filter. As shown in Fig. 1(a), a maximum ME tunability of 270

Fig. 1. (a) Measured E-field tunable operating frequency range of the bandpass filter under different magnetic bias fields, showing the dual E- and H-field tunability. (b) Diagram showing the device with ferrite/PMN-PT multiferroic heterostructure.19

MHz (2.1%) was obtained at 100 Oe H-field bias field, when E-field is applied from 3 kV/cm to 9 kV/cm. The central frequency was shifted from 13.22 GHz to 13.33 GHz correspondingly.

To further increase the tunability of bulk ME laminates, according to Eq. (1), piezoelectric substrates with larger piezoelectric coefficient d should be considered. Tatarenko and Bichurin designed and fabricated layered YIG/PMN-PT structures,29 see Fig. 2, in which the PMN-PT has stronger piezoelectric property. The ME coupling theory and experiment of attenuators, bandpass filters and phase shifters were discussed. Figure 2 shows the design of YIG/PMN-PT attenuator and the tunability of insertion loss from 26 dB to 2dB at 7.251 GHz by applying E-field across the PMN-PT substrate. Other multiferroic devices like bandpass filter and phase shifter were also discussed: tunability of 25MHz in bandpass filter at 7.36 GHz frequency achieved, meanwhile, a 30-40 ° phase shift around the frequency range of 6-9 GHz was obtained in YIG/PMN-PT multiferroic composites.

2.2. FMR tuning in thin film/bulk multiferroic heterostructures

Eventually, bulk multiferroic composites suffer from limited tunability due to sample clamping effect of magnetic bulk component as well as the poor adhesion condition of interface


Fig. 2. (a) Design of microstrip ME attenuator and ME resonator.

(b) Experimental curves of insertion loss versus frequency. YIG [111] thickness is 110 ^m; diameter is 2.5 mm; PMN-PT thickness is 0.5 mm; diameter is 6 mm; field H = 1910 Oe; field is parallel to plane of sample; central frequency is 7251MHz.

(c) Comparison of experimental and theoretical data. YIG [111] thickness is 110 ^m; diameter is 2.5 mm; PMN-PT thickness is 0.5 mm; diameter is 6 mm. Field H = 1910 Oe; field is parallel to plane of sample; average is 30; central frequency is 7251MHz.29

between ferromagnetic slab and ferroelectric substrate. Achieving strong ME coupling in multiferroic hetero-structures has been of paramount importance for achieving multiferroic devices with large tunability. First of all, magnetic thin film/ferroelectric slab is an improved multiferroic heterostructure for its better adhesion at the interface and magnetic thin film can be influenced by strain/stress change easily. In addition, known from Eq. (1), to further increase the ME coupling coefficient, magnetic thin film with large magnetostriction XS and piezoelectric substrate with large piezoelectric coefficient of d should be considered.

Lou et al.37 developed a FeGaB/PZN-PT (lead zinc nio-bate-lead titanate) bilayer multiferroic heterostructure, in which, the FeGaB alloy has high magnetostriction of ~ 80 ppm and relative small coercivity field of < 10 Oe and narrow FMR linewidth of < 5 Oe that proves the good soft and RF/microwave property of FeGaB thin films. The PZN-PT single crystal that has high piezoelectric coefficient > 3000 pC/N serves as piezoelectric substrate. By applying E-field of 0kV/cm to 8 kV/cm, a large FMR frequency (S21) switching from 1.75 GHz to 7.57 GHz (5.82 GHz) was obtained, see Fig. 3. These novel ME multiferroic hetero-structures with strong ME coupling provide great opportunities for multiferroic devices.

To push the FMR tunability limitation, Liu et al. then demonstrated a Terfenol-D/PZN-PT composite bilayer structure with an effective E-field-induced magnetic anisot-ropy field of 3500 Oe and a corresponding ME coefficient of 580 Oe cm/kV.42 So far, this is the highest E-field-induced ME coupling field to date, resulting in a strong tunable FMR in both amorphous and crystalline Terfenol-D films. The reason why they choose Terfenol-D alloy thin film as magnetic thin film is that it has the highest magnetostriction of 320-420 ppm among magnetic materials. Figure 4(a) shows the E-field dependence of FMR spectrum of Terfenol-D/PZN-PT. The FMR field is shifted upward by 3500 Oe as applying an E-field of 6 kV/m, indicating a record-high E-field-induced FMR field change of 3500 Oe and a giant

ME coefficient of 580 Oe cm/kV. The E-field dependence of FMR field or both amorphous and polycrystalline Terfenol-D/PZN-PT composites (see Fig. 4(b)) was also investigated. The resonance fields or effective magnetic fields were dramatically increased up to 3500 Oe and 2700 Oe for poly-crystalline and amorphous Terfenol-D/PZN-PT, respectively.

