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Optically Transparent Ferromagnetic Nanogranular Films with Tunable Transmittance

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Developing optically transparent magnets at room temperature is an important challenge. They would bring many innovations to various industries, not only for electronic and magnetic devices but also for optical applications. Here we introduce FeCo-(Al-fluoride) nanogranular films exhibiting ferromagnetic properties with high optical transparency in the visible light region. These films have a nanocomposite structure, in which nanometer-sized FeCo ferromagnetic granules are dispersed in an Al-fluoride crystallized matrix. The optical transmittance of these films is controlled by changing the magnetization. This is a new type of magneto-optical effect and is explained by spin-dependent charge oscillation between ferromagnetic granules due to quantum-mechanical tunneling.


Magnets with transparency to light are very promising for new applications. Various transparent magnetic materials have been proposed (e.g., magnetic semiconductors doped with ferromagnetic elements such as Co1,2,3 and nanocrystalline iron oxides such as magnetite (Fe3O4)4 and hematite (Fe2O3)5,6). However, materials with large magnetization and high optical transparency at room temperature have not yet been realized. In semiconductors, either the magnetization is too small at room temperature to be useful for applications or the magnetic transition temperatures are too low. If iron oxides have strong magnetization, the optical transparency is low (Fe3O4); and if they have high optical transparency, the magnetization is very weak (Fe2O3). On the other hand, magnetorefractive effect in nanogranular films and multilayers with giant magnetoresistance (GMR) has been reported7,8,9,10,11. Magnetorefractive effect is a magneto-optical effect due to GMR.

In this study, we present FeCo-(Al-fluoride) nanogranular films exhibiting ferromagnetic properties with high optical transparency in the visible light region. Optical transmittance is controlled by changing the magnetization. This is a new magneto-optical effect that is explained by the tunneling magneto-dielectric (TMD) effect12,13.

Nanogranular films consisting of nanometer-sized magnetic metal granules and a ceramic insulating matrix exhibit various functional properties depending on the composition ratio of the two elements, granules to matrix14,15. Because dielectric and optical properties are intimately correlated16, there is significant interest in the optical properties of nanogranular films with the TMD effect. In addition, these films have significant practical advantages (e.g., they are easily fabricated and are thermally stable17,18, and have been applied in magnetic sensors19,20).


Optical and magnetic properties of FeCo-(Al-fluoride) nanogranular films

Figure 1a is a photograph of a Fe9Co5Al19F67 film deposited on a glass substrate (Corning Eagle 2000) heated to 660 °C. The film is about 1 μm thick. Red, blue and yellow letters behind the thin film are seen clearly. Figure 1b shows the dependence of the transmittance on the light wavelength in the Fe9Co5Al19F67 film presented in Fig. 1a. This film has substantial optical transmittance even for short wavelengths less than 400 nm, which is the limit that can be measured in this experiment, and exhibits a high transmittance of 90% to light of wavelength 1500 nm, which is in the band for optical communications. The magnetization curve of the Fe9Co5Al19F67 film is presented in Fig. 1c. The film exhibits hysteresis, and the magnetization is 18 kA/m, confirming that the film has both good optical transmittance and ferromagnetic properties.

Figure 1: Optical transmittance and magnetic properties of Fe9Co5Al19F67 film.
Figure 1

(a) Photograph of Fe9Co5Al19F67 film deposited on the 660 °C glass substrate (Corning Eagle 2000). Film thickness is 1 μm. Film is transparent; and the red, blue, and yellow letters behind the film are seen clearly. (b) Transmittance vs. wavelength of Fe9Co5Al19F67 film depicted in Fig. 1a. This measurement is in the wavelength range of ultraviolet (400 nm) to near infrared (2000 nm). Using FTIR, only the film transmittance was measured with reference to the substrate glass at the same time. (c) The magnetization curve of Fe9Co5Al19F67 film presented in Fig. 1a. This magnetization curve has hysteresis with coercivity of 12 kA/m and magnetization of 18 kA/m, indicating that this film is ferromagnetic.

Figure 2a shows a high-resolution transmission electron microscope image obtained from the Fe9Co5Al19F67 film depicted in Fig. 1. This film consists of FeCo magnetic alloy of nanometer-sized granules dispersed in an Al-fluoride matrix. This micrograph has many dark circles with diameters ranging from 10 to 15 nm. In addition, a bright section covers the whole area. The dark circles are FeCo alloy granules, and the bright section with a lattice pattern indicates the Al-fluoride matrix with AlF3 crystal structure.

