Magnetic sensing technology has found widespread application in a diverse set of industries including transportation, medicine, and resource exploration. These uses often require highly sensitive instruments to measure the extremely small magnetic fields involved, relying on difficult-to-integrate superconducting quantum interference devices and spin-exchange relaxation-free magnetometers. A potential alternative, nitrogen-vacancy (NV) centers in diamond, has shown great potential as a high-sensitivity and high-resolution magnetic sensor capable of operating in an unshielded, room-temperature environment. Transitioning NV center–based sensors into practical devices, however, is impeded by the need for high-power radio frequency (RF) excitation to manipulate them. We report an advance that combines two different physical phenomena to enable a highly efficient excitation of the NV centers: magnetoelastic drive of ferromagnetic resonance and NV-magnon coupling. Our work demonstrates a new pathway that combine acoustics and magnonics that enables highly energy-efficient and local excitation of NV centers without the need for any external RF excitation and, thus, could lead to completely integrated, on-chip, atomic sensors.

( A ) Schematic diagram of the experimental sample and the optical excitation/detection scheme. The magnetic field was applied at 45° in-plane from the SAW propagation direction for all optically detected measurements to maximize the power absorption in the magnetic films due to ADFMR. Small particles on the magnetic pad indicate deposited nanodiamonds. ( B ) Photograph of measured device shows IDTs and the magnetoelastic film and indicates the direction of SAW propagation. Dark spots on the film and substrate are clusters of nanodiamonds. ( C ) Diagram of energy flow in the system, showing transduction methods between the different components of the sample. Microwave electrical energy is converted into acoustic energy via piezoelectricity, which then drives magnetic precession. As this precession damps, it generates magnons that couple to the NV centers, modulating their photoluminescence (PL).

Here, we report an advance that combines two different physical phenomena to enable a highly efficient excitation of the NV centers (see Fig. 1 ). The energy flows in this combined system are outlined in Fig. 1C . The first of these is the recent demonstration that FMR in a thin ferromagnetic film can be excited using magnetoelastic interaction with a piezoelectric material ( 9 – 12 ). This allows for the excitation of a purely voltage-driven FMR. The magnetoelastic interaction transduces acoustic excitations into an internal effective magnetic field within the ferromagnet. As a result, the field is extremely local and resides within the ferromagnetic film atop the piezoelectric material. In addition, this effective magnetic field is several orders of magnitude more efficient than traditional FMR excitation via Oersted fields in a stripline ( 12 ), reducing the input power requirement by the same amount. Once the ferromagnet is excited into FMR, the highly local interaction between the NV centers and spatially periodic magnons can now be used to excite the NV centers. This NV-magnon coupling is also extremely efficient, showing comparable Rabi frequencies to microwave excitation using over 1000 times more power (at an NV-antenna spacing of 20 μm) ( 13 , 14 ). Therefore, the entire interaction from piezoelectric to NV centers is highly local and efficient. This combination of localized interaction and reduced input power requirements leads to minimal perturbation of the surrounding environment.

One potential mechanism for localizing the influence of the incident radio frequency (RF) power to the diamond NV centers is to leverage the recently observed interaction between NV centers in diamond and a proximal resonating ferromagnet ( 5 – 8 ). The time-varying excitations responsible for the NV–ferromagnetic resonance (FMR) coupling are spatially periodic magnons, whose magnetic effects should be entirely confined to within a few wavelengths (on the order of micrometers or less for these systems). Commonly, however, such systems run into the same problems of high-power RF excitation—with studies using more than 15 W of microwave power to obtain low-noise measurements ( 7 , 8 ).

Experiments investigating high-sensitivity magnetometry with nitrogen-vacancy (NV) centers commonly require the application of a microwave frequency excitation on the order of 1 to 10 W ( 1 – 3 ). The need for such large excitation power not only complicates the integration of the sensors in a small footprint but also has the potential to substantially perturb the environment that it is trying to measure. For example, a 10-W microwave excitation traveling in a standard 50-ohm stripline creates a magnetic field of approximately 90 μT at a distance of 1 mm, thus making it impossible to take advantage of the intrinsic ability of NV centers to detect fields on the order of tens of femtoteslas in an unshielded environment ( 4 ).

