A major issue in the development of spintronic memory devices is the reduction of the power consumption for the magnetization reversal. For this purpose, the artificial control of the magnetic anisotropy of ferromagnetic materials is of great importance. Here, we demonstrate the control of the carrier-energy dependence of the magnetic anisotropy of the density of states (DOS) using the quantum size effect in a single-crystal ferromagnetic material, GaMnAs. We show that the mainly twofold symmetry of the magnetic anisotropy of DOS, which is attributed to the impurity band, is changed to a fourfold symmetry by enhancing the quantum size effect in the valence band of the GaMnAs quantum wells. By combination with the gate electric-field control technique, our concept of the usage of the quantum size effect for the control of the magnetism will pave the way for the ultra-low-power manipulation of magnetization in future spintronic devices.
The control of the magnetic anisotropy1,2,3,4,5,6,7 is a particularly crucial issue for the reduction of the power required for the magnetization reversal that will enable the exploitation of the full potential of the spintronic memory and logic devices, such as magnetic tunnel junctions8,9,10,11,12 and spin transistors13,14, that may outperform the CMOS circuits commonly used in existing computers. Meanwhile, band engineering is a useful technique to manipulate the electronic structures of materials and heterostructures using an electric field15, the quantum size effect16,17 and modulation doping18,19, and it is a well-established and important technology for the design of electronic devices based on semiconductors. For example, by designing quantum well structures, we can completely control the quantized energy levels or two-dimensional sub-band structures of materials as calculated using band engineering. Although band engineering was developed mainly for semiconductor electronics, it could potentially be extended to magnetism because electron spins and their motions are coupled by spin–orbit interactions. However, this point of view of the usage of band engineering is lacking1,2,3,4,5,6,7,20,21,22,23,24,25, and there are a wide variety of possibilities for band engineering to design or control magnetic materials and devices.
Here, we demonstrate the artificial control of the carrier energy dependence of the magnetic anisotropy of the density of states (DOS) for the first time by designing quantum well structures consisting of a single-crystal ferromagnetic thin film and semiconductor barriers and tuning the strength of the quantum size effect. We use the prototypical ferromagnetic semiconductor GaMnAs that has a band structure in which the energy regions of the valence band (VB) and impurity band (IB) overlap26. We find that the magnetic anisotropy of the DOS varies depending on the energy of the carriers. This phenomenon has never been reported in any ferromagnetic materials. Furthermore, we reveal that the relative strength of the magnetic anisotropy between the VB and IB, which have fourfold and twofold symmetries in the film plane, respectively, can be varied by controlling the strength of the quantum size effect induced in the VB (Fig. 1). These new findings suggest that band engineering provides the possibility of artificially designing magnetic anisotropy by controlling the electronic structures of magnetic materials. By combining this technique with the recently developed gate electric-field control technique of the carrier density and magnetization, our results will lead to ultra-low-power manipulation of magnetization in future spintronic devices.
We use a tunnel heterostructure consisting of Ga0.94Mn0.06As (25 nm, Curie temperature TC: 134 K)/AlAs (5 nm)/GaAs:Be (100 nm, hole concentration p=7 × 1018 cm−3) grown on a p+-GaAs (001) substrate by molecular beam epitaxy (MBE) (see Fig. 2a). We carefully etch a part of the GaMnAs layer from the surface and fabricate three tunnel diode devices with a diameter of 200 μm on the same wafer27,28 with different GaMnAs thicknesses, d: 22 nm (device A), 16 nm (device B) and 9 nm (device C). In the GaMnAs layer, holes are confined by the AlAs barrier and the thin depletion layer (∼1 nm) formed at the surface of the GaMnAs layer27,28, and thus the VB energy levels in the GaMnAs layer are quantized. As shown in Fig. 2b, we measure the current–voltage (I–V) characteristics at 3.5 K with a strong magnetic field μ0|H|=890 mT applied at an angle from the  direction in the plane so that the magnetization M becomes parallel to H, where μ0 is the vacuum permeability (see Supplementary Note 1 and Supplementary Fig. 1 for the relation between the directions of H and M). We ground the backside of the substrate and apply a bias voltage V to the Au top electrode. In this manner, we measure the magnetization direction dependence of the tunnel conductance at various values of V29,30,31,32. For these measurements, we vary V and at intervals of 2 mV and 5°, respectively. As shown in Fig. 2c, when a negative V is applied, holes tunnel from the GaAs:Be layer to the GaMnAs layer. Because dI/dV is proportional to the DOS at the energy where tunnelling occurs, the energy dependence of the DOS below the Fermi level EF of the GaMnAs layer is detected in negative V. When V is positive, holes tunnel from the GaMnAs layer to the GaAs:Be layer, and thus dI/dV is proportional to the DOS at EF of GaMnAs regardless of V (see Fig. 2d). Our measurements provide the dependence of the DOS at various energies below EF in GaMnAs.