Figure 2: Nanogranular structure and composition dependence of FeCo-(Al-fluoride) film.
Figure 2

(a) High-resolution transmission electron microscope image obtained from Fe9Co5Al19F67 film. The lattice spacing of AlF3(012) in 0.35 nm. (scale bar, 10 nm) (b) Relationship between the amount of Fe + Co in the films and the magnetization and transmittance of 1 μm thick film. These films were deposited on substrates at 660 °C. As Fe + Co increases, magnetization increases and transmittance decreases.

Fluoride crystals (e.q., MgF2 and BaF2) have good transmittance and are widely used as optical materials. AlF3 crystals also exhibit good transmittance from the short-wavelength region (200 nm) to near-infrared (2000 nm). On the other hand, FeCo is a ferromagnetic alloy with the largest known magnetization21. FeCo alloy granules with diameters exceeding 10 nm exhibit ferromagnetism because the granules are larger than the superparamagnetic critical diameter22 at room temperature. However, since the diameter of the granules is very small compared to the light wavelength, light can pass through the film (to be discussed later). If the density of the FeCo granules in the film increases, transmittance decreases (Fig. 2b). This behavior can be explained simply since the FeCo granules are of the origin of the ferromagnetic properties while the Al-fluoride matrix allows optical transparency.

Figure 3a depicts the change in the transmittance (ΔT/T0) of light with wavelength of a 1500 nm, Fig. 3b presents the magnetization curve of the Fe13Co10Al22F55 film. Transmittance decreases with an increase of magnetic field. The hysteresis of the transmittance is caused by the magnetization, as seen in Fig. 3. Here, ΔT = TMT0, where TM is the transmittance with the magnetization M, and T0 is that with zero magnetization. Table 1 lists ΔT/T0, the magnetization and the transmittance in Fe9Co5Al19F67 (Fe + Co = 14 at.%) and Fe13Co10Al22F55 (Fe + Co = 23 at.%) films. ΔT/T0 is observed in both films. It is noteworthy that optical transmittance changes with the magnetic field (ΔT/T0  = 0.03% and 0.05%). As indicated in Fig. 3a, the magnetic fields at which two of the maxima in the transmittance appear are consistent with the coercivity. This result clearly confirms that the change in the transmittance corresponds to magnetization. The DC resistivity of the films shown in Fig. 3 and Table 1 is larger than 1011 μΩ m and the magnetoresistance was not observed. The result in Fig. 3 and Table 1 demonstrate a new magneto-optical effect in transparent nanogranular films.

Figure 3: Magneto-optical effect of Fe13Co10Al22F55 film.
Figure 3

(a) Change in the transmittance of the light wave length of 1500 nm of Fe13Co10Al22F55 film deposited at 600 °C. The dots denote the experiment results of ΔT/T0. The solid lines denote the theoretical results as a function of magnetic field H, where the magnetization curve in Fig. 3b is used for m = M(H)/M400 and M400 is the magnetization at the maximum measured magnetic field of 400 kA/m. (b) Magnetization curve of Fe13Co10Al22F55 film. Transmittance decreases with increased magnetic field. This result indicates that transmittance is controlled by magnetization.

Table 1: List of optical and magnetic properties.

Mechanism of optical transmission responses in nanogranular films

Optical transmission responses to magnetization in nanogranular films may be explained by the TMD effect. Figure 4 illustrates a nanogranular structure with the image of optical transmittance and a model of a granular pair. The magneto-optical response is due to transition of electric charges between neighboring ferromagnetic granules through an insulating barrier via quantum-mechanical electron tunneling23,24, which depends strongly on the relative orientation of magnetization of the granules. When optical light is incident on the film, electric charge carriers in granules are subject to the oscillating electric field of the light that causes tunneling of the charge carriers back and forth between neighboring granules through the thin insulator barrier (Fig. 4). The oscillation of charging states between granules is spin-dependent and contributes to additional magneto-dielectric and optical responses of nanogranular films24.

Figure 4: Image of optical transmission and magneto-optical response of a nanogranular film.
Figure 4

Schematic of a nanogranular film with nanometer-sized granules dispersed in an insulator matrix. The right side of Fig. 4 depicts a schematic profile of two granules. In an AC electric field, the oscillating transition of an electric charge carrier occurs due to the quantum-mechanical tunneling. Tunneling depends on the relative orientation of the magnetization of the granules. This spin-dependent charge oscillation induces the magneto-optical response of the nanogranular films.

