## Introduction

The majority of spintronics research and applications has so far dealt with ferromagnetism, with much less attention given to antiferromagnetic materials. Although they have no net magnetic moment, the microscopic magnetic moments in antiferromagnetic materials can in principle exhibit similar spintronic effects, such as various magnetoresistance effects and the spin torque effect1, as seen in ferromagnetic materials2.

Theoretical and experimental studies have suggested that it is possible to control the antiferromagnetic moments by the spin transfer torque due to a consequence of the interaction between the local moment and the itinerant electron spins3,4,5,6,7. It is also predicted and demonstrated that magnetoresistances, such as anisotropic magnetoresistance8,9,10,11, the planer Hall effect8,11, and the spin Hall magnetoresistance12,13,14, were available for detecting the orientation of the magnetic moments in antiferromagnets.

Wadley et al.8 reported that the CuMnAs having a broken inversion symmetry in its spin sublattices gives rise to the relativistic effective fields by a flow of an electric current in itself. This effective field switches the magnetic moments and the orientation is read by the magnetoresistance. Although the seminal reports8,15,16,17 seem to magnificently advance a spin operation of the antiferromagnet using this relativistic effective field, choice of the materials having such a complex unit cell structure may be limited. To further pave a wide pathway of antiferromagnetic spintronics, it is desirable to seek the control of more generic antiferromagnetic materials.

In this letter, we show a control of the orientation of the magnetic moments in an antiferromagnetic NiO by the spin Hall effect induced spin transfer and also show an electrical detection of the orientation of the magnetic moments based on spin Hall magnetoresistance (SMR). Our results essentially demonstrated a spin torque antiferromagnetic memory with NiO.

NiO is one of the most common natural antiferromagnetic oxides the study of which dates back to the dawn of the antiferromagnetism18. It still continues to be an archetype material for investigating interesting novel phenomena, such as the THz magnon dynamics19, the spin current transmission20,21, and the spin Hall magnetoresistance12,13,14. NiO has a rock-salt structure with magnetic moments inhabiting on Ni cations. The magnetic moments lie in one of the {111} planes and are ferromagnetically aligned on an {111} plane and they antiferromagnetically couple with the magnetic moments in neighboring {111} planes by super exchange coupling18.

Layer structures employed in this study are epitaxially grown Pt 4 nm/NiO 10 nm/Pt 4 nm formed on MgO (111) single crystal substrate by magnetron sputtering. The reflection high-energy electron diffraction (RHEED) analyses confirmed that the each layer was grown as single crystal with (111) face as expected by the lattice matching of the MgO, NiO and Pt (see Methods and Supplementary Information (SI) for details.). Figure 1(a) shows the basic principle of the spin torque rotation of the antiferromagnetic moments in a Pt/NiO/Pt multilayer structure. A current flow Iw in Pt layers invoke the spin Hall effect22,23 and injects a spin current with a spin polarization Is into the NiO layer by $${{\boldsymbol{I}}}_{{\boldsymbol{s}}}=(\hslash /2e){\theta }_{SH}{{\boldsymbol{I}}}_{{\boldsymbol{w}}}\times {\boldsymbol{q}}$$ where $$\hslash$$ is the reduced planck constant, e is the elementary charge, θSH is the spin Hall angle, and q is the unit vector parallel to the flow of the spin current. The spin current with the spin polarization Is,1 from the top Pt layer exerts a spin torque τ1 on the magnetic moment m1 in the NiO layer as τ1 m1 × Is,1× m1. The spin current from the bottom Pt layer similarly results in a spin torque τ2 m2 × Is,2 × m2. Assuming the antiferromagnetic order is coherent in the thickness direction and also assuming a situation where two sets of the spin torque act on the bipartite magnetic moments in the same rotation direction as depicted in Fig. 1(a), the magnetic moments can efficiently rotate without a cost to increasing the exchange energy (or to competing with the molecular field) which strongly ties the neighboring moments. The magnetic moments rotate until they become orthogonal to the current flow and no more spin torque is exerted (See also the macro-spin simulations in Section 2 of SI). In order to demonstrate the control of the antiferromagnetic moments, we used the Hall bar structure with an experimental procedure described in Fig. 1(b). A writing current Iw flowing from the electrode 2 and 3 to the electrodes 1 and 4, as represented by write “1”, rotates the magnetic moments and stabilizes them orthogonal to the direction of Iw. In the same manner, another writing current Iw flowing from the electrode 2 and 4 to the electrode 1 and 3 writes “0”. The orientation of the magnetic moments is read, after each write, by the transverse resistance (RHall) with a small excitation current Ir flowing from the electrode 1 to 2. We particularly took advantage of SMR to read out the orientation of the magnetic moments. In the phenomenology of SMR24, the longitudinal and transverse resistance vary by the relative angle between the magnetic moments in a magnetic layer and the spin polarization of the spin current created by the spin Hall effect in a non-magnetic layer. By adopting the equation for the ferromagnetic case24 for our geometry, RHall due to the orientation of the NiO magnetic moments can be written as,