The dI/dV-V characteristics obtained for devices A–C at =0° show different oscillatory behaviour (see Fig. 3a); the oscillation becomes stronger as d decreases. Also, the V values of the dI/dV peaks systematically change by changing d, indicating that these oscillations originate from the resonant tunnelling effect33,34 induced by the quantum size effect in the VB of the GaMnAs layer27,35,36,37,38. (See Supplementary Fig. 3 for the I–V characteristics of devices A–C. More systematic data of the d2I/dV2-V characteristics of tunnelling devices with various GaMnAs thicknesses (d=7.3–23.6 nm) are described in Supplementary Note 3 and Supplementary Fig. 4.) The oscillation amplitude of dI/dV decreases by changing from 0° (along ) to 45° (along ) or 135° (along ) (see Fig. 3b). The peak (blue arrow) value of dI/dV when =0° is larger than that when =45° or 135°, whereas the dip (green arrow) value of dI/dV when =0° is smaller than that when =45° or 135°. This feature can be seen in Fig. 3c as the opposite sign of the oscillation of dI/dV as a function of between when V=−0.13 V (the peak of dI/dV-V in Fig. 3b) and when V=−0.166 V (the dip of dI/dV-V in Fig. 3b). In Fig. 3c, the symmetry of the dependence of dI/dV changes depending on V. Here, we normalize dI/dV using
where is the dI/dV value averaged over at a fixed V. As seen in Fig. 4a,d,g, primarily twofold symmetry along  is observed at negative V when d=22 nm, but fourfold symmetry along emerges as d decreases. At the peaks and dips of the dI/dV-V curves indicated by the blue and green arrows in Fig. 4b,e,h, the symmetry of the dI/dV- curves shown in Fig. 4c,f,i is changed from twofold to fourfold as the resonant tunnelling is enhanced by decreasing d. Because resonant tunnelling is induced in the VB, the enhanced fourfold symmetry is attributed to the VB. The curves in Fig. 4i are those obtained by normalizing the dI/dV- curves shown in Fig. 3c (blue and green).
We derive the symmetry components C4 (fourfold along ), (twofold along ) and (twofold along ) of the normalized dI/dV- curves by fitting the following equation to the experimental normalized dI/dV- curves:
The V dependences of C4, and show oscillations that synchronize with the oscillations of the dI/dV-V curves that are induced by the resonant tunnelling (see Fig. 5). C4 is significantly enhanced as d is decreased and the oscillation of dI/dV-V is enhanced. Therefore, the oscillatory behaviour of the V dependence of the symmetry components is attributed to the quantization of the VB states.
