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# Electrical charge state identification and control for the silicon vacancy in 4H-SiC

## Abstract

Reliable single-photon emission is crucial for realizing efficient spin-photon entanglement and scalable quantum information systems. The silicon vacancy ($${V}_{{\rm{Si}}}$$) in 4H-SiC is a promising single-photon emitter exhibiting millisecond spin coherence times, but suffers from low photon counts, and only one charge state retains the desired spin and optical properties. Here, we demonstrate that emission from $${V}_{{\rm{Si}}}$$ defect ensembles can be enhanced by an order of magnitude via fabrication of Schottky barrier diodes, and sequentially modulated by almost $$50 \%$$ via application of external bias. Furthermore, we identify charge state transitions of $${V}_{{\rm{Si}}}$$ by correlating optical and electrical measurements, and realize selective population of the bright state. Finally, we reveal a pronounced Stark shift of 55 GHz for the V1′ emission line state of $${V}_{{\rm{Si}}}$$ at larger electric fields, providing a means to modify the single-photon emission. The approach presented herein paves the way towards obtaining complete control of, and drastically enhanced emission from, $${V}_{{\rm{Si}}}$$ defect ensembles in 4H-SiC highly suitable for quantum applications.

## Introduction

Solid-state single-photon emitters (SPEs) and optically addressable spin centers are an emerging technology ideally suited for quantum computing, sensing, and information processing applications.1,2 Efficient room-temperature single-photon sources naturally fulfill key requirements for enabling secure communication via quantum key distribution,3,4 and offer a platform for optical quantum computing5 and communication.6 Moreover, single-photon emission from a bound and individually addressable paramagnetic state enables optical manipulation of the spin state and entanglement between quantum systems,7 culminating in the feasibility of quantum networks.8

The nitrogen-vacancy center in diamond1 has become a benchmark for implementing semiconductor point defects in quantum technologies, but is suffering from the immaturity of the material and device fabrication. More recently, point defects in silicon carbide (4H-SiC) have gained attention as a more device-friendly alternative, offering a platform to merge existing semiconductor processing capabilities with the quantum technology of the future.9,10 Recent testaments to the viability of 4H-SiC as a quantum host include single-photon emission from, and coherent control of, the silicon vacancy ($${V}_{{\rm{Si}}}$$),11,12,13 carbon antisite-vacancy pair ($${{\rm{C}}}_{{\rm{Si}}}{V}_{{\rm{C}}}$$),14 transition metal15 and silicon-carbon divacancy ($${V}_{{\rm{Si}}}{V}_{{\rm{C}}}$$)16 spins at room temperature, as well as observations of millisecond spin coherence times for $${V}_{{\rm{Si}}}$$17 and $${V}_{{\rm{Si}}}{V}_{{\rm{C}}}$$18 at cryogenic temperatures.

Hitherto, the desired quantum properties of defects in 4H-SiC have been established for specific charge states only, with the remainder being dark and exhibiting no identified spin signals. In the case of $${V}_{{\rm{Si}}}$$, the negative charge state ($${V}_{{\rm{Si}}}^{-}$$) exhibits both a high-spin ground state of $$S=3/2$$ and two single-photon radiative channels, as observed by photoluminescence (PL), and labeled V1 and V2.19 Recently, robustness towards detrimental effects such as electron–phonon interactions and fast spin dephasing was established for $${V}_{{\rm{Si}}}^{-}$$,20 and a large fraction ($$40 \%$$) of optical emission was found in the zero-phonon line (ZPL),21 cementing the position of $${V}_{{\rm{Si}}}^{-}$$ as a promising qubit candidate. However, the overall low photon count rates plague emission from $${V}_{{\rm{Si}}}$$ in SiC, and optical signals from isolated defects are challenging to detect without resorting to nanofabricated waveguides,11,22,23 or implementation into photonic crystal cavities.24

Charge state conversion between the different $${V}_{{\rm{Si}}}$$ and $${V}_{{\rm{Si}}}{V}_{{\rm{C}}}$$ states in 4H-SiC9,25 has been demonstrated by applying electric fields26,27,28 or via laser excitation.29,30,31 Unfortunately, the dark charge states under scrutiny remain largely unknown, and selective charge state population of $${V}_{{\rm{Si}}}^{-}$$ accompanied by reliable switching between known bright and dark states has not been achieved so far.

In the present work, we enhance the V1 emission from ensembles of negatively charged silicon vacancies via the built-in field generated by Schottky barrier diodes (SBDs), and manipulate the bright state by an external bias. Our findings are discussed in terms of band bending at the SBD/semiconductor interface and the resulting selective charge state population of $${V}_{{\rm{Si}}}^{-}$$. The charge state transitions $${V}_{{\rm{Si}}}$$($$-/2-$$) and $${V}_{{\rm{Si}}}$$($$2\!-\!/3-$$) are then identified by combining deep level transient spectroscopy (DLTS), PL spectroscopy, and hybrid density functional theory calculations. The correlation between optical and electrical characterization is rarely seen for qubit candidates, and to the best of our knowledge unique in silicon carbide. Finally, we reveal a Stark shift for $${V}_{{\rm{Si}}}^{-}$$-related emission with a quadratic field dependency, illuminating the nature of the $${V}_{{\rm{Si}}}^{-}$$ ground and excited states and providing a means of tuning the emission energy. Our findings prove that selective and controlled charge state population and switching is possible for a solid-state quantum bit, and we therefore propose the SBD platform to control the charge state, spin state and luminescence from isolated qubits (or ensembles thereof) in 4H-SiC.