$${R}_{Hall}\propto -{\rm{\Delta }}{R}_{SMR}\,\sin \,{\theta }_{n}\,\cos \,{\theta }_{n},$$
(1)

where ΔRSMR is the coefficient of SMR and θn is the angle of the Néel vector n with n = m1m2 (see Fig. 1(b) for our circular coordinate with the definition of the general angle θ.). m1 and m2 represent a unit vector for the bipartite magnetic moments as depicted in Fig. 1(a). Here we only consider the in-plane orientation of the magnetic moments.

Figure 1(c) shows representative results of the sequential write-read operation in Pt 4 nm/NiO 10 nm/Pt 4 nm and Pt 4 nm/SiO2 10 nm/Pt 4 nm (a control sample) with various Iw. The operation of write “1” results in a high resistance state and “0” in a low state, which is coherently explained by the spin torque rotation of the magnetic moments and the change of RHall due to SMR described in Eq. (1). For instance, with the write “1”, the spin torque directs the Neel vector at θn = 135° or 315° (these two possibilities are degenerated in our experiment.) as the magnetic moments m1 and m2 become orthogonal to the direction of Iw. Equation (1) yields a high resistance state with θn = 135° or 315° after write “1” and a low state with θn = 45° or 225° after write “0”. One can also clearly see the ΔRHall, which is defined as the change of RHall after each writing operation, varies with Iw. The control experiments in Pt/SiO2/Pt, where SiO2 is a diamagnetic material, show no ΔRHall. We note that the results of the write-read operations are found irrelevant to the polarity of Iw.

Figure 2(a) shows Iw dependence of ΔRHall for the Pt/NiO/Pt. We observed a threshold around 20 mA, corresponding to the current density of 4 × 107 A/cm2. The transverse resistivity change Δρ1 over the resistivity ρ of Pt (Δρ1/ρ) was translated from ΔRHall (See SI for the derivation.). The maximum ΔRHall = 112 mΩ corresponding to Δρ1/ρ = 7.1 × 10−4 was obtained with Iw = 27 mA. On the other hand, RHall in a rotating magnetic field with the angle θH, as shown in Fig. 2(b), shows a sin2θH dependence as expected by the SMR due to the rotation of the spin-flopped Neel vector. We obtained Δρ1/ρ = 1.5 × 10−4 with 14.5 T and it seems to be still increasing with increasing the field magnitude14. Both Δρ1/ρ obtained by the two different measurements are within a reasonable range comparing to previously reported values13,14. We emphasize that the spin torque switching using our scheme requires the current density of only ~107 A/cm2 to control the Neel vectors while the external field requires more than 5 T.

In order for our spin torque writing scheme (Fig. 1(a)) to work, the minimum requirement may be that the magnetic moments of the NiO need to lie in the sample plane and the staggered magnetic moments are coherent in the thickness direction. This condition can be satisfied as the NiO layer is epitaxially grown with (111) plane on which the magnetic moments can lie although magnetic moments laying on other diagonals of {111} may not contribute to the switching. One may also notice that our writing scheme requires the NiO layer to have oppositely pointing magnetic moments at the top and bottom interfaces as exactly depicted in Fig. 1(a) (Otherwise, two sets of the spin torque compete with each other.). Considering the chance of being such a spin configuration, we expect that some parts of the device area are suitable for the writing scheme.

