Influence of Sputtered ZnO and Al:ZnO Top Layers on Magneto-Optic Responses of Yttrium Iron Garnet Films

Abstract

Zinc oxide (ZnO) is a promising material for combining with magneto-optic (MO) materials because it can propagate stable exciton-polaritons, with velocities considerably lower than that of photons in a vacuum. This study investigated the influence of sputtered ZnO and Al:ZnO top layers on MO responses of a bismuth-substituted yttrium iron garnet (Bi:YIG) film. The ZnO top layer modulated the Faraday rotation and magnetic circular dichroism (MCD) of the Bi:YIG around the exciton resonance wavelength of ZnO at 369 nm. Furthermore, Al-substituted ZnO, which is a conductive ZnO, also changed the MO effects around the exciton resonance wavelength. These results imply that the exciton-polaritons in ZnO affect the MO interaction, because of their considerably low group velocity. The results suggest potential for controlling the MO response via excitons.

1. Introduction

The magneto-optic (MO) effect is widely used in optical applications. Recently, enhancement or modulation of the MO effect was reported in hybrid structures of MO materials with metallic [1,2,3] and dielectric materials [4,5,6]. These kinds of structures attract a great deal of interest because they possess advanced functional capabilities for optical devices. One method of changing MO responses is to localize the light in or around MO materials. Localization of light extends the time for interaction between light and MO media and, consequently, MO responses can be modulated. In earlier studies [1,2,3,4,5,6], plasmon resonance and photonic crystals were used to localize the light.

Exciton-polaritons are another promising phenomenon that localizes or slows light. An exciton is an optically excited quasiparticle formed by the electrostatic Coulomb interaction between an electron and a hole. When the semiconductor absorbs a photon, an electron can be excited into the conduction band and a hole is left behind in the valence band. This electron–hole pair is known as an exciton. Electromagnetic dipolar oscillations of excitons and photons are strongly coupled at the exciton resonance wavelength, which is called an exciton-polariton. Figure 1 shows a schematic view of an exciton-polariton. The interaction of a photon with the exciton can be expressed by Maxwell equations. The dispersion relation of the exciton-polariton is given by [7]

$${\omega }^2=\frac{1}{2{\epsilon }_{\infty }}\left\{c^2{k}^2+{\epsilon }_{\infty }{\omega }_L^2\pm \sqrt{{\left(c^2{k}^2+{\epsilon }_{\infty }{\omega }_L^2\right)}^2-4{\epsilon }_{\infty }{c}^2{k}^2{\omega }_T^2}\right\},$$

(1)

where c is the velocity of a photon in a vacuum, k is the wavenumber, and ω_T and ω_L are longitudinal and transverse exciton frequencies. The difference between ω_T and ω_L is called longitudinal–transverse (LT) splitting, which reflects the exciton bonding energy. A dispersion relationship of the exciton-polariton approaching ω_T when k → ∞ means the group velocity v = ω/k of exciton-polaritons is considerably slow at a wavelength of ω_T. It potentially enlarges the interaction time and, thus, the MO responses.

Figure 1. Schematic of an exciton-polariton.

The zinc oxide (ZnO) wide-band material is an attractive material for employing exciton-polaritons. ZnO propagates relatively stable exciton-polaritons at room temperature because its exciton bonding energy of 60 meV is sufficiently stronger than heat energy at a room temperature of 26 meV [8]. One study found the experimentally measured group velocity of exciton-polaritons in ZnO to be 6 × 10⁶ m/s, which is 1/50 of light speed in a vacuum [9]. In a previous study, we deposited ZnO on bismuth-substituted yttrium iron garnet (Bi:YIG) using an electroless plating method. The electroless-plated ZnO slightly changed the MO responses [10].

In this study, ZnO and Al-substituted ZnO (Al:ZnO) were sputtered onto bismuth-substituted yttrium iron garnet (Bi:YIG). Magnetic circular dichroism (MCD) and Faraday rotation of the bilayers were compared with single-layered Bi:YIG.