Although giant tunability of Terfenol-D/PZN-PT was achieved, the microwave property like linewidth of Terfenol-D is very large and that will limit its application in real devices. Moreover, the tunability of FMR frequency, instead of FMR field, should be studied. By using a new technical solution with dual E- and H-field controlling, the ME tun-ability dramatically enhanced FMR tunability range up to 13.1 GHz in FeGaB/PZN-PT multiferroic heterostructure,43 see Figs. 5(a) and 5(b), which will greatly satisfy engineering requirements for a variety of microwave applications. In addition, with regard to the hysteretic and reversible E-field-induced phase transition in single-crystal PZN-PT (011) substrates, we successfully realize a novel voltage-impulse-induced memory-type magnetization switching and FMR tuning in FeGaB/PZN-PT(011) multiferroic heterostructures. Extremely large converse ME coupling coefficients of 3850 Oe cm kVand 3620 Oe cm kVare observed at

3.5 5.5 7.5 Magnetic Field (kOe)

Fig. 3. (Color online) Data showing a high electric field tunable FMR frequency range from 1.75 GHz to 7.57 GHz at zero magnetic field and 0 kV/cm to 6 kV/cm E-field.37

Fig. 4. (Color online) (a) FMR spectra of polycrystalline Terfenol-D/PZN-PT at E =0 kV/cm (blue) and E =6 kV/cm (red). (b) E-field dependence of resonance field for polycrystalline (red) and amorphous (blue) Terfenol-D/PZN-PT.41

« „ . H-4M09

Y _J\__j\ _ .

ii=5.£3 GHi

^ V H=20B0 Oe

-ir- —Kr-KAt-

-ekV^rn (Hff [1D0II

-a k'.'/tm ;i:iiT|; j

Afab=13.1 GHZ

J to 12 Frequency (GHz)

Fig. 5. (a) E-field-induced FMR frequency shift under various magnetic bias fields. (b) Comparison of theoretical simulation (solid line) and experimental results (symbols) of electric field-induced FMR change under various magnetic bias fields.42

phase transition points of 3kVcm—1 and 5.8 kV cm_1, respectively.

Besides FMR tunability, the nonvolatile controlling use voltage impulse, instead of constant voltage to tune the FMR frequency, is of great importance of nonvolatile ME devices that has much smaller energy consumption and with strong memory effect. Liu et al.43 studied a unique ferroelastic switching pathway in (011)-oriented PMN-PT (0.71Pb (Mg1/3Nb2/3)O3-0.29PbTiO3), see Fig. 6(a), single crystals that allows up to 90% of the polarization to rotate from an out-of-plane to a purely IP direction (71 ° and 109 ° switching), thereby producing two distinct, stable and electrically reversible lattice strain states. All FMR measurements were taken in a co-planar waveguide, see Fig. 6(b). Voltage-impulse switching between these remnant strain states is demonstrated and results in a highly energy-efficient, nonvolatile tuning of FMR field of 320 Oe (Fig. 6(c)) and FMR frequency up to 2.3 GHz (Fig. 6(d)) in elastically coupled amorphous FeCoB films deposited on PMN-PT (011). A nonvolatile FMR switching of 2.3 GHz back and forth was successfully achieved in a definite E-field range, see Figs. 6(e) and 6(f), and paves a way to nonvolatile RF/ microwave devices.