RESULTS

A schematic diagram of our experiment can be found in Fig. 1A, and an optical image of a measured device can be found in Fig. 1B. The system consists of an acoustically driven FMR (ADFMR) device where microfabricated resonant interdigitated transducers (IDTs) launch surface acoustic waves (SAWs) in the piezoelectric LiNbO 3 substrate when driven with a microwave voltage. A ferromagnetic pad, either cobalt or nickel (with a thickness of 20 nm), is located on top of the substrate. Nanodiamonds containing NV centers were deposited at multiple locations on top of the ferromagnetic pad to enable localized optical detection of the ADFMR. These spots can be seen as the dark circles in the optical image.

Figure 2 shows ADFMR absorption data collected from a 20-nm nickel device at 1429 MHz. The dependence of absorption on applied magnetic field and field angle can be seen in Fig. 2A. The characteristic fourfold symmetry evident in the angular scan is a direct consequence of the magnetoelastic driving field that excites ADFMR. An analysis of the magnetoelastic interaction between a ferromagnetic film and longitudinal SAWs shows that the amplitude of the effective magnetic field generated by this interaction varies as cos(θ)sin(θ) (where θ is the angle between the magnetization and the direction of SAW propagation) (15). As the magnetic power absorption in ferromagnetic resonance varies directly with the square of the driving field, this dependence is clearly reflected in the power absorption spectrum.

Fig. 2 Power absorption in ADFMR. (A) Plot of power absorption as a function of applied magnetic field for a 20-nm nickel ADFMR device at 1429 MHz. The x component of the field is taken to be parallel to the direction of SAW propagation, and the y component is in-plane and perpendicular to the direction of SAW propagation. The color bar indicates absorption in decibels per millimeter. (B) Line cut along the angle of highest absorption (45°) showing a large field-dependent attenuation at 287, 861, and 1429 MHz. Although absorption at 287 MHz appears small on a logarithmic scale compared to the other frequencies, absorption in a 1-mm film is still >0.69 dB or ≈15% at 287 MHz.

Figure 2B shows a line cut of the field dependence along the angle of highest absorption (45°) from the SAW propagation direction for all frequencies of excitation used in this study (287, 861, and 1429 MHz). The microwave absorption can be observed as extremely large for such a low-frequency excitation—several orders of magnitude more than a traditional stripline FMR excitation (16).

The ADFMR phenomenon occurs as a result of a combination of piezoelectric and magnetoelastic interactions. An RF voltage applied to an IDT first generates SAWs. These waves generate a time-varying strain that can alter the magnetocrystalline anisotropy of a magnetoelastic ferromagnet via the Villari effect and generate an effective magnetic field internal to the magnet (10). The amplitude of this effective field as a function of applied strain and magnetoelastic coefficients has been previously derived by analyzing the free energy of the magnet in the presence of periodic elastic excitation (15). This effective field is capable of driving the system into FMR.

As the precession generated by ADFMR is damped, it emits spin waves over a range of frequencies (7). The NV center is a spin 1 defect whose PL is dependent on its spin state and is hyperpolarized into its 0 state by the 532-nm pump laser (17). The incoherent spin waves emitted by the precession as it damps can be resonant with the NV, causing the NV spins to relax. NV PL intensity is spin-dependent, being high for the 0 state and low for the ±1 state. Thus, as the NV spins relax because of FMR, their PL intensity changes and this change can be recorded.

Figure 3A shows the change in NV center PL under different conditions for a nickel device. The frequency sweeps done around the first, third, and fifth harmonics (287, 861, and 1429 MHz, respectively) of the IDTs are shown; the IDTs only allow odd harmonics to be transmitted as they are patterned with a 50% metallization ratio (18). The scans shown in Fig. 3A are representative scans to demonstrate the optical detection of ADFMR. The amplitude of the peaks can vary between samples and between nanodiamond clumps on the same sample, in addition to the variation due to position and frequency. Near the edge of the ferromagnetic pad closest to the excitation IDT, at higher frequencies, the average fractional change is approximately 1%, which is comparable to the signal observed in other NV-FMR coupling experiments using diamond nanocrystals (5). All data for PL change presented in this paper are fractional change, that is, lock-in voltage/DC voltage.