2. Materials and Methods

We employed the radio-frequency magnetron sputtering method to fabricate the bilayer of Bi:YIG and ZnO. Figure 2 shows a schematic of the cross-section of the fabricated bilayers. Firstly, a precursor of Bi:YIG films was deposited on an alkali-free glass substrate (Eagle XG, Corning Inc., Corning, NY, USA) by sputtering for two hours. The films were then sintered at 680 °C for 20 min. The composition and thickness of the Bi:YIG film were Bi_0.5Y_2.5Fe₅O₁₂ and 200 nm, respectively. Then, 200-nm-thick ZnO films were deposited onto the fabricated Bi:YIG films by sputtering. Figure 3 shows the X-ray diffraction spectra of the fabricated ZnO films at various annealing temperatures. All films had good crystallinity; therefore, ZnO films without post-annealing were used so as to avoid a change in the characteristics of the Bi:YIG by heat-diffusion of Zn. The single-layered ZnO films were formed on the glass substrate, allowing the evaluation of crystallinity and optical absorption. As with ZnO, Al:ZnO films were also fabricated and magneto-optically evaluated.

Figure 2. Representation of a cross-section of a fabricated ZnO/bismuth-substituted yttrium iron garnet (Bi:YIG) bilayer.

Figure 3. X-ray diffraction (XRD) spectra of ZnO films at various annealing temperatures.

3. Results and Discussion

3.1. Bi:YIG Film with a ZnO Top Layer

Figure 4 shows a comparison of magnetization curves of single-layered Bi:YIG and Bi:YIG with ZnO. The circular point with a black line represents the single layer, and the cross point with a red line shows the measurement results of the fabricated bilayer. The magnetization characteristics of Bi:YIG were not changed upon formation of the ZnO top layer. This result means Zn was not significantly diffused to Bi:YIG via deposition of the ZnO. Figure 5 shows the absorption spectrum of the fabricated ZnO. The exciton absorption peak occurred at 365 nm, which is slightly shooter than 369 nm (exciton resonance wavelength of ZnO). This could be because of a lattice distortion due to impurities or a lattice defect.

Figure 4. Comparison of the magnetization curve of single-layered Bi:YIG and Bi:YIG with ZnO.

Figure 5. Absorption spectrum of the fabricated ZnO film.

Figure 6 shows a comparison between the Faraday rotation spectra of Bi:YIG with ZnO and the single Bi:YIG film. The single Bi:YIG film showed a typical spectrum of magnetic garnet. In contrast. the Faraday rotation spectra of Bi:YIG with the ZnO top layer changed considerably around 369 nm. This wavelength is the exciton resonance energy of ZnO of 3.36 eV. Small peaks occurred on both sides of 369 nm. As the MO effect represents a phase shift of the circular polarized light, these two peaks could be due to the influence of the exciton for the left and right circular lights being different.

Figure 6. Faraday rotation spectra of Bi:YIG and ZnO/Bi:YIG.

Figure 7 is a comparison of the magnetic circular dichroism (MCD) spectra. As with the Faraday rotation, the MCD spectra of Bi:YIG was modulated around 369 nm upon depositing the ZnO top layer. According to Equation (1), a gradient of the dispersion relation of the exciton-polariton, which is equal to group velocity, approaches zero when the wavelength is close to exciton resonance. Therefore, these changes in MO response could be caused by the formation of the exciton-polariton and its slow group velocity. Furthermore, this change in MO can potentially be controlled by voltage because the exciton resonance in semiconductor systems can be altered via an electro-optic effect [11,12,13,14]. The modulation of the Faraday rotation and MCD was about 20 times bigger than that of a previous electroless-plated ZnO study [10]. This change could be due to the fabrication method being changed to a sputtering method, consequently increasing the density of the ZnO film.

