Abstract
Proposals for novel spin-orbitronic logic1 and memory devices2 are often predicated on assumptions as to how materials with large spin–orbit coupling interact with ferromagnets when in contact. Such interactions give rise to a host of novel phenomena, such as spin–orbit torques3,4, chiral spin structures5,6 and chiral spin torques7,8. These chiral properties are related to the antisymmetric exchange, also referred to as the interfacial Dzyaloshinskii–Moriya interaction (DMI; refs 9, 10). For numerous phenomena, the relative strengths of the symmetric Heisenberg exchange and the DMI are of great importance. Here, we use optical spin-wave spectroscopy (Brillouin light scattering) to directly determine the volume-averaged DMI vector D for a series of Ni80Fe20/Pt thin films, and then compare the nearest-neighbour DMI coupling energy with an independently measured value of the Heisenberg exchange for each sample. We show that the dependence on Ni80Fe20 thickness of both the microscopic symmetric and antisymmetric exchange are nearly identical, consistent with the notion that the fundamentals of the DMI and Heisenberg exchange essentially share the same underlying physics, albeit with different symmetries, as was originally proposed by Moriya11 for superexchange in magnetic oxides, and by Fert and Levy12 for RKKY coupling in metallic spin glasses. Indeed, our result demonstrates the generality of the original DMI theory, insofar as the proportionality of the symmetric and antisymmetric exchange is robust with regard to the details of spin coupling for the material system in question. Although of significant fundamental importance, this result also leads us to a deeper understanding of DMI and how it could be optimized for spin-orbitronic applications.
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Main
Recent experimental results have demonstrated how the interplay of symmetric (Heisenberg) exchange and antisymmetric (DMI) exchange, together with anisotropy, can give rise to a variety of magnetostatic phenomena, such as magnetic skyrmion lattices13, spiral spin structures14 and chiral domain walls6. In bilayer materials with a sufficiently thin, perpendicularly magnetized ferromagnet (FM) adjacent to a metal with large spin–orbit coupling in the conduction band, a large DMI favours Néel domain walls with a fixed chirality15, as opposed to Bloch walls. The combination of a chiral domain wall structure and spin–orbit torque can give rise to fast current-induced domain wall motion16. The direction and the speed are both dependent on the sign and the strength of the DMI and the spin–orbit torque7,8. Moreover, theory for a Rashba model predicts that the interfacial spin–orbit torque is proportional to the ratio of symmetric and antisymmetric exchange17. Thus, direct determination of both the DMI and Heisenberg exchange is crucial for an understanding of the underlying physics in such materials systems and a better understanding of the spin–orbit torques.
So far, direct measurements of antisymmetric exchange are limited to exotic measurement techniques that can only be applied to a few highly specialized sample systems. For example, the DMI constant has been measured by means of synchrotron-based X-ray scattering interferometry for the weak ferromagnet FeBO3 (ref. 18), by spin-polarized electron energy loss spectroscopy for an atomic bilayer of Fe on W(110) (ref. 19) and by spin-polarized scanning tunnelling microscopy for atomic monolayer Mn on W(110) (ref. 5). Until now, estimation of the antisymmetric exchange in the case of arbitrary materials has been possible only via inference from indirect measurement methods. These methods include both determination of the critical ferromagnetic layer thickness at the transition from a Néel to a Bloch wall6, and measurements of domain wall motion20,21. Furthermore, quantitative experimental comparison of the symmetric and antisymmetric exchange is still outstanding.
Recent theory predicts an asymmetric dispersion shift of long-wavelength thermal spin waves in magnetic thin films due to the DMI (refs 22, 23, 24, 25, 26). Motivated by this theory, we used Brillouin light scattering (BLS) to directly measure the predicted asymmetric dispersion shift, which in turn allowed us to determine the magnitude and direction of the DMI vector in a technological relevant sample system: we used a series of sputtered multilayer stacks consisting of SiN/Ni80Fe20(t)/Pt(6 nm)/Ta(3 nm)/substrate, where t ranged from 1 nm to 13 nm. We independently determined the symmetric exchange by fitting low-temperature magnetometry data to the Bloch T3/2 law for the same samples. Comparison of the two data sets allowed us to unambiguously determine the proportionality of the symmetric and antisymmetric exchange.