Fig. 3 Frequency and spatial dependence of NV-ADFMR coupling in nickel devices. (A) Change in NV center PL normalized to the DC level for nanodiamonds both on and off the ferromagnetic pad. NV centers located off the ferromagnetic pad (red) and NV centers on the pad with a high (35.8 mT) applied bias field (green) show no change in PL. Only NV centers on the pad with zero applied bias field (blue) show a notable PL change. All measured NV PL change outside the shown frequency range is within noise. (Inset) Left: Position of the NV centers on the device. Right: Power absorption of the ferromagnetic film along the applied field direction at the field values of interest. The colors in the insets correspond to the colors in the figure. The peaks in the NV center signal align with the first, third, and fifth harmonics of the IDTs. (B) NV PL change in a 20-nm nickel sample as a function of longitudinal position from the edge of the ferromagnet closest to the excitation IDT. Measurements were performed with the drive frequency set to the first (red), third (green), and fifth (blue) harmonics of the IDTs and at zero applied magnetic field. (Inset) Schematic illustration of nanodiamond positions.

Clear peaks in the optical signal can be seen for nanodiamonds at zero magnetic field and on the nickel pad (blue). The NV spins by themselves should not have any signal at 287 and 861 MHz since they are far away from any NV resonances in zero field. However, at 1429 MHz, a direct drive signal can be observed since this coincides closely with the NV’s excited state resonance frequency. To check the origin of the signal, we performed a control measurement away from the ferromagnetic pad (red), which shows no signal even at 1429 MHz, although this spot was closer to the input IDT and should have a larger amplitude of acoustic waves (and spurious microwaves). Thus, we can rule out any spurious interaction of the acoustic waves or microwaves directly with the NV in our experiment. Although strain waves can couple to the NV center (19, 20), we do not see any evidence for this interaction in our experiment—most likely because of the very weak mechanical coupling between the substrate and the nanodiamonds. To further verify the FMR origin of the peaks scene in the blue data, we measured the signal at a higher field (green). A field strength of 35.8 mT is sufficient to bias the magnetic films out of resonance. As it can be seen, we observe no PL signal at these fields. Thus, our control measurements verify that the peaks scene in the blue data is due to FMR.

Next, we demonstrate the local nature of the drive by recording spatially localized data across the ADFMR device. Figure 3B shows the change in fractional NV PL at zero field for the 20-nm nickel device as a function of longitudinal position, that is, distance from the edge of the nickel pad closest to the excitation IDT along the SAW propagation direction. The data presented here are an average of three spots that are the same distance from the edge of the nickel pad (see inset). This averaging helps mitigate the effect of inhomogeneity in nanodiamond spots at various locations. The distance between the NV centers and the ferromagnet determines coupling efficiency, and thus, inhomogeneity arising from the deposition process can lead to a noisy signal.

These direct spatial measurements performed via coupling to NV centers provide another means of measuring the power absorption data shown in Fig. 2B. At 287 MHz, the PL amplitude is constant (within measurement error) over the full length of the film, as would be expected given the relatively small power absorption seen at this low frequency. As the excitation frequency is increased, the NV PL change can be seen to decrease as a function of distance from the leading edge of the film. This decrease is due to absorption of the excitation signal as it travels through the magnetic layer. These measurements corroborate previous measurements of ADFMR power absorption as a function of magnetic element length (11) and excitation frequency (10, 11, 21).

We now provide further evidence for optical detection of ADFMR by performing field sweeps around these IDT harmonic frequencies for both cobalt and nickel devices. These data are presented in Fig. 4, where we show change in the detected electrical signal (corresponding to absorption in the ferromagnetic film) in addition to the optical signal. The correlation between the optical signal and the transmission signal can be seen, especially in the case of cobalt. No peaks in the optical signal were seen in nanodiamonds not located on the ferromagnetic pads. It should be noted that, although we have previously detected FMR in cobalt using our relaxation-based technique, this is the first report of optical detection of FMR in nickel using NV centers. The peak heights of the optical signal are comparable in both cobalt and nickel, although the absorption signal is an order of magnitude (or more) larger in nickel films. This would imply that the coupling between nickel and NV centers is much smaller than for the case of cobalt. The reason for dependence of the coupling on the magnetic material is currently unknown.