We discuss the origin of the fourfold symmetry of the dI/dV- curves induced by the quantum size effect in the VB of GaMnAs. Our results mean that the strength of the quantization depends on as shown in Fig. 3b; in other words, the coherence length of the VB holes depends on . In GaMnAs, there is a weak interaction between the VB holes and Mn spin magnetic moments, indicating that the coherence length of the VB holes depends on the strength of this interaction. Thus, the fourfold symmetry of the magnetic anisotropy originates from the anisotropy of the wave function of the VB holes that are mainly composed of As 4p orbitals located at the lattice points having a fourfold symmetry in the film plane. This shows that the interaction between the spins and orbitals reflects the anisotropy of the wave function distribution and the direction of spins. We calculated the DOS of the VB that is weakly interacting with the magnetic moments of Mn, using the k·p Hamiltonian and p-d exchange Hamiltonian, and confirmed that the DOS versus characteristic shows the fourfold symmetry (see Supplementary Note 4 and Supplementary Fig. 5).
Magnetic anisotropy of the IB
In the region of V=−0.07 V–+0.1 V of the colour-coded maps shown in Fig. 4a,d,g, the normalized dI/dV as a function of and V is similar in devices A–C, meaning that it is insensitive to the change in d, and thus the twofold symmetry along  observed in this region is attributed to the IB. This insensitivity to d agrees with the previous report39 that the magnetic anisotropy of magnetization in GaMnAs films at low temperature is independent of d. In the region of V>0 V, the dependence of the normalized dI/dV does not depend on V because it always reflects the DOS at EF in GaMnAs regardless of V. The twofold symmetry along  is also observed in the region of V<−0.07 V for device A (d=22 nm, Fig. 4a), in which the effect of the quantization of the VB holes is small. This indicates that the dependence of the tunnelling transport is dominated by the IB holes in the entire region of V when the quantization of the VB holes is weak. However, as the quantization becomes stronger, the fourfold symmetry originating from the VB emerges in the IB region, meaning that the IB and VB overlap (Fig. 4b,e,h). This finding is consistent with recent angle-resolved photoemission spectroscopy measurements of GaMnAs26.
As shown in Fig. 4b, we can classify the region of V<0 V (corresponding to the DOS below EF in GaMnAs) into three parts, from top to bottom: 0 V–−0.03 V (region X), −0.03 V–−0.27 V (region Y) and −0.27 V–−0.3 V (region Z). In regions X and Z, the DOS when M is along  and  is larger than when M is along  and , whereas it is smaller in region Y. We discuss the origin of this sign change of the dependence of the DOS of the IB depending on the energy. A single Mn atom doped into GaAs forms an impurity state because of the inter-atomic interaction (hybridization) between the Mn 3d orbitals and the As 4p orbitals. Tang and Flatté40 predicted that the hybridization and spin–orbit interaction in the As 4p orbitals result in an antiparallel condition between the spin angular momentum of the Mn 3d spins and the orbital angular momentum of the hole in the impurity state. Because of this condition, the wave function of the hole in the impurity state favours extension in the direction perpendicular to the Mn 3d spins, and thus the distribution of the wave function depends on the direction of the Mn 3d spins. This behaviour is well reproduced by a tight binding method (see Supplementary Note 5 and Supplementary Fig. 6). Figure 6a,b schematically illustrates the distributions of the wave functions of the two impurity states α and β originating from the two neighbouring Mn atoms A and B located along , respectively. Here, we consider the cases in which M is aligned in the  direction (Fig. 6a) and in the  direction (Fig. 6b), in which the wave functions tend to extend in the  and  directions, respectively (the calculated results are shown in Supplementary Fig. 6). As shown in Fig. 6c,d, the hybridization between the Mn 3d (red lines) and As 4p (blue lines) orbitals forms α (yellow line) and β (purple line) around Mn atoms A and B, respectively. The bonding (green line) and antibonding (orange line) impurity states are formed by the wavefunction overlap between α and β, the origin of the IB41,42. As indicated in Fig. 6a,b, the wavefunction overlap between α and β is larger when M|| than that when M||. Thus, the energy separation Δ between the bonding and antibonding states when M|| is larger (Fig. 6c) than that when M|| (Fig. 6d). The energy regions X–Z indicated in Fig. 6c,d correspond to the regions of V shown in Fig. 4b. When M||, the antibonding and bonding states are formed in regions X and Z, respectively (Fig. 6c). When M||, both antibonding and bonding states are formed in region Y (Fig. 6d). Thus, the energy dependence of the DOS of the IB differs depending on the M direction (that is,  or ), as shown in Fig. 6e. In regions X and Z, the DOS when M|| is larger than that when M||. In region Y, the DOS when M|| is larger than that when M||. The same scenario can be applied for the Mn atoms whose distance is larger than that between the nearest Mn atoms. The twofold symmetry along the  axis in the DOS versus characteristic is well reproduced by a tight-binding calculation (see Supplementary Note 5 and Supplementary Fig. 7).