## Results

The silicon monovacancy ($${V}_{{\rm{Si}}}$$) remains one of the most extensively studied quantum emitters in 4H-SiC. Two ZPLs observed in the near-infrared region of PL spectra from n-type 4H-SiC exhibit single-photon emission characteristics and have been attributed to internal transitions of the negatively charged $${V}_{{\rm{Si}}}$$,11,19 namely V1 at 1.44 eV and V2 at 1.35 eV.32 An exemplar PL spectrum of proton-irradiated n-type 4H-SiC, with the V1 and V2 lines highlighted, is shown in Fig. 1a (see Supplementary Notes 1 for further details). Recently, the V1 and V2 emission lines were attributed to the inequivalent hexagonal ($$h$$) and pseudo-cubic ($$k$$) $${V}_{{\rm{Si}}}^{-}$$ defect configurations, respectively,20,33 in contrast to what was previously suggested.32 Figure 1b illustrates the ground state defect configuration, partial charge density and spin state for $${V}_{{\rm{Si}}}^{-}$$($$h$$) and $${V}_{{\rm{Si}}}^{-}$$($$k$$), respectively. In addition, $${V}_{{\rm{Si}}}^{-}$$ manifests single-photon emission, from one excited state accessible for $${V}_{{\rm{Si}}}^{-}$$($$k$$) (the V2 transition) and two for $${V}_{{\rm{Si}}}^{-}$$($$h$$) (the V1 and V1′ transitions). The presence of V1′, a ZPL closely related to V1, but assigned to a second excited state of $${V}_{{\rm{Si}}}^{-}$$ that is slightly higher in energy,19,21,24,33 marks the V1/V1′ defect center as dichroic. Here, we will focus on the V1/V1′ defect, firstly to avoid interference from the broad luminescence band overlapping with V2, and secondly because of the large Debye–Waller factor of the V1 line ($$>40 \%$$21). With a large portion of photons channeled into the V1 ZPL, we are more likely to observe any electrically induced modulation of the V1/V1′ emission intensity.

### Effect of built-in field on silicon vacancy-related emission

The influence of the SBD-induced built-in field on the V1 emission originating from $${V}_{{\rm{Si}}}^{-}$$ is investigated using an experimental setup as illustrated in Fig. 2a. We study n-type 4H-SiC samples having 10 µm epitaxial layers topped by circular nickel SBDs of 1 mm diameter. The defects are optically addressed at temperatures ranging from 10 to 100 K, and defect-related PL is analyzed using backside imaging geometry, where both laser excitation and PL acquisition are from the substrate side (see Fig. 2a). The dopant concentration in the epitaxial layer was $$1\,\times 1{0}^{15}$$ cm$${}^{-3}$$, as determined by capacitance–voltage measurements, with substrate doping being estimated at several orders of magnitude higher (see Supplementary Notes 2 for further information about the samples and SBDs). The silicon vacancies were formed using 1.8 MeV proton irradiation to varying fluences, having a projected range located $$\sim\!27\,\mu {\rm{m}}$$ into the sample, which was calculated using collision Monte Carlo models as implemented in the SRIM code34 (see Supplementary Methods 1). At room temperature, the space charge region (SCR, see Fig. 2a) spans approximately 1.5 µm and 4 µm into the sample for zero (0 V) and reverse bias ($$-10$$ V), respectively. Consequently, the $${V}_{{\rm{Si}}}$$ concentration is assumed constant throughout the probed region, as illustrated by the $${V}_{{\rm{Si}}}$$ concentration versus depth profile in Fig. 2c.

The effect of the built-in field induced by the SBD on the V1/V1′ emission intensity is displayed in Fig. 2b, where PL spectra obtained at 10 K from the SCR within the SBD and from the nearby area outside the SBD perimeter are put alongside for comparison. One can observe significant, more than by an order of magnitude, enhancement of V1-related emission once collected from the SCR of the SBD (further examples are shown in Supplementary Notes 3). Importantly, this drastic increase is larger than could be expected from purely geometrical considerations that include reflection/scattering from the semiconductor–metal interface along with possible contributions from double-pass excitation and retroflection. In our opinion, such a significant enhancement can only be adequately explained by assuming that the band-bending induced by the Schottky barrier is affecting the charge state of the silicon vacancies being illuminated, with a larger portion of $${V}_{{\rm{Si}}}$$ in the negative charge state inside compared to outside of the space charge region. It is worth noting at this point that the V1-related emission peak is clearly visible up to 150 K, although a significant line broadening occurs at higher temperatures (see Supplementary Notes 1). Moreover, the identity of the two peaks around 867 nm in Fig. 2b are at the present time unknown.