Interfacial DMI in a thin ferromagnetic film adjacent to a high spin–orbit material is mediated by an atom in the high spin–orbit material. The Hamiltonian for the DMI between two spins Si and Sjon the atomic sites i and j is given by HDMI = −Dij ⋅(Si × Sj). Here, Dij = Dij n × eij is the DMI vector, which lies in the symmetry-breaking plane and is perpendicular to the unit vector that connects sites i and j, eij ≐rij/ |rij|, as shown in Fig. 1a, b, and n is the interface normal. Spin waves in the ferromagnet have a spatial chirality, which depends on their propagation direction with respect to the direction of the magnetization. In particular, for M∥ + z, spin waves propagating in the −x direction have anticlockwise spatial chirality (Fig. 1a), whereas those propagating in the +x direction have clockwise chirality (Fig. 1b). However, the spatial chirality favoured by the DMI is fixed by the sign of Dij, thus the presence of the DMI causes an asymmetric modification of the spin-wave dispersion relation. For an in-plane magnetized film with spin waves propagating perpendicular to the magnetization direction, the DMI modifies the frequency
of the spin waves22 (see middle panel of Fig. 1c.) Here, f0 is the spin-wave frequency in the absence of the DMI and
is the DMI-induced frequency shift, where DDMI ∝ Dij is the volumetric DMI constant that determines the sign and magnitude of the DMI vector, g∥ is the in-plane spectroscopic splitting factor, Ms the saturation magnetization, k (with magnitude k) the wavevector of the spin waves, μB the Bohr magneton and h Planck’s constant. In the presence of the DMI, the spin-wave frequencies have a shift linear in kx to either higher or lower frequencies, depending of the propagation direction and the polarity of the static magnetization component M. If the spin-wave spatial chirality is favoured by the DMI, the spin-wave frequency is reduced. Conversely, it is increased for the opposite chirality. Although the presence of surface anisotropy can also lead to a non-reciprocal spin-wave dispersion27, calculations presented in the Methods show that the asymmetric frequency shift of magnetostatic surface waves due to interfacial anisotropy is small for our measurements.
The dispersion characteristics of spin waves in thin magnetic films can be measured with BLS. In our BLS measurements, a laser is focused onto a sample, and the photons are inelastically backscattered by the quantized spin waves—that is, magnons. Momentum conservation dictates that magnons propagating towards the incoming laser beam must be annihilated (the anti-Stokes process), and magnons propagating in the opposite direction must be created (the Stokes process). (See Fig. 1c.) Energy conservation then uniquely identifies the inelastic energy shift of the backscattered photons with the magnon propagation direction: if the energy of the scattered photon is increased (or decreased) by the magnon energy, the direction of magnon propagation is either towards (or away from) the laser beam. Thus the measurement of the scattered photon energy can be used to determine the frequency difference of spin waves propagating in opposite directions, as sketched in Fig. 1c. We measured the spin-wave frequencies for the two field polarities transverse to the scattering plane, and for the two propagation directions. This yields four independent measurements of spin-wave frequency as a function of magnetization polarity and propagation direction. In Fig. 2a, b, normalized BLS spectra for Ni80Fe20 film samples of thickness t = 1.3 nm and 2.0 nm, respectively, on a 6 nm Pt underlayer are shown. For comparison, we also show data for a control sample film of 2.0 nm Ni80Fe20 without a Pt underlayer in Fig. 2c. The BLS spectra of the samples with a Pt underlayer exhibit a frequency shift of the order of 100 MHz that changes sign with magnetization polarity or reversal of the spin-wave propagation direction. This frequency difference is larger for the sample with thinner Ni80Fe20, as expected for an interfacial source of symmetry breaking, whereas there is no frequency difference for the control sample, in agreement with the absence of interfacial DMI in this case.