Above, we considered only the case in which the Mn atoms are located along . Although there are several possible Mn alignments in real GaMnAs, there are reasons that only the interaction between the Mn atoms located along  is important. The overlap between the wave functions of the impurity states originating from the two Mn atoms located along is known to be larger than that from the Mn atoms along other directions, such as and 41,42. Furthermore, an anisotropic distribution of Mn atoms along  in GaMnAs is predicted43. Slightly more Mn atoms are located along  than along , and this is attributed to the direction of the Mn-As bonds on the surface during the MBE growth. This is thought to be the origin of the twofold symmetry along  of the dI/dV- curves. Also, the anisotropic interaction between two Mn atoms and the anisotropic distribution of the Mn atoms are thought to be the reason that GaMnAs has magnetic anisotropy with the in-plane twofold symmetry along .
is also slightly enhanced at the peaks and dips of the resonant oscillation in dI/dV-V as d decreases (see Fig. 5), indicating that the VB has a small twofold symmetry along . The twofold symmetry of the VB is induced because the interaction between the VB holes and Mn spin magnetic moments transmits the anisotropy of the Mn distribution to the VB.
To verify that the fourfold symmetry of the magnetic anisotropy of DOS is induced by the quantization in the GaMnAs quantum well (QW), we compare devices A–C with device Z that consists of GaMnAs (25 nm, TC 116 K)/AlAs (6 nm)/GaAs:Be QW (15 nm)/AlAs (6 nm)/GaAs:Be (100 nm) grown on a p+-GaAs (001) substrate (see Fig. 7a,b), in which the ferromagnetic layer and the QW layer are separated and the quantum size effect does not occur in the ferromagnetic layer. The surface GaMnAs layer is thick enough to prevent the quantum size effect in this layer. We perform the same measurement on device Z. The obtained dI/dV-V characteristics oscillate because of the quantum size effect in the nonmagnetic GaAs:Be QW (see Fig. 7c). The V dependence of the normalized dI/dV- curves shown in Fig. 7e reflects the energy dependence of the magnetic anisotropy of the DOS of the GaMnAs electrode and exhibits an oscillatory behaviour that is attributed to the oscillation of the dI/dV-V curves induced by the resonant tunnelling effect in the GaAs:Be QW (see Fig. 7f). Similar to devices A–C, C4, and oscillate as a function of V, synchronizing with the oscillation of dI/dV-V (Fig. 7c,d); however, the symmetry of the dependence of the normalized dI/dV is mainly twofold, reflecting the magnetic anisotropy of the GaMnAs top electrode (see Fig. 7d,e,g), that offers a remarkable contrast to the results of devices A–C that the quantum size effect in the GaMnAs QW layer enhances C4 (fourfold symmetry). This contrast provides evidence that the magnetic anisotropy of the DOS changes by enhancing the quantum size effect in the GaMnAs QW in devices A–C. Between the different V values indicated by the green and blue arrows in Fig. 7f, the symmetry of the dI/dV- curves shows an opposite sign (Fig. 7g) that is induced by the small shift of the peak V of the dI/dV-V curves (see Supplementary Note 2 and Supplementary Fig. 2 for details).
It should be noted that surface states, if any, may have different anisotropy from the bulk or quantum well states. However, the surface of GaMnAs is depleted and does not induce the carrier-mediated ferromagnetism. This means that the surface does not couple with the magnetization of the GaMnAs layer beneath the surface. Thus, the DOS of the nonmagnetic surface does not depend on the direction of the magnetization of the GaMnAs layer.