Intriguingly, which excited state $${V}_{{\rm{Si}}}^{-}$$ prefers upon illumination seems to depend on the presence of the SBD. When no SBD is present, both the V1 and V1′ lines (with typically reported values of 861.3 nm and 858.7 nm, respectively) are observed, with the V1:V1′ ratio depending on factors such as the $${V}_{{\rm{Si}}}$$ concentration, the incident laser intensity and polarization, and the temperature. The built-in field of the SBD, however, seems to promote excitation to the higher-lying V1′ excited state as shown in Fig. 2b; the lower energy V1 emission line was not detected for any of the tested SBDs. Thus, the promotion of $${V}_{{\rm{Si}}}^{-}$$ to the V1′ excited state (see Fig. 1b) appears to be connected to the SBD-induced field. Fortunately, as optical spin manipulation can be improved by selectively exciting the V1′ state due to the reduced intersystem crossing rates,20 the straightforward process of depositing a nickel SBD on the sample surface promises both enhanced optical emission and now also augmented control over spin dynamics. Therefore, for the remainder of this manuscript, we have opted to refer to the collected $${V}_{{\rm{Si}}}^{-}$$ emission as V1′.

### Intensity modulation

To verify the influence of the SBD-induced built-in field on V1′ emission, and to provide a means of tuning the bright state of $${V}_{{\rm{Si}}}$$, we apply external (i) forward and (ii) reverse bias to the SBD and study the resulting V1′ PL intensity. Figure 2d showcases representative PL spectra of the proton-irradiated samples with SBD (here for a fluence of $$2\,\times 1{0}^{12}$$ cm$${}^{-3}$$) during sequential zero (black) and forward (red) bias conditions. Solid lines denote first acquisition of a given voltage, and dashed lines the second acquisition (acquisitions with time occurred in the order of the legend). Indeed, an intensity modulation is observed when modifying the electric field via biasing of SBD, confirming the influence of the band bending and charge state manipulation of the bright $${V}_{{\rm{Si}}}^{-}$$ state: emission from the V1′ defect can be selectively switched off (lower intensity) and on (higher intensity) by manipulating the electric field at the interface of the Schottky contact and 4H-SiC. While some variation between diodes and applied voltages exists (see also Supplementary Notes 3), unambiguous evidence of V1′ emission intensity manipulation via the applied voltage is found. The general trend is clear; for a larger ($$>\pm\, 1.5$$ V) forward or reverse bias, the intensity of V1′ is reduced compared to that without applied bias. For low forward bias conditions up to $$\sim\!\! 1$$ V, however, the V1′ intensity can be manipulated to increase compared to the 0 V conditions (we will return to this in a moment). The reproducible electrical modulation of the V1′ intensity is further confirmed in Fig. 2e, showing a series of cyclic acquisitions for two relevant biasing conditions, forward (top panel) and reverse (bottom panel), obtained for a different proton fluence than that of Fig. 2d. Here, it should be noted that only low to moderate electric fields are required. Once the applied bias exceeds approximately $$\pm 5$$ V, the electrically induced modulation of the V1′ emission intensity, demonstrated in Fig. 2d, e, ceases to be predictable and reproducible, with intensities changing in a more random manner. While the exact reasons for this remain unclear, among the most likely are charging effects of defects localized at the interface with the Schottky contact. It is also important to point out that both the enhancement and modulation are observed also at higher temperatures, e.g. 80 and 100 K, although the line width of the V1′ peak increases.

Finally, Fig. 2d, e also demonstrate the defect concentration dependency of our SBD-centered technique. The sample used to create Fig. 2d was irradiated to a proton fluence twice that of the sample shown in Fig. 2e, which is visualized in the enhanced modulation depth of over $$45 \%$$ in 2d as compared to a $$15 \%$$ modulation in Fig. 2e.

### Identifying charge state transitions of the silicon vacancy

To explain the switching demonstrated above, the accessible $${V}_{{\rm{Si}}}$$ charge states must be established, including the energy level transitions. Figure 3 displays the formation energy diagram for $${V}_{{\rm{Si}}}$$ as calculated using hybrid density functional theory, where the red and blue lines represent hexagonal and pseudo-cubic $${V}_{{\rm{Si}}}$$ configurations, respectively. Evidently, $${V}_{{\rm{Si}}}$$ is electrically active, with thermodynamic ($$0/-$$) transition levels located close to mid-gap for both $${V}_{{\rm{Si}}}$$ configurations, ($$-/2-$$) at $${E}_{{\rm{c}}}-0.6$$ eV for both $${V}_{{\rm{Si}}}$$($$k$$) and $${V}_{{\rm{Si}}}$$($$h$$), and ($$2-/3-$$) at $${E}_{{\rm{c}}}-0.4$$ eV for $${V}_{{\rm{Si}}}$$($$k$$) and $${E}_{{\rm{c}}}-0.3$$ eV for $${V}_{{\rm{Si}}}$$($$h$$). Note the predicted stability of the triply negative charge state for both the $$h$$ and $$k$$ configurations, $${V}_{{\rm{Si}}}^{3-}$$, the presence of which has previously been subject to some controversy.9,25 The calculations presented in Fig. 3 indicate that $$q=0$$, $$2-$$ and $$3-$$ are likely candidates for the so-called dark states accessed during the electrical modulation of $${V}_{{\rm{Si}}}^{-}$$ emission demonstrated above (Fig. 2), and provide upper and lower bounds for the stability region of the negative silicon vacancy.