2.3. FMR tuning in thin films multiferroic heterostructures

In real Si substrate-based integrated RF/microwave devices, piezoelectric thin films may be applied to Si substrate for FMR tuning of magnetic thin film on top. Nevertheless, there is a fundamental challenge that the deposition temperature of conventional piezoelectric materials like PZT, PMN-PT and PZN-PT are very high (> 600 °C) that will ruin the Si substrate. Additionally, bulk piezoelectric substrate (0.2-0.5 mm) requires high voltage for tuning (> 600V), which is too large for integrating electronics system. In short, multiferroic heterostructures with thin piezoelectric films should be considered well in multiferroic devices. Zhou et al. developed a novel Fe3O4/ZnO multiferroic heterostructure46,47 by spin spray low temperature fabrication method microwave ME interactions and magnetic tunabilities of the Fe3O4/ZnO multilayer were demonstrated by electrostatic field-induced IP FMR field changes at room temperature, as shown in Fig. 7(a). Here, a custom-made microwave FMR spectrometer using a planar transmission line48 was used to perform the FMR measurements of the ferrite/ferroelectric ME thin films composites at X-band (9.3 GHz) with high sensitivity (—1Oe). In Fig. 7(a), the bias magnetic field was applied in the Fe3O4/ZnO film plane with IP microwave RF field and was perpendicular to the DC bias field. A clear E-field-in-duced effective magnetic field 14 Oe, correspondingly, was observed between a bias voltage of —20 V and 20 V, which is indicated by the electric field-induced FMR field change, as shown in bottom right inset of Fig. 7(b). Figure 7(c) shows the FMR field dependence of applied voltage from —30 V to 30 V. The FMR field varies linearly as applied voltage switches from —20 V to 20 V, indicating the piezoelectric property of ZnO thin film.

3. Voltage Control of FMR through other Mechanisms-Induced ME Coupling

As we predicted, the piezoelectric thin film layer derived multiferroic heterostructure has limited FMR tunability due to sample clamping effect that the piezoelectric deformation energy was significant consumed in thick substrate like Si and glass. Therefore, in real Si substrate integrated multi-ferroic devices, ME coupling based on other mechanisms beyond strain/stress need to be developed. People have discovered several new ME coupling mechanisms (EM-spin wave coupling, interfacial charge, MTJ, BFO) that can control FMR properties in thin film multiferroic heterostructure without suffering from sample clamping effect. Detailed discussions are listed in each section.

3.1. FMR tuning by EM-spin wave coupling

Das and coworkers have recently demonstrated an YIG/ BSTO thin film multiferroic FM/FE heterostructure for

• III- T * J è A' M ■ Ji A l Lj-^^

Electric He Id (kV/cm) (e)

Repeating "

Fig. 6. (Color online) (a) IP magnetic hysteresis loops of FeCoB/PMN-PT (011). Insets are schematic (upper left) and FMR spectra (bottom right). (b) Schematic of FMR measurement for (c)-(f). The sample is laid face down on an S-shape co-planar waveguide. Magnetic fields are applied in the [100] direction and electric fields are applied along the [011] direction. (c) Electric field dependence of the FMR frequency in field sweeping mode. (d) Electric field dependence of the FMR field in frequency sweeping mode. (e) FMR frequency responses under unipolar (red) and bipolar (blue) sweeping of electric fields at room temperature. (f) Voltage-impulse-induced nonvolatile switching of FMR frequency.43

voltage tunable RF/microwave devices.49 This hetero-structure consisted of a pulsed-laser-deposited (PLD) deposited textured 0.3 ym YIG layer, an oriented 1 ym barium strontium titanate (BSTO) layer, and embedded 50nm platinum (Pt) electrodes between the BSTO and YIG layers on a single-crystal gadolinium gallium garnet (GGG) substrate. By applying voltage of 0-25 V on BSTO layer, the thin film heterostructure showed an electric field tunable FMR response shift by 5 Oe through the coupling between EM wave in BSTO and spin wave in YIG, resulting in a

tunability of 2MHz/V at 9.5 GHz, as shown in Figs. 8(a) and 8(b). In another paper, Das and coworkers also demonstrated a BaM/BSTO heterostructure, which was made of 200 ^m thick IP c-axis oriented single crystalline BaM combined with PLD BSTO films.48 A tunability of FMR frequency of 3.5 MHz/V has been observed at 60 GHz by applying bias voltages in the range of 0-6 V. The fundamental limitation of EM-spin wave coupling tuning of FMR frequency is that the tunability is too small for real applications.

Fig. 7. (a) Piezoelectric coefficient measurements of ZnO thin film. (b) Electric field dependence of the IP field-sweep FMR spectra of the Fe3O4/ZnO ME heterostructure measured at 9.3 GHz. The zero cross part was enlarged to demonstrate a clear ME coupling shift at bottom right inset; (c) X-band IP FMR field of the Fe3O4/ZnO heterostructure measured at varying applied voltages across the ZnO