Figure 3 shows the results of the NiO antiferromagnetic domain imaging of the epitaxial Pt 4 nm/NiO 10 nm/Pt 4 nm sample after the write “0” and “1” operations observed by X-ray magnetic linear dichroism-photoemission electron microscopy (XMLD-PEEM) in BL17SU RIKEN beamline at SPring-825. NiO antiferromagnetic spin domains (S-domains) were observed at the Ni-L2 edge in a similar manner described in Refs26 and27. The images after the write “0” and “1” shown in Fig. 3(a,b) were processed by dividing the higher energy peak by the lower energy peak at the L2 edge indicated in Fig. 3(c,d). Therefore, the image contrast directly indicates the NiO S-domains. By the incident direction of the linearly polarized X-ray beam (indicated in Fig. 3(a,b)), the light (dark) regions reflect the Neel vector oriented perpendicular (collinear) to the beam incidence. The NiO domain patterns after the write “0” and “1” clearly differ. They remarkably image the partial rotation of the Neel vector within the Hall bar structure as viewed in the Fig. 3(a,b). For instance, after the write “0”, the black region indicated by the yellow rectangle is widen and the white region indicated by the green rectangle appears. The post-processed monochrome images around the central area of the Hall cross shown in Fig. 3(e) clearly resolve the expansion of the NiO domain after the writing operation. These final states of the Neel vector are perpendicular to the switching current flow, which is consistent with our proposed model described in Fig. 1(a). It is important to emphasize that the Neel vector rotation is not coherent rotation over the Hall bar structure but it occurs in a part satisfying the spin configuration as discussed above.

Since the size of the NiO antiferromagnetic domains is comparable to the Hall bar and the locations where the domain rotates are random as shown in Fig. 3, one may expect that the switching characteristics can easily vary from sample to sample. We indeed found that ΔRHall and Δρ1/ρ with the same Iw are quite scattered from sample to sample as shown in Table 1. For possible antiferromagnetic memory applications in which a full rotation of the NiO domains would be desirable, further efforts may be required to increase the area of switching by more rigorously controlling the appropriate spin configurations in the NiO layer as well as at the NiO/Pt interfaces. Challenging but realistic approaches would be an atomic control of the NiO layer stack and introduction of an additional anisotropy to remove the degeneracy of the NiO {111} easy planes.

In summary, we successfully demonstrated the spin-torque control and the resistive read of the magnetic moments in NiO which is an archetype collinear antiferromagnet. The scheme of controlling and detecting antiferromagnets presented here can be applicable to a wide variety of collinear antiferromagnets, and perhaps other types of antiferromagnets. We emphasize that the demonstrated spin-torque control of NiO is apparently much more efficient than a field control requiring >5 Tesla. The detection scheme using SMR is much more easily accessible than traditionally used neutron scattering18 as well as X-ray magnetic linear dichroism28. Thus, those of our easily accessible combined methodologies will open up more fundamental research opportunities on antiferromagnets. Ultimately, we stress that basic requirements for practical antiferromagnetic spintronic devices, i.e. the electrical control and detection of antiferromagnetic moments, are now fulfilled.

## Methods

### Sample fabrication and characterization

The multilayers were formed by magnetron sputtering on MgO (111) single crystal substrate. We used a sintered NiO sputtering target for the deposition of the NiO layer. All the depositions were done at room temperature with a base pressure below 2 × 10−6 Pa. The reflection high-energy electron diffraction (RHEED) was performed in-situ after the deposition of each layer. The control samples Pt 4 nm/SiO 10 nm/Pt 4 nm were formed on a thermally oxidized Si substrate by magnetron sputtering. As shown in Fig. 1(b), the Hall bar structure with 5 µm-wide channel was patterned by a conventional photolithography followed by an Ar ion milling. Ti (5 nm)/Au (100 nm) was deposited for the contact pads. All the measurements were performed at room temperature.

### The spin torque write-read procedure

We used a multiplexer system built with Keithley 2700 to quickly route the current flow and voltage probes among the electrodes 1~4. We applied Iw for 3 seconds to write, then shut it off, and started reading RHall with an excitation current Ir of 1 mA. RHall was read multiple times with an interval of 30 seconds.

### XMLD-PEEM imaging

XMLD-PEEM was performed in the beamline BL17SU at SPring-8 capable of generating linearly polarized X-ray beams with the photon energy ranging from 500 to 900 eV. An s-polarized (i.e. the oscillating electric field is within the sample plane) X-ray beams were incident to the sample with an incident angle of 16° with respect to the sample surface. The spin torque writing operations were performed outside the PEEM vacuum chamber. After each writing operation, the sample was introduced in the PEEM chamber and observed the images.