Incorporating the TMD constant12 with a broad distribution of dielectric relaxation around the characteristic relaxation time24,25 , where PT is the tunneling spin polarization, m = (M/Ms) is the normalized magnetization and Ms is the saturation magnetization, we have the total magneto-dielectric constant of granular films

where εr(ω) is the effective dielectric constant of the media in the absence of tunneling effect between granules, Δεm(ω) is the tunneling contribution12, Δε is the dielectric strength, and β is the Cole-Cole’s exponent (0 < β ≤ 1) representing a measure of the distribution of relaxation time26. In magnetic nanogranular films, β = 0.7 to 0.8 was found in a previous study12.

Using the dielectric constant (1) in the formula of transmission for a normal-incident optical light through a film27, we obtain the magneto-optical transmittance of a granular film as , where Δα0 is the magneto-optical absorption coefficient and d is the film thickness (see Methods for details). In Fig. 3a, we fit the magnetic field dependence of ΔT/T0 using the experiment data of the magnetization curve in Fig. 3b for the optical light of wave-length λ = 1500 nm and frequency ω = 108 s−1, refractive index nr = 3, and film thickness d = 1000 nm. Using the values of PT = 0.5, β = 0.7 (PT and β values are a little different from the previous results12. This is because of the increase of the granule size and the granule size distribution as seen in Fig. 2), Δε = 300 and τ0 = 10−8 s, appropriate for the Fe+Co of 23 at.% granular film12 and Δα0d = (2πd/nrλ)(ωτ0)−βΔεsin(βπ/2) = 2.3×10−3 we find a good agreement between the experiment and theoretical data (Fig. 3a), in particular for the hysteretic behavior of the transmittance reflecting the magnetization process in Fig. 3b. The magnetic fields, at which the transmittance is greatest, coincide with the coercive fields where there is a change of sign in the magnetization curves.

The values of ΔT/T0 can be enhanced if one uses a half-metal with full spin polarization (PF = 1) for ferromagnetic nanogranules; makes the granule density higher, which shortens relaxation time due to the reduced distance between granules; and designs broader size distribution, which makes β smaller. Nanogranular structures can be controlled by changing the film composition, the deposition conditions, and the annealing. For instance, when the values of PF = 1 and τ0 = 10−9 s are used, large magneto-optical transmittances of ΔT/T0 (~5% for β = 0.6 and ~10% for β = 0.5 are expected in half-metallic nanogranular films.


We have reported that nanogranular FeCo-(Al-fluoride) films are optically transparent ferromagnetic materials. These films have transmittance even for short wavelengths of light (less than 400 nm), exhibit 90% transmittance at a wavelength of 1500 nm, and are ferromagnetic with magnetization exceeding 18 kA/m at room temperature. Furthermore, these films have magneto-transmittance response ΔT/T0 of 0.05% at a wavelength of 1500 nm. This new magneto-optical phenomenon is explained by the TMD effect due to the spin-dependent quantum effect in the nanogranular structure. A large value of ΔT/T0 (more than 10%) is expected theoretically in nanogranular films by optimizing material and structural conditions.

Magnetic materials in electric devices are not optically transparent. With the realization of a transparent magnet, more complete display devices will be constructed. For example, speed and fuel meters and a map can be displayed directly on the front glass of a car or an airplane.


Preparation of thin film samples

Thin films were prepared by a tandem deposition method28 using a conventional RF-sputtering apparatus. Sputter deposition was performed on a 50 × 50 mm glass (Corning Eagle 2000) substrate at 600 to 700 °C in argon atmosphere with 1.3 Pa pressure during deposition, using a 76 mm-diameter Fe60Co40 alloy disk target and an AlF3 powder target compacted in the form of a 76 mm-diameter disk.

Composition and structural analysis

The composition ratio of Fe-Co (granule) and Al-F (matrix) was controlled by changing the RF power applied to each target. The chemical composition of Fe, Co, Al, and F in the thin films was analyzed using wavelength dispersion spectroscopy (WDS). For structural analysis, transmission electron microscopy (TEM) was performed on several selected thin films.

Measurements of optical and magnetic properties

Optical transmittance was measured using Fourier transform infrared spectroscopy (FTIR) with a measurement waveband of 400 to 2000 nm. Change in the transmittance was measured using an optical spectrometer with a measurement waveband of 900 to 2000 nm and a magnetic field of 0 to 480 kA/m. The magnetization curves were measured using a vibrating sample magnetometer (VSM). In the magnetization and magneto-optical measurements, a magnetic field was applied parallel to the films surface. All the measurements reported in this paper were carried out at room temperature.