3.2. FMR tuning by interfacial charge-induced ME coupling

Strong ME coupling has been demonstrated in magnetic/ dielectric or magnetic/ferroelectric thin film heterostructures through a voltage controllable magnetic surface anisotropy mediated by spin polarized charge.51-59 The charge accumulation at ultrathin magnetic/dielectric or ferroelectric interface will change the spin-orbit coupling of magnetic layer51-57 and then influence the surface anisotropy of magnetic layer, resulting in FMR frequency change. Nan et al.58 studied the NiFe (— 1 nm)/PMN-PT bilayer heterostructure where the strain and charge co-mediated ME coupling are expected, which could lead to significantly enhanced ME coupling. It is however challenging to observe the combined strain charge mediated ME coupling, and difficult to quantitatively distinguish these two ME coupling mechanisms. Nan et al.58 demonstrated in this work that, by inserting a thin

Cu layer between NiFe and PMN-PT, the charge effect can be excluded with only strain-mediated ME coupling left. A 202 Oe FMR field shift was shown in only strain-mediated ME coupling and a total 357 Oe FMR field change was demonstrated in strain and charge co-existed NiFe/PMN-PT multiferroic heterostructure. By distinguishing the ME coupling mechanisms, a pure surface charge modification of magnetism shows a strong correlation to polarization of PMN-PT, see Fig. 9. A nonvolatile effective H-field change of 104 Oe was observed at zero electric field originating from different remnant polarization states of PMN-PT. The strain and charge co-mediated ME coupling in ultra-thin magnetic/ ferroelectric heterostructures could lead to power efficient and nonvolatile ME devices with enhanced ME coupling.

After distinguishing the charge mediated ME coupling strength, Zhou et al.59 then investigated the correlation between charge mediated ME coupling strength and thickness of NiFe ultrathin magnetic film in order to maximize the performance of charge-mediated ME devices. Precise quantification of the ME coupling strength in surface charge-induced ME effect was studied in NiFe/SrTiO3 thin film heterostructures with different ultra-thin NiFe thicknesses through voltage-induced FMR measurements, as shown in Fig. 10(a). As demonstrated in Fig.10(b), the voltage-induced FMR field shifts in these NiFe/SrTiO3 thin films hetero-structures showed a maximum value of 65 Oe at an intermediate NiFe layer thickness of 1.2 nm, which was interpreted based on the thin film growth model at the low thicknesses and on the charge screening effect at large thicknesses. Figure 10(c) shows the angular dependence of FMR switching under varied E-field, the isotropic FMR change implies the charge effect-induced out-of-plane surface anisotropy change of magnetic thin films.51-57 By optimizing the magnetic thin film thickness, the ME devices with stronger FMR tunability can be achieved.

3.3. FMR tuning in MTJ

Voltage control of magnetic anisotropy will lead a way to control magnetoresistance (MR) by applying a DC voltage

Fig. 8. Electric field tuning of the FMR response. (a) The FMR absorption derivative versus IP static field H spectra at 9.5 GHz for 0V and 25V applied voltages, as indicated. Right inset shows. The FMR resonance position as a function of the applied voltage. (b) Incremental frequency shift versus applied voltage.48

Fig. 9. (Color online) The change of the effective magnetic field upon the applied electric field induced by pure screening charge effect in NiFe/PMN-PT (black) and P(E) loop of PMN-PT (orange). Insets show the schematics of the positive (up) and negative (down) screen charge on the NiFe interface.58

across the isolating layer like MgO.60'61 As a consequence, a small voltage bias can reduce 1-2 order of current density for spin transfer torque (STT) that switches the magnetization of free layer in MTJ structure, see Fig. 11(a). Nozaki et al. revealed that by the FMR dynamics of ultrathin CoFe magnetic layer can be excited by using a radiofrequency (RF) voltage bias onto isolating layer at room temperature, see Fig. 11(b), and this phenomenon could enable more energy-efficient spintronic devices and related technologies compared to conventional RF magnetic fields or injection of spin-polarized current control of FMR dynamics.60,61 Figures 11(c) and 11(d) show the FMR dynamics in magnetic layer induced by RF voltage bias under different DC magnetic bias. This technique provides a low-power, highly localized and coherent means to manipulate electron spin dynamics.