In Fig. 3, we show the t-dependence of the frequency shift ΔfDMI averaged over the four possible combinations of the magnetization polarity and propagation direction. Consistent with the interfacial nature of the DMI, ΔfDMI decreases with increasing t. According to equation (1), Ms and g∥ are required to determine DDMI from the measured ΔfDMI. Ms at 300 K, measured by means of superconducting quantum interference device (SQUID) magnetometry, is shown in Fig. 4a. g∥ is measured by ferromagnetic resonance spectroscopy (see Supplementary Information). We use equation (1) to calculate DDMI, shown in Fig. 4b. Under the assumption that the DMI is a strictly interfacial property that is not affected by the bulk properties of the magnetic film, the magnitude of DDMI should be linearly proportional to 1/t and be zero in the limit of an infinitely thick film. However, the measured DDMI exhibits a nonlinear dependence on 1/t. This result implies that the DMI strength at the interface itself changes with the film thickness. Under the assumption that only the first monolayer of Ni80Fe20 at the Pt interface contributes to the antisymmetric exchange, the strength of the DMI at the interface DDMIint can be calculated from
where a = 0.354 nm is the lattice constant for Ni80Fe20. DDMIint is shown in Fig. 4c (left scale) and has a non-trivial dependence on the Ni80Fe20 thickness. In particular, we find that the magnitude of the antisymmetric exchange varies by a factor of almost 2.5 over the range of sample thicknesses. Using equation (6) in the Methods, the largest value for the interatomic antisymmetric exchange energy Dnn that we obtain (for t = 6.1 nm) is −2.2−0.4+0.7 meV. This is very similar in magnitude to the recently reported result of +0.9 meV for Fe/W in ref. 19 and −1.05 meV for a Co/Ni multilayer on Pt(111) in ref. 6.
Theoretical calculations for the Dzyaloshinskii–Moriya interaction in bulk magnetic oxides and metallic spin glasses with magnetic impurities predict that the symmetric and antisymmetric exchange are proportional to each other11,12,28. It is therefore possible to speculate that the thickness dependence of DDMIint is the result of a coincidental thickness dependence of the symmetric exchange for this particular system. The Heisenberg exchange Hamiltonian that describes the interaction of two spins is given by Hex = −JijSi ⋅ Sj, with the exchange integral Jij = 2g∥μBDspin/(Msa5) for the fcc lattice, where Dspin is the spin-wave stiffness. Given that Jij is strongly influenced by the local environment of the electron wavefunction that overlaps sites i and j, it is always plausible that there is a non-trivial thickness dependence for the volume-averaged exchange. As we show below, this is indeed the case for our particular sample system.
We measure the temperature dependence of the saturation magnetic moment ms(T) with a SQUID magnetometer and fit the data with the Bloch T3/2 law at low temperatures29,
where T is the temperature, Dspin0 K is the low-temperature spin-wave stiffness, and kB is the Boltzmann constant29. To determine the exchange constant A at 300 K, we use
where we take the temperature-dependent renormalization of the spin-wave stiffness into account, as detailed in the Supplementary Information. In Fig. 4c (right scale), the thickness dependence of A is shown. Although the microscopic origins of the variation in the symmetric exchange with film thickness is unclear, it is an empirical fact that both the symmetric exchange A and the antisymmetric exchange DDMIint exhibit the same non-trivial functional dependence on reciprocal thickness. If we consider only nearest-neighbour interactions, the ratio DDMI/A is proportional to the ratio of the nearest-neighbour exchange integral Jnn and the magnitude of the nearest-neighbour DMI Dnn,
as shown in the Methods. From DDMIint and A in Fig. 4c, we find by fitting equation (3) to the data that Dnn/Jnn = −(8.4 ± 0.3)%, independent of Ni80Fe20 thickness. Any potential existence of a gradient in the magnitude of the symmetric exchange A through the thickness of the Ni80Fe20 can only be very small and would only marginally affect the proportionality between Dnn and Jnn. The homogeneity of the exchange is exemplified by the fact that the volume-averaged magnetization for the 3.4 nm (16.6 monolayers) sample is already equal to the bulk value of μ0Ms ∼ 1 T at 300 K. The linear proportionality between the symmetric and antisymmetric exchange was first proposed for bulk materials in the original theory of Moriya11. Similarly, such a proportionality was also predicted by Fert et al.12,28, for metallic spin-glass systems. Our results confirm that this proportionality also applies to two-dimensional systems at the interface between a ferromagnetic layer and a material with large spin–orbit coupling.
An important implication of our result is the independence of interfacial chiral ordering on parameters that affect the Heisenberg exchange, as the spin canting angle at adjacent atomic sites is proportional to the ratio DDMIint/A. Thus, the methods and results presented here not only serve to elucidate the fundamental properties of the DMI, but may also have a substantial impact on the methodology to successfully develop spin-orbitronic devices.
Note added in proof:
During the review process further evidence of the non-reciprocal spin-wave dispersion due to DMI has emerged: Phys. Rev. Lett., 114, 047201 (2015); Phys. Rev. B, 91, 214409 (2015); Phys. Rev. B, 91, 180405(R) (2015); Appl. Phys. Lett., 106, 052403 (2015).
Methods
Sample preparation.