Deep level transient spectroscopy (DLTS) is a capacitance spectroscopy technique enabling both direct observation of defect charge state transitions as well as extraction of their energetic positions within the band gap. Unfortunately, the quantum-compatible defects in 4H-SiC ($${V}_{{\rm{Si}}}$$, $${V}_{{\rm{Si}}}{V}_{{\rm{C}}}$$, $${{\rm{C}}}_{{\rm{Si}}}{V}_{{\rm{C}}}$$) lack reliable identification of their thermodynamic charge transition levels, rendering the dark states generated during both electrical and optical charge state control experiments uncertain. DLTS spectra of irradiated n-type 4H-SiC samples are presented in Fig. 4a and show two main carrier traps in the vicinity of the conduction band edge: the Z$${}_{1/2}$$ double acceptor level arising from the ($$0/2-$$) charge state transition of the carbon vacancy ($${V}_{{\rm{C}}}$$),35 and the S-center consisting of two contributions (S1 and S2) located at 0.4 and 0.7 eV below the conduction band minimum (CBM), respectively. S1 and S2 arise from different charge state transitions of the same defect, and have been tentatively attributed to $${V}_{{\rm{Si}}}$$ following theoretical calculations.25 DLTS measurements occur under conditions where the defect can relax fully to its equilibrium configuration after the charge state transition. For this reason, the activation energy for carrier emission from a defect extracted from DLTS should be compared with thermodynamic charge state transition levels,36 i.e., those indicated in Fig. 3. However, the activation energies obtained by DLTS may also include a capture barrier, which can be sizable in some cases. An upper estimate for this barrier can be obtained by constructing a one-dimensional configuration coordinate diagram for the transition, as explained in refs. 37,38, i.e., the activation energies for $${V}_{{\rm{Si}}}$$ observed by DLTS are predicted to occur within the highlighted ranges in Fig. 3. Here, we observe excellent overlap between the DLTS-deduced activation energies for the S-center (Fig. 4a) and the $${V}_{{\rm{Si}}}$$($$-/2-$$) and $${V}_{{\rm{Si}}}$$($$2\!-/3-$$) charge state transitions obtained from Fig. 3, and attempt to prove that the S-center indeed arises from $${V}_{{\rm{Si}}}$$.

Interestingly, the S1 DLTS peak accommodates contributions from two distinct defect centers,39 as revealed by the Laplace-DLTS spectra (see Supplementary Methods 2 for details) in Fig. 4b. Recently, Z$${}_{1/2}$$ was also found to contain two distinct signals, which were assigned to the $$h$$ and $$k$$ configurations of the carbon vacancy.40 Similarly, we infer from Fig. 3 that the $$h$$ and $$k$$ $${V}_{{\rm{Si}}}$$($$2\!-/3-$$) charge state transitions likely have an energy level position difference of up to 0.1 eV. The temperature-dependent Laplace-DLTS signal in Fig. 4b of the S1 peak, and the Arrhenius plot in Fig. 4c, evidence that the two individual S1 contributors are separated in energy by 0.04 eV. Accordingly, we assign the two defect centers encompassed by S1 to $${V}_{{\rm{Si}}}$$($$h$$) and $${V}_{{\rm{Si}}}$$($$k$$), and make a tentative assignment of S1(peak 1) and S1(peak 2) to the ($$2\!-/3-$$) transitions of $${V}_{{\rm{Si}}}$$($$k$$) and $${V}_{{\rm{Si}}}$$($$h$$), respectively. In contrast to what is often found for Z$${}_{1/2}$$,40 the two contributions to the S1 defect center have approximately equal integrated intensities. This is as expected for proton-irradiated material, with the $$h$$ and $$k$$ $${V}_{{\rm{Si}}}$$ configurations formed by displacement caused by the nuclear energy deposition.