3.4. FMR tuning in CoFe/BFO system

BFO is a very interesting multiferroic material system that has both ferroelectricity and antiferromagnetism coexistence in each crystal lattice.62-73 Ferroelectric polarization and antiferromagnetic canted moment in BFO system are coupled through Dzyaloshinskii-Moriya (DM) interaction and the antiferromagnetic vector, therefore, can be manipulated by switching the polarization of BFO by E-field. Lots of researches have been devoted to realized nonvolatile control of 180 ° magnetization switching in exchange coupled CoFe/ BFO thin-film heterostructures, in which, the moment of CoFe layer is coupled to the antiferromagnetic canted moment in BFO layer. Heron et al. realized 180 ° magnetization switching in CoFe/BFO multiferroic heterostructure by MR measurements71,72 in previous research. Recently, Zhou et al.13 studied the FMR dependence of CoFe/BFO by using high sensitive ESR system. Figure 12(a) shows the schematic

Fig. 10. (a) Schematic of the sample used for a voltage-induced FMR field change. A schematic of multilayer structure of Cu/NiFe/ STO/Pt/Si. The magnetic field was applied perpendicular to the film plane for FMR measurements. (b) Voltage dependence of the IP field-sweep FMR spectra of the NiFe/STO multiferroic hetero-structure measured at 9.5 GHz. The zero cross part was enlarged to demonstrate a clear ME coupling shift at bottom left inset. (c) Angular dependence of FMR field measurements in NiFe (1.2 nm)/STO (50 nm) under varying voltages: the positive (up) and negative (down) screen charge on the NiFe interface.59

of CoFe/BFO bilayer structure with 0.4 mm diameter CoFe spot on BFO thin layer and the voltage impulses were applied onto BFO layer. Figure 12(b) shows the FMR spectra under varied E-field and a significant nonvolatile FMR shift was

Fig. 11. (Color online) E-field-induced FMR in a magnetic tunnel junction with an ultrathin ferromagnetic layer. (a) Application of a DC voltage can switch the magnetic easy axis between the IP and out-of-plane directions. (b) Application of a RF voltage can excite the FMR dynamics under a static external magnetic field. The yellow arrow represents the RF effective field change originating from the anisotropy control. (c) External-magnetic-field dependence of homodyne detection signals measured under the fixed RF power of 32 Wand elevation angle of 55The external-magnetic-field strength was varied from 0.04 T to 0.3 T. (d) Resonant frequency as a function of the external magnetic field. The results are modeled well (red line) by the modified Kittel formula.61

Magnetic f (b)

Fig. 12. FMR measurements of CoFe/BFO multiferroic heterostructure. (a) Schematic of CoFe (2.5nm)/BFO (200 nm) multiferroic het-erostructure for FMR measurements at varying angles between the magnetic field and the easy axis. (b) FMR spectra of CoFe/BFO multiferroic heterostructure measured at open circuit after applying +5V and —5V. Upper right inset is the relative FMR field dependence on applied voltage. (c) Relative FMR field dependence after applied voltage pulses along different orientations of the magnetic field. (d) Relative FMR field versus applied voltage pulses after 50 and 100 cycles of a 10-V sinusoidal voltage.73

demonstrated. As summarized in Fig. 12(c), the E-field dependence of FMR fields along different magnetic field orientations was demonstrated and that proves a unidirectional magnetic anisotropy change by exchange coupling of CoFe and BFO. The FMR dependence of E-field is similar to a typical polarization-electric field hysteresis loop which indicates the strong correlation between ferroelectric property and FMR properties. At last, Fig. 12(d) gives a robust FMR switching after > 100 round testing. This progress constitutes an important step towards robust repeatable and nonvolatile voltage-induced 180 ° magnetization switching in thin-film multiferroic heterostructures and tunable RF/microwave devices.

4. Conclusion

In summary, we introduce voltage control of FMR in multi-ferroic heterostructures. Firstly, conventional strain/stress ME coupling induced FMR change in different multiferroic het-erostructures, from bulk/bulk magnetic/ferroelectric hetero-structures to thin film/thin film heterostructures, were systematically studied. Nevertheless, sample clamping effect that reduced ME coupling strength limited its real applications. Secondly, to overcome the limitation of strain/stress-induced ME coupling for FMR tuning, other mechanisms like EM-spin wave coupling, interfacial charge and exchange coupling in BFO systems were discovered and investigated. Finally, as a unique characterization method, FMR measurement is a widely used technology to precisely determine the electric field-induced small effective magnetic anisotropy change in multiferroic system with few magnetic moments. The voltage control of FMR in multiferroics provide a path toward next generation small, fast, energy efficient voltage tuning military/civilian RF/microwave devices.


This work is supported by the Natural Science Foundation of China (Grant Nos. 51412199, 11534015), the National 111

Project of China (B14040), the Beijing Institute of Technology Research Fund Program for Young Scholars (Grant No. 3050012261521), W.M. Keck Foundation and National Science Foundation. Dr. Ming Liu was supported by China Recruitment Program for Young Professionals.


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