All samples were prepared by d.c. magnetron sputtering in an Ar base pressure of ∼0.07 Pa (∼0.5 mtorr) and a chamber base pressure of 3 × 10−6 Pa (2 × 10−8 torr). Samples were rotated at 1–2 Hz during deposition to eliminate growth-induced anisotropy. The deposition rates were calibrated by X-ray reflectometry. The SiN(5 nm–10 nm)/Ni80Fe20(t)/Pt(6 nm)/Ta(3 nm)/substrate films were deposited on thermally oxidized Si. The silicon nitride capping layer was sputter-deposited from a pure Si target in an Ar and N2 gas mixture. The Ta seed layer induced a strong (111)-texture of both the Pt and Ni80Fe20.
SQUID magnetometry.
We measured in-plane hysteresis curves at room temperature to determine the saturation magnetization Ms(300 K) of our samples. We find that Ms(300 K) decreases with decreasing Ni80Fe20 layer thickness. In addition, we measured the dependence of the magnetic moment ms(T) on temperature T while exposed to an applied field of μ0H = 10 mT. The saturation magnetization Ms(0 K) was determined by extrapolation of the fit of ms(T) to the Bloch T3/2 law29. To determine from these fits the spin-wave stiffness, Dspin0 K, at 0 K for the Ni80Fe20 thickness series, we first calculate the density of excited magnons at a given temperature. This calculation takes into account finite-size effects due to the reduced thickness of the Ni80Fe20 layer. The room-temperature exchange constant A is then determined using a mean-field approach for the temperature dependence of the exchange. The details on the determination of the exchange constant, renormalization and calculation of the magnon density are given in the Supplementary Information.
Brillouin light scattering spectroscopy.
We use a Brillouin light scattering spectrometer with a six-pass, tandem Fabry–Perot interferometer to measure the thermal spin waves frequency at a fixed angle of incidence θ = 45°. For our measurements the incident laser power was 40 mW. A λ = 532 nm laser beam was focused on the sample with an f/1.2 lens. Thus the wavevector of the measured spin waves is k = 16.7 μm−1. The collimated backscattered light was spatially filtered with an aperture (14 mm in diameter) to reduce the wavenumber uncertainty.
Ferromagnetic resonance measurements.
We employed ferromagnetic resonance spectroscopy with the external magnetic field both parallel and perpendicular to the sample plane to determine the respective spectroscopic splitting factors g⊥ and g∥ and the perpendicular anisotropy field Hk. Details about the measurements are given in the Supplementary Information.
If not otherwise stated, all error bars and all uncertainties stated in the text are single standard deviation uncertainties.
Determination of the Dzyaloshinskii–Moriya exchange.
The DMI Hamiltonian for two atoms at sites i and j with the spins Si and Sj, respectively, is given by
where is the Dzyaloshinskii–Moriya vector, with rij being the vector between sites i and j and is a unit vector along the axis of broken symmetry—that is, the interface normal—for our particular case. The following calculation applies to a single ferromagnetic monolayer in contact with a high spin–orbit material. Following the analysis of Udvardi and Szunyogh, for the case where a spin wave propagates perpendicular to the magnetization, the DMI contribution to the spin-wave energy for an atomic monolayer is25
where , k is the spin-wave wavevector, S is the total spin on each site, and c = ±1 is the spin-wave chirality. (The necessary factor S is missing in the original version of equation (4) in ref. 25.) The chirality is defined by the orientation of the magnetic moment at each lattice site25:
Here, Ri is the position vector for the atomic site i, θ is the relative angle of the moments and , and are unit vectors. In a (111)-textured fcc crystal, the grains are randomly rotated around the surface normal and equation (4) needs to be averaged about all possible orientations. Evaluation of equation (4) in the long-wavelength limit then yields
where φ is the angle between rij and k, Dnn is the magnitude of the nearest-neighbour DMI vector, and a is the lattice constant.
Damon–Eshbach modes with antisymmetric exchange.