Comparing the expected behavior of $${V}_{{\rm{Si}}}$$ and S-center, we find a striking similarity (see also Supplementary Discussion 1); the S-center only appears in irradiated n-type material, and anneals out between 400 and 600 °C.41,42 Coincidentally, the $${V}_{{\rm{Si}}}$$ is a metastable defect in 4H-SiC, transforming into $${{\rm{C}}}_{{\rm{Si}}}{V}_{{\rm{C}}}$$ within the same temperature range in n-type material.14 The calculated barrier for $${V}_{{\rm{Si}}}$$ transforming into $${{\rm{C}}}_{{\rm{Si}}}{V}_{{\rm{C}}}$$ is 1.8 eV,43 which is identical to the experimentally deduced barrier for S-center annealing.44 At these temperatures, self-interstitials should already have annealed out,45 while the carbon vacancy remains present and becomes mobile at significantly higher temperatures,46 eliminating these defects as contenders for the S-center source. Furthermore, the absence of the Poole–Frenkel effect for S1 indicates an acceptor-like behavior, and the difference of more than an order of magnitude between the capture cross-sections for S1 and S2 is well explained by the large electron repulsion associated with $${V}_{{\rm{Si}}}^{2-}$$ capturing an additional electron.44 In conclusion, the excellent agreement between calculated and experimental $${V}_{{\rm{Si}}}$$ and S-center properties provide compelling evidence for the assignation of the $${V}_{{\rm{Si}}}$$($$-/2-$$) and $${V}_{{\rm{Si}}}$$($$2\!-/3-$$) charge state transitions to generate the S2 and S1 signals, respectively, and indicate these transitions as accomplices in reducing the single-photon count from $${V}_{{\rm{Si}}}$$.

### Proton fluence dependence of the S-center

To unambiguously attribute the DLTS S-center to $${V}_{{\rm{Si}}}$$, and thereby provide experimental verification of the upper boundary for the Fermi level where $${V}_{{\rm{Si}}}^{-}$$ and hence single-photon emission prevails, we relate the DLTS S-center to PL emission from the V1 center. Figure 5a demonstrates a linear dependence of S-center concentration41 in blue (and $${V}_{{\rm{C}}}$$ in pink) on proton irradiation fluence, as expected for primary point defects. Note that the proton fluence range reflects the detection limits of the DLTS technique, where the defect concentration cannot exceed $$20 \%$$ of net carriers. All defect concentrations were estimated assuming uniform defect concentration profiles within the depletion region as justified by Fig. 2c, and simulated due to overlapping peaks in the 4H-SiC DLTS spectrum (see Supplementary Discussion 2 for details). The slight difference between S1 and S2 concentrations is attributed to the overlap between the S2 and Z$${}_{1/2}$$ peaks (see Fig. 4a). Figure 5a also compares experimentally deduced S-center concentrations to those estimated using SRIM simulations (using displacement energies of 20 eV and 30 eV for C and Si, respectively), with simulated concentrations depicted as red open squares for $${V}_{{\rm{C}}}$$ and black open triangles for $${V}_{{\rm{Si}}}$$. An excellent agreement is found between the experimentally deduced S-center concentration and that estimated for $${V}_{{\rm{Si}}}$$ using the SRIM code, using the well known and ever-present $${V}_{{\rm{C}}}$$ as a benchmark.

### Correlating the S and V1 centers

Figure 5b correlates the proton fluence dependence of the S-center concentration (fit to experimental data in blue extended from Fig. 5a) and V1/V1′ emission intensity (green). The V1/V1′ intensities were determined after baseline subtraction, and the deviation from a linear fit for the largest fluences is partly attributed to the strong compensation resulting in a substantial shift in the Fermi level. The match in slope between the S1/S2 and V1/V1′ linear fits is excellent, and provides strong support for the optical V1/V1′ signals and the electrical S1/S2 signals having the same origin: the silicon vacancy.

To summarize, we combine DFT calculations with DLTS and PL measurements to assign the S1 and S2 DLTS peaks to the ($$-/2-$$) and ($$2\!-/3-$$) charge state transitions of the silicon vacancy in 4H-SiC, respectively. Hopefully, the newfound electrical degree of freedom provided by the DLTS technique will yield enhanced control over both $${V}_{{\rm{Si}}}$$ formation and placement, and the relation between bright and dark charge states. Indeed, we have identified two new accessible charge states for $${V}_{{\rm{Si}}}$$ in 4H-SiC: the doubly and triply negative, and thus experimentally provided an upper bound for the bright $${V}_{{\rm{Si}}}^{-}$$.

### Field effect on band bending

The strong enhancement of the V1′ signal under the SBD indicates that emission arises from the depletion region of the junction, and is related to the electric field or the current provided by the junction. However, no electroluminescence has so far been observed, and the strong enhancement also occurs without applied bias. Thus, one can rule out enhancement of the emission by impact excitation47 as the only cause for the increased V1′ emission, i.e. that charge carriers are accelerated in the electric field and cause excitation resulting in V1′ emission when interacting with $${V}_{{\rm{Si}}}$$. Hence, the manipulation of the charge states by the depletion region appears as an important factor for the enhanced emission of V1.