The magnetic anisotropy of magnetization in ferromagnetic materials reflects that of the DOS at EF30. Our study indicates that the magnetic anisotropy of DOS depends on the carrier energy (applied voltage) and can be controlled by band engineering. Combining our results with the electric-field gating technique to tune the EF position will provide a new method to manipulate the magnetization direction by controlling the magnetic anisotropy with an ultra-low power. This method will be useful for the development of nonvolatile spin devices using magnetization in the future.
We grew a Ga0.94Mn0.06As (25 nm)/AlAs (5 nm)/GaAs:Be (100 nm, p=7 × 1018 cm−3) tunnel heterostructure by MBE for the fabrication of devices A–C. The GaAs:Be, AlAs and GaMnAs layers were grown at 550, 530 and 210 °C, respectively. We grew a Ga0.94Mn0.06As (25 nm)/AlAs (6 nm)/GaAs:Be QW (15 nm, p=1 × 1019 cm−3)/AlAs (6 nm)/GaAs:Be (100 nm, p=3 × 1018 cm−3) tunnel heterostructure for device Z. The GaAs:Be electrode, AlAs, GaAs:Be QW and GaMnAs layers were grown at 570, 530, 400 and 210 °C, respectively. The growth rates of GaAs, AlAs and GaMnAs were 500 nm h−1.
After the growth, we annealed the samples in air at 180 °C for 38 h for devices A–C and 20 h for device Z to improve the crystallinity and TC of the GaMnAs layers44,45,46,47,48. We estimated the TC of the GaMnAs layers by measuring the magnetic circular dichroism (MCD) on the samples and analysed the Arrott plots derived from the MCD-μ0|H| curves at various temperatures. The estimated TC is 134 K for devices A–C and 116 K for device Z.
We fabricated tunnel diode devices on the wafer after growth. In our process, we used chemical wet etching with an acid solution composed of phosphoric acid, hydrogen peroxide and water. For devices A–C, we sank the wafer vertically into the etching liquid so that the thickness of the GaMnAs layer changes from 0 to 25 nm in the same wafer. Then, we made circular mesa devices with a diameter of 200 μm on the wafer by chemical wet etching for devices A–C and Z. We then coated a negative insulating resist on the wafers for the passivation of the surfaces and opened contact holes with a diameter of 180 μm on the mesa devices. Then, we deposited Au on the wafers and fabricated contact pads on them.
We carried out the device process, especially the procedure from the surface etching to the Au evaporation, very quickly to minimize the oxidation of the surface GaMnAs layer. Indeed, the resonant levels systematically change with the change in the thickness d of the GaMnAs layer as shown in Supplementary Fig. 4. Also, similar results have been observed in tunnelling devices with GaMnAs fabricated by similar methods27,49. Furthermore, the dependence of dI/dV around 0 V and in the positive V region is similar among samples A–C as shown in Fig. 4a,d,g. Therefore, extrinsic effects induced by the device process are negligible.
We obtained the derivative of the I–V characteristics numerically using the Savitzky–Golay filter. We used seven data points to obtain the derivative at a single point.
In our fitting, we determined the fitting parameters by the modified Levenberg–Marquardt least squares method.
The data that support the findings of this study are included in Supplementary Information, and other data are available from the corresponding authors on request.
How to cite this article: Muneta, I. et al. Artificial control of the bias-voltage dependence of tunnelling-anisotropic magnetoresistance using quantization in a single-crystal ferromagnet. Nat. Commun. 8, 15387 doi: 10.1038/ncomms15387 (2017).
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This work was partially supported by Grants-in-Aid for Scientific Research, including Specially Promoted Research, the Project for Developing Innovation Systems of MEXT, and Spintronics Research Network of Japan. Part of this work was carried out under the Cooperative Research Project Program of RIEC, Tohoku University. I.M. thanks the JSPS Research Fellowship Program for Young Scientists.
Supplementary Figures, Supplementary Notes and Supplementary References