Following the analysis of Moon et al.22, the spin-wave dispersion for spin waves in a thin film with k ⊥ M for in-plane magnetization—that is, the Damon–Eshbach mode (DE)—in the presence of interfacial DMI is22,23,24,25,26,30,31
where A is the exchange constant. The last term in equation (5) accounts for the DMI, which causes a frequency shift linear in the spin-wave wavenumber k. The sign of the DMI-induced frequency shift depends on the sign of DDMI, the orientation of the magnetization (sign of M) and the propagation direction of the spin waves (sign of k). Here we are using a volumetric DMI constant instead of including the DMI into the boundary conditions. The results for these two approaches are in good agreement for |k| t < 0.28, which is the case for our measurements23. Comparison with equation (5), and accounting for the conversion from the interfacial DMI to the volumetric DMI, as quantified in equation (2), allows us to express the volumetric DMI constant DDMI in terms of the microscopic Dnn as
and in terms of the interfacial DMI constant DDMIint we have , which yields
In the main part of the manuscript we calculate the exchange constant:
The ratio of the interfacial DMI constant and the exchange constant can now be related to the fundamental quantities of the symmetric and antisymmetric exchange:
Thus, if the antisymmetric exchange simply scales in proportion to the symmetric exchange for a given material system, the ratio of the interfacial DMI and the exchange constant should be constant.
Non-reciprocal spin-wave modes.
For thin magnetic films, the DE spin-wave modes are non-reciprocal—that is, the mode is localized either at the top or bottom interface—depending on its propagation direction and the orientation of M. Hence, spin waves with k > 0 are localized at the bottom (top) interface for M∥ + z (M∥ − z) and spin waves with k < 0 are localized at the top (bottom) interface for M∥ + z (M∥ − z). Thus, if the two Ni80Fe20 interfaces were to have strongly differing magnetic properties, it is possible that the non-reciprocal nature of the DE modes could also give rise to an asymmetric spin-wave dispersion. In the following, we will estimate an upper value for the frequency shift due to the non-reciprocal character of the surface waves.
For the geometry used here, the spin wave propagating in the positive x-direction is localized at the Pt interface for positive applied field, whereas the spin wave propagating in the opposite direction is localized at the SiN interface. If we neglect the symmetric-exchange contribution—that is, the long-wavelength limit—the DE-mode amplitude decays exponentially into the film thickness with a decay length = 1/k. For the wavevector k = 16.7 μm−1 of the spin waves, which are measured in the BLS experiment, this results in a decay length δ = 60 nm. This yields a difference of the spin-wave amplitude between the two interfaces of 2 and 20% for the thinnest and thickest sample of the Ni80Fe20/Pt series, respectively. The Pt interface induces a thickness-dependent perpendicular anisotropy field Hk (see Supplementary Fig. 4 in the Supplementary Information). Thus, the frequency of the spin wave with stronger localization at the Pt interface is shifted to lower frequencies with respect to the spin wave propagating in the opposite direction. To calculate the frequency shift due to the surface anisotropy we use a mean-field approach. The anisotropy field Hkint(t) is assumed to be localized within the first monolayer of the Ni80Fe20 layer. The effective anisotropy for each spin wave propagating in the positive and negative directions, respectively, is then calculated by weighting the anisotropy field with the spin-wave amplitude for the respective mode profile m±(t):
The integrals extend over the Ni80Fe20 layer thickness. The estimate of the frequency difference for the spin waves propagating in opposite directions is then calculated with equation (5). We find a frequency shift for the samples of about 0.03 GHz, almost independent of Ni80Fe20 thickness. Note that this is in qualitative contrast to the strong dependence of the DMI-induced frequency shift on Ni80Fe20 thickness (see Fig. 3 in the main text). The frequency shift due to the surface anisotropy would be even smaller if exchange were taken into account, because this would lead to a more gradual decrease of the spin-wave amplitude from the respective surface. Hence the value of 0.03 GHz is an upper limit for the frequency shift due to the localization of the Damon–Eshbach modes. This upper limit is included in the error bars in Fig. 3 in the main text. The frequency shift due to the non-reciprocal character of the surface spin waves thus has only a very marginal influence on the frequency shifts determined by BLS in our measurements.
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Acknowledgements
The authors are grateful to Ward Johnson for his support of our BLS measurements, and thank M. Stiles and R. McMichael for stimulating discussions. M.W. acknowledges a stipend by the German academic exchange service (DAAD).
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H.T.N. conceived the experiment, performed the BLS measurements and analysed the BLS data. J.M.S. fabricated and characterized the samples and performed SQUID measurements, M.W. performed the FMR measurements and analysis. All authors contributed to the interpretation of the results and writing of the manuscript.
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Nembach, H., Shaw, J., Weiler, M. et al. Linear relation between Heisenberg exchange and interfacial Dzyaloshinskii–Moriya interaction in metal films. Nature Phys 11, 825–829 (2015). https://doi.org/10.1038/nphys3418
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DOI: https://doi.org/10.1038/nphys3418
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