Combining the optical and electrical observations above, we can consider the field-induced switching of $${V}_{{\rm{Si}}}^{-}$$ luminescence shown in Fig. 2 with respect to the charge state transitions: $${V}_{{\rm{Si}}}$$($$-/2-$$) at $${E}_{{\rm{C}}}-0.7$$ eV, and $${V}_{{\rm{Si}}}$$($$2\!-/3-$$) at $${E}_{{\rm{C}}}-0.4$$ eV. First, consider the band diagram at temperatures above the freeze-out of the main dopant, so that thermally excited charge carriers are still available, i.e., above $$\sim\!\! 50$$ K in nitrogen doped 4H-SiC. As illustrated in Fig. 6a for a temperature of 100 K, the Fermi level in n-type 4H-SiC, having carrier concentrations in the $$\sim\!\! 1{0}^{15}$$ cm$${}^{-3}$$ range or above, is situated $$\lesssim\! 0.1$$ eV below the conduction band edge, or lower. Therefore, at 80 K or above, $${V}_{{\rm{Si}}}$$ predominantly inhabits the triply negative charge state, with the doubly and singly negative charge states mainly being available through illumination.

Applying a SBD causes band bending in the near surface region, as illustrated in the technology computer-aided design (TCAD) simulation shown in Fig. 6b (further details on the temperature- and voltage dependence can be found in Supplementary Methods 3). The blue colored region in Fig. 6b indicates where $${V}_{{\rm{Si}}}^{-}$$ is predominantly populated. Importantly, at room temperature and zero bias, the depletion region provides conditions where $${V}_{{\rm{Si}}}^{-}$$ is the prevailing charge state, and likely explains the enhancement of the V1′ emission demonstrated in Fig. 2b.

Although not directly transferable to the non-equilibrium situation of carrier injection established by external bias and illumination, the conceptual band model presented in Fig. 6 hints at which charge state transitions are occurring during the electrically induced V1′ modulation of Figs. 2d, e. Under forward biasing, we approach flat-band conditions. The resulting lowering of the V1′ intensity demonstrated in Fig. 2d likely results from transitions between the singly negative and the $$2-$$ and $$3-$$ charge states of $${V}_{{\rm{Si}}}$$, occurring from the deep end of the depletion region. Furthermore, we speculate that the enhancement of V1′ PL intensity shown in Fig. 2e may be explained by a transition from neutral to negative $${V}_{{\rm{Si}}}$$ in the near surface region when increasing the voltage slightly. The $${V}_{{\rm{Si}}}$$($$0/-$$) transition is expected at 1.3–1.5 eV above the valence band edge (Fig. 3), but this has not been experimentally verified.

### Stark shift of the V1′ line

The SBDs also provide opportunities to study the $${V}_{{\rm{Si}}}$$ emission under larger electric fields. Although the intensity modulation of the V1′ PL peak is no longer accurately predicted for applied voltages $$>\pm\! 5$$ V in our samples, we observe a significant shift in the energy positioning of the V1′ ZPL for reverse biasing $$>10$$ V. Figure 7a demonstrates the effect of large electric fields on V1′ emission for a sample irradiated to a proton fluence of $$1\times 1{0}^{12}$$ cm$${}^{-3}$$. Interestingly, the full width half maximum (FWHM) of the V1′ peak is consistent as the field increases, although shifted. Thus, one can conclude that a majority of the emitting $${V}_{{\rm{Si}}}$$ centers is affected by the electric field, confirming that V1′ emission mainly arises from defects within the depletion region of the SBD. Electrically induced shifting or splitting of spectral lines is a phenomenon commonly known as the Stark effect,48 and would explain the observed continuous red-shift of the V1′ line with increasingly negative applied bias. Forward biasing the sample did not affect the V1′ peak position. The extent of the red-shift exhibits a clear dose dependence, and was also influenced by both the carrier concentration and the depth of the depletion region. Indeed, a stronger Stark effect can be attributed to the individual $${V}_{{\rm{Si}}}$$ defects experiencing stronger local field (see Supplementary Notes 2 for a discussion on how the electric field strength was estimated from the reverse bias and the SBD characteristics).

The shift in V1′ peak position exhibits both quadratic and linear dependences on the applied electric field, as shown in Fig. 7b, regardless of $${V}_{{\rm{Si}}}$$ concentration and carrier concentration. Defects in 4H-SiC, $${V}_{{\rm{Si}}}$$ included, are non-centrosymmetric, and for such defects both linear and quadratic Stark effects take place.49 The $${V}_{{\rm{Si}}}^{-}$$ has C$${}_{3\nu }$$ ground state symmetry, and the V1′ transition is between the $${}^{4}{\rm{E}}$$ excited and $${}^{4}{{\rm{A}}}_{2}$$ ground states.19 This transition is analogous to that of the negatively charged NV center in diamond, for which the quadratic Stark effect was previously demonstrated.50 At the moment, the reason for the quadratic Stark shift of the V1′ ZPL remains an open question.