Derivation of the transmittance

The transmittance of the electromagnetic wave incident normal to the plane of a film with the effective dielectric constant ε (ω) and thickness d is obtained by calculating the Poynting vectors of the incident, reflected, and transmitted electromagnetic waves. The resulting transmittance TM is expressed as27

where Ei is the incident electric field, Et is the transmitted electric field, is the complex wave number,  = n +  is the complex refractive index, α = 4πκd/λ is the absorption coefficient, θ = 2πnd/λ, φ = −tan−1[2κ/(n2 + κ2−1)], λ is the wave length, and R0 = [(n−1)2 + κ2]/[(n + 1)2 + κ2].

The interference is weak (Fig. 1b), due to modulation of film thickness and/or refractive index, which allows us to average TM over (θφ) from 0 to 2π, yielding25

The effective dielectric constant of granular films may be separated into the two contributions

where εr(ω) is the effective dielectric constant in the absence of the tunneling effect between granules and Δεm(ω) is the tunneling contribution of the form12,

where Δε is dielectric strength; τm is the characteristic relaxation time given by the spin-dependent tunneling rate24,25 where PT is the tunneling spin polarization, M is the magnetization and Ms is the saturation magnetization; and β is an exponent representing a measure of the distribution of relaxation time26 (β ~ 0.7 to 0.8 in the granular films12). In the optical region, the light frequency (~1015 s−1) is much higher than the tunneling rate (~104 s−1 to 109 s−1) depending on the ferromagnetic composition12 (ωτm1) so that the tunneling contribution is approximated as Δεm(ω) ≈ Δεeiβπ/2(ωτm)β.

In the optical region (ωτm1), the refractive index can be expanded with respect to the tunneling contribution Δεm(ω) as


The real and imaginary parts of the complex refractive index are written as


in the highly transparent region (kr/nr)21.

It follows from Eqs (3), (9) and (10) that the dominant contribution to the magneto-optical effect arises from the magneto-optical part Δαm of the absorption coefficient α = αr + Δαm, where αr = 4πκr/λ and Δαm = 4πΔκm/λ, yielding the transmittance

as a function of applied magnetic field H through the magnetization curve M(H). Therefore, the magneto-transmittance effect of a granular film is obtained as

where Δα0 = (2π/nrλ)(ωτ)−βΔεsin(βπ/2) and m = M(H)/Ms. Equation (12) is used to analyze the experimental results of the magneto-optical transmittance ratio ΔT/T0 versus applied magnetic field H in the Fe13Co10Al22F55 (Fe+Co = 23 at.%) film, as illustrated in Fig. 4.

Additional Information

How to cite this article: Kobayashi, N. et al. Optically Transparent Ferromagnetic Nanogranular Films with Tunable Transmittance. Sci. Rep. 6, 34227; doi: 10.1038/srep34227 (2016).


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The authors are grateful to T. Masumoto and K. I. Arai for valuable discussions. They are indebted to K. Ishida for the sample preparation and to T. Iwasa for the measurement of optical transmittance. This work was supported by Engineering and Grant-in-Aids for Scientific Research (Grant No. 26289253) from the JSPS and Nippon Sheet Glass Foundation for Materials Science.

Author information


  1. Research Institute for Electromagnetic Materials, 2-1-1, Yagiyama-minami, Taikaku-ku, Sendai 982-0807, Japan

    • Nobukiyo Kobayashi
  2. Frontier Research Institute for Interdisciplinary Sciences, Tohoku University, 6-3, Aramaki aza Aoba, Aoba-ku, Sendai 980-8578, Japan

    • Hiroshi Masumoto
  3. Institute for Materials Research, Tohoku University, 2-1-1 Katahira, Aoba-ku, Sendai 980-8577, Japan

    • Saburo Takahashi
  4. Advanced Science Research Center, Japan Atomic Energy Agency, 2-4, Shirakata Shirane, Tokai-mura, Naka-gun, Ibaraki-ken 319-1195, Japan

    • Sadamichi Maekawa


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The experiments were carried out by N.K. The data was discussed by N.K. and H.M. The theoretical model was developed by S.T. and S.M. All authors contributed to the writing and editing of the paper.

Competing interests

The authors declare no competing financial interests.

Corresponding author

Correspondence to Nobukiyo Kobayashi.


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