Figure 7. Magnetic circular dichroism (MCD) spectra of Bi:YIG and ZnO/Bi:YIG.

3.2. Bi:YIG Film with an Al-Substituted ZnO Top Layer

Al:ZnO, which is transparent conductive ZnO [15], was evaluated for its ability to electrically control the exciton. Al:ZnO was deposited and its conductivity was measured at various post-annealing temperatures. Figure 8 shows the sheet resistances of the fabricated Al:ZnO. Al:ZnO showed conductivity at 300 °C or lower annealing temperature. Figure 9 shows the annealing temperature dependence of the absorption spectra of Al:ZnO. Conductive Al:ZnO does not show an absorption peak around 369 nm; however, the insulating Al:ZnO showed this absorption peak. The absorption peak or the optical band edge shifted to longer wavelengths as the annealing temperature increased. When the ZnO film is doped with Al, the Fermi level would move into the conduction band and lead to the energy band gap widening, this effect is known as Moss–Burstein effect. The width of the optical band gap decreased as the annealing temperature increased, especially over 400 °C [16]. As a result of this effect, as-deposited Al:ZnO showed conductivity and an optical absorption edge at short wavelengths. According to the Reference [16], this absorption edge also shifted to longer wavelengths with higher annealing temperature, similar to the present results with Al:ZnO.

Figure 8. Sheet resistance dependence on annealing temperature of the fabricated Al:ZnO.

Figure 9. Absorbance spectra of the fabricated Al:ZnO at various annealing temperatures.

Figure 10 and Figure 11 show the Faraday rotation spectra and MCD spectra, respectively, of the Al:ZnO/Bi:YIG bilayers. Surprisingly, the bilayers showed a change in MO response around 369 nm at all annealing temperatures, although the measured absorption peak differed, and the sheet resistance changed from conductive to insulating. These results imply that pure ZnO, which modulates the MO effects, was included in Al:ZnO. The spectrum at 700 °C was not consistent with other spectra. The crystalline temperature of Bi:YIG is 680 °C. Therefore, crystallinity and MO responses of Bi:YIG changed at this temperature, resulting in the spectrum being different at 700 °C.

Figure 10. Faraday rotation spectra of Al:ZnO/Bi:YIG bilayer at various annealing temperatures.

Figure 11. MCD spectra of Al:ZnO/Bi:YIG bilayer at various annealing temperatures.

The MO responses of Bi:YIG changed upon introducing the conductive transparent Al:ZnO. This result presents the possibility of applying an electric field to Al:ZnO/Bi:YIG and electrically controlling the MO response via excitons. Figure 12 shows the voltage-induced modulation of MCD of the Al:ZnO/Bi:YIG. The sample structure was a glass substrate with indium tin oxide (100 nm), along with Bi:YIG (170 nm) and the as-deposited Al:ZnO (200 nm). The voltage was applied from Al:ZnO to indium tin oxide. The MCD changed slightly when 1.5 V was applied, and this result was reproduced three times.

Figure 12. Voltage-induced modulation of the MCD. The sample structure was a glass substrate with indium tin oxide (100 nm), along with Bi:YIG (170 nm) and Al:ZnO (200 nm). The voltage was applied from Al:ZnO to indium tin oxide.

4. Conclusions

We investigated the influence of sputtered ZnO and Al:ZnO top layers on the MO response of a Bi:YIG film. The ZnO top layer modulated the Faraday rotation and MCD of Bi:YIG around the exciton resonance wavelength of ZnO at 369 nm. This result implies that exciton-polaritons were excited in ZnO, and its considerably low group velocity modulated the time for interaction between photons and Bi:YIG. This change in MO effects can potentially be controlled by voltage because the exciton resonance in semiconductors can be altered via an electro-optic effect. Al-substituted ZnO, which is conductive ZnO, was also evaluated for its ability to electrically control the exciton. Al-substituted ZnO showed conductivity and modulation of MO response. This result offers the potential to electrically control MO response via excitons.