Stark tuning has previously been demonstrated for the divacancy in 4H-SiC,26,28 but not for the the silicon vacancy. Consequently, we herein provide a means of tuning the $${V}_{{\rm{Si}}}$$-related emission energy, while simultaneously establishing that the V1′ excited state of $${V}_{{\rm{Si}}}$$($$h$$) seems to be more robust towards stray electric fields than, e.g., the $$hh$$ configuration of the divacancy.28

## Discussion

In summary, we characterize the electric field response of optical emission from $${V}_{{\rm{Si}}}$$ ensembles, and find that both a substantial intensity increase as well as controlled modulation of V1′ emission are obtainable using highly accessible techniques and voltages. By correlating the PL and DLTS responses of $${V}_{{\rm{Si}}}$$ and identifying the DLTS S-center, we identify thermodynamic transition levels of a solid-state qubit candidate, and provide an additional means of detecting and controlling the $${V}_{{\rm{Si}}}$$ in 4H-SiC. Having established upper and lower bounds for the Fermi levels ensuring optimal $${V}_{{\rm{Si}}}^{-}$$ charge state populations, our work promises greater ease of ensuring that all silicon vacancies inhabit the bright state. The results presented herein for charge state modulation of $${V}_{{\rm{Si}}}$$ in n-type 4H-SiC apply to a defect ensemble, and we are therefore unable to completely switch the $${V}_{{\rm{Si}}}^{-}$$ luminescence ON and OFF by manipulating the defect charge state. However, in the event of a single $${V}_{{\rm{Si}}}$$ defect being situated at a suitable distance from a Schottky contact, applying external bias is a promising approach to selectively alter the $${V}_{{\rm{Si}}}$$ charge state and effectively switching the quantum-compatible state ON and OFF. In that event, the challenge becomes placing a $${V}_{{\rm{Si}}}$$ within a highly localized and easily identifiable depletion region, which can be solved by, e.g, depositing a SBD on top of a nanopillar containing only one or two silicon vacancies.22

Recently, electric field-dependent manipulation of single silicon vacancies was demonstrated using the intrinsic region of 4H-SiC p-i-n diodes.51 In the intrinsic region, the Fermi level is close to the middle of the band gap, and switching may occur between the neutral and single negative charge state. In n-type material, on the other hand, the Fermi level is close to the conduction band with $${V}_{{\rm{Si}}}$$ predominantly in the $$2-$$ or $$3-$$ charge states. Hence, the charge states affected by the depletion region will be closer to the metal–semiconductor interface compared to that of the p-i-n diode.

Finally, we reinforce the robustness of the V1 defect center ZPL with respect to stray electric fields by demonstrating a Stark shift that is much smaller than the splitting between the V1 and V1′ excited states. Although electric fields above $$2\,\times 1{0}^{4}$$ V$$/$$cm are needed to shift the V1′ peak position, voltages below $$\pm\! 5$$ V can subdue or enhance the intensity by over $$40 \%$$. Combined with the strong sensitivity of the $${V}_{{\rm{Si}}}$$ electron spin to magnetic fields,52 we cement the position of $${V}_{{\rm{Si}}}^{-}$$ in 4H-SiC as a promising quantum sensor with nanoscale resolution, employing V1′ intensity for low-field and V1′ peak position for high-field applications. Combined with nanofabrication, the SBD approach presents a powerful tool and paves the way towards obtaining complete control of, and drastically enhanced emission from, $${V}_{{\rm{Si}}}$$ defect ensembles in 4H-SiC highly suitable for quantum applications.

## Methods

### Computational details

First-principles calculations were performed within density functional theory, as implemented in the Vienna ab-initio simulation package (VASP),53,54,55,56 using the HSE06 hybrid functional57 to accurately describe the electronic structure and the Projector-Augmented Wave (PAW) method to consider valence electrons only.58 The calculated 4H-SiC 0 K band-gap of 3.17 eV is close to the experimental value of 3.27 eV,59 lending support to the calculated charge state transitions. The $${V}_{{\rm{Si}}}$$ was created by removing a Si($$h$$) or Si($$k$$) atom from a 96-atom cubic 4H-SiC supercell. The electronic self-consistent energy was minimized to a numerical accuracy of $$1{0}^{-6}$$ eV, while atomic coordinates were optimized until forces were below $$0.02\,{\rm{eV}}/\AA$$. A $$2\,\times 2\,\times 2$$ Monkhorst-Pack type k-mesh and a 420 eV plane-wave energy cut-off were deemed sufficient for capturing defect energetics accurately. Defect formation energies and thermodynamic charge state transition levels were calculated by using the established formalism described in ref. 36 For charged defects, the extended60 Freysoldt, Neugebauer, and Van de Walle correction scheme60,61,62 was employed.

### Sample preparation

The $${V}_{{\rm{Si}}}$$ was studied experimentally using ($$0001$$) 4H-SiC samples purchased from Cree, Inc. holding $$10\ \mu {\rm{m}}$$ thick epitaxial layers with net doping concentrations of $${N}_{{\rm{D}}} \sim 1\times 1{0}^{15}{{\rm{cm}}}^{-3}$$, as determined from capacitance-voltage measurements. The substrates are n-doped with a nominal concentration of $$8\,\times 1{0}^{18}$$ cm$${}^{-3}$$. To selectively form the $${V}_{{\rm{Si}}}$$ defects, the samples were irradiated at room temperature with 1.8 MeV protons, having a projected range of $$\sim\!\! 27\ \mu {\rm{m}}$$ calculated using collision Monte Carlo models as manifested in the SRIM code,34 while being tilted $$\sim {8}^{\circ }$$ off with respect to the surface normal to reduce channeling effects. Proton irradiation was performed to fluences ranging from $$1\,\times 1{0}^{11}$$ to $$8\,\times 1{0}^{13}\ {{\rm{cm}}}^{-2}$$ to enable detection using both DLTS (with an upper defect concentration limit of $$0.2{N}_{{\rm{D}}}$$) and PL spectroscopy (our setup has a lower $${V}_{{\rm{Si}}}$$ detection limit in the $$1{0}^{13}\ {{\rm{cm}}}^{-3}$$ range). Following irradiation, circular nickel (Ni) contacts having 1 mm diameter and 150 nm thickness were deposited on the epitaxial-layer surface using an electron-beam evaporator to form SBDs. To alleviate implantation damage and reduce the concentration of metastable peaks appearing in the temperature region relevant for DLTS measurements,63,64 all samples were annealed at 300 °C in air for 30 min using a conventional tube furnace.

### PL spectroscopy and field-dependent intensity modulation

For the PL spectroscopy the samples were placed inside a close-cycled He refrigerator system (CCS-450 Janis Research, Inc.), and the samples were measured at temperatures ranging from 10 to 300 K. Sample excitation was employed using a pulsed Ti sapphire tunable laser operating in a femtosecond mode-locked mode and utilizing an excitation wavelength of $$740\ {\rm{nm}}$$. The emission was analyzed by a fiber-optic (Ocean Optics, HR4000) and imaging spectrometer systems (Horiba iHR320 coupled to Andor iXon888 EMCCD), with a spectral resolution below 0.2 nm in both cases. Positive and negative bias was applied to the SBD being addressed by individual wires attached to the Ni contact by conductive glue, and the luminescence modulation was investigated at temperatures ranging from 10 to 100 K and with laser intensities of 25 and 250 mW, which correspond to $$\sim\!\! 100$$ W/cm2 and $$\sim\!\! 1$$ kW/cm2 intensities for a given diameter of the excitation beam spot on the sample of $$\sim\!\! 200\mu$$m.

### Defect identification

Electrical characterization in the form of DLTS was performed in the 77–370 K temperature range to encompass both the S1 and S2 peaks, with the scans starting at low temperature. The reverse bias was kept at $$-10$$ V using a 10 V filling pulse. Rate windows in the range 20–640 $${\rm{ms}}$$ and a standard lock-in weighting function were used to extract the DLTS signal. Optical characterization to obtain correlation with DLTS measurements was performed at 10 K using the PL setup described above with a 25 mW excitation intensity and a wavelength of $$740\ {\rm{nm}}$$.

SRIM simulations were performed to provide an estimate for the $${V}_{{\rm{Si}}}$$ concentration by comparing to that known for $${V}_{{\rm{C}}}$$. For the simulations, we used 20 eV (30 eV) for the C (Si) displacement energy, and for the post-processing we estimated that $$3 \%$$ of all vacancies (both silicon and carbon) survive dynamic annealing during ion implantation and the 300 $${}^{\circ }$$C post-irradiation anneal.

### Device simulations

Based on TCAD simulations using Sentaurus Device from Synopsys, the Schottky diode was investigated regarding its electrical behavior. A simplified structure including the most important physical models for 4H-SiC was used to replicate the diode’s response to various conditions such as the external bias. The simulations were performed for $$T=100$$ K and $$T=300$$ K.

## Data availability

The data that support the findings of this study are available from the corresponding author upon reasonable request.

## Code availability

The code used to analyze the results presented in this paper will be made available from the corresponding author upon reasonable request.

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## Acknowledgements

The authors would like to sincerely thank the late Professor Bengt G. Svensson for all the enlightening discussion and support, and for initiating the work presented herein. Financial support was kindly provided by the Research Council of Norway and the University of Oslo through the frontier research project FUNDAMeNT (no. 251131, FriPro ToppForsk-program), and the Norwegian Micro- and Nanofabrication Facility (NorFAB 245963). The computations were performed on resources provided by UNINETT Sigma2—the National Infrastructure for High Performance Computing and Data Storage in Norway. J.C. thanks the Fundação para a Ciência e a Tecnologia (FCT) for support under project UID/CTM/50025/2019, co-funded by FEDER funds through the COMPETE 2020 Program. J.C. also acknowledges support by the NATO SPS programme (Project No. 985215).

## Author information

Authors

### Contributions

M.E.B. and Y.K.F. performed the calculations. M.E.B, L.V., A.G., and B.G.S. designed the experiments; M.E.B., A.G., and H.M.A performed the experiments. J.M. and U.G. performed the device simulations. All authors analyzed the data and wrote the manuscript.

### Corresponding author

Correspondence to M. E. Bathen.

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Bathen, M.E., Galeckas, A., Müting, J. et al. Electrical charge state identification and control for the silicon vacancy in 4H-SiC. npj Quantum Inf 5, 111 (2019). https://doi.org/10.1038/s41534-019-0227-y

• Accepted:

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