Ensembles of negatively charged nitrogen vacancy centers (NV-) in diamond have been proposed for sensing of magnetic fields and paramagnetic agents, and as a source of spin-order for the hyperpolarization of nuclei in magnetic resonance applications. To this end, strongly fluorescent nanodiamonds represent promising materials, with large surface areas and dense ensembles of NV-. However, surface effects tend to favor the less useful neutral form, the NV0 centers, and strategies to increase the density of shallow NV- centers have been proposed, including irradiation with strong laser power [1]. Here, we study the fluorescence properties and optically detected magnetic resonance (ODMR) of NV- centers as a function of laser power in strongly fluorescent bulk diamond and in nanodiamonds obtained by nanomilling of the native material. In bulk diamond, we find that increasing laser power increases ODMR contrast, consistent with a power-dependent increase in spin-polarization. Conversely, in nanodiamonds we observe a non-monotonic behavior, with a decrease in ODMR contrast at higher laser power. We hypothesize that this phenomenon may be ascribed to more efficient NV- → NV0 photoconversion in nanodiamonds compared to bulk diamond, resulting in depletion of the NV- pool. A similar behavior is shown for NDs internalized in macrophage cells under the typical experimental conditions of imaging bioassays. Our results suggest strong laser irradiation is not an effective strategy in NDs, where the interplay between surface effects and local microenvironment determine the optimal experimental conditions.
Research Article
Divergent Effects of Laser Irradiation on Ensembles of Nitrogen-vacancy Centers in Bulk and Nano-diamonds: Implications for Biosensing
https://doi.org/10.21203/rs.3.rs-1343505/v1
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nanodiamonds
polarization
nitrogen-vacancy centers
bulk diamond
spin dynamics
charge dynamics
charge stability
photoconversion
nanomilling
13C
cells
Negatively charged Nitrogen-Vacancy centers (NV-) can be used as probes for ultrasensitive detection of magnetic [2–4] and electric fields [5–7], temperature [8,9], as well as electron and nuclear spins at the nanoscale [10,11]. NV- centers can be optically polarized and readout with irradiation of laser light at room temperature and at the Earth’s magnetic field [12–14], thus enabling applications in biomedical assays [15–18], including intracellular thermometry [8,19,20], optical magnetic imaging in living cells [3,21,22] or optical magnetic detection of single-neuron action potentials [23,24]. Moreover, optical pumping of NV- centers has been proposed as an alternative to dynamic nuclear polarization (DNP) for the hyperpolarization of nuclear spins inside or outside the diamond lattice [25–27].
These applications rely on ensembles of NV- centers in the vicinity of the diamond surface [28,29]. Due to their large surface area, NV-rich fluorescent nanodiamonds (NDs) are promising candidates for these applications [8,16,22]. Moreover, NDs are biocompatible, and [30–32] can be internalized in living cells, thus probing the microenvironment in subcellular compartments [33,34]. Importantly, their surface can be functionalized to target specific cells or proteins [30–32]. Furthermore, 13C-enrichment of NDs can improve hyperpolarization efficiency, quantum sensing and magnetic resonance signal enhancement [35].
Several techniques have been proposed for the production of NDs, including nanomilling [36] of bulk diamond, detonation [37,38] and high-power laser ablation [39,40]. Detonation NDs tend to be small (5-10 nm) and rich in impurities [37]. High-power laser ablation can produce fluorescent NDs in a single-step process [39,40], but the yield is still insufficient for practical applications. Conversely, nanomilling of bulk diamond makes it possible to control concentration of defects and NV centers, as well as particle size, with good production yield [41].
A larger surface area increases exposure of shallow NV centers to the external environment, thus improving sensitivity and potentially promoting polarization transfer to molecules outside the diamond surface. However, surface effects tend to favor the neutral charge state NV0 [42], which does not present useful spin properties [12–14]. As a result, a larger concentration of NV0 in NDs compared to the starting material is often observed [42].
Laser light used to polarize and interrogate NV- centers can also induce charge conversion between NV- and its neutral form NV0 [28,43–48]. Photoconversion depends on the presence of nitrogen defects and surface acceptor states, and thus both NV- → NV0 and NV0 → NV- photoconversion routes have been observed in different diamond samples [14,44,45]. Recently, we have shown that increasing laser power can substantially enhance the availability of shallow NV- in nanostructured, 15N-implanted ultrapure CVD diamond [1]. However, it is unclear whether a similar strategy may be advantageous in NDs, and here we test this hypothesis in NDs of various sizes obtained by nanomilling of highly-fluorescent 13C-enriched diamond. Fluorescence spectra and optically detected magnetic resonance (ODMR) spectra were acquired at different laser powers for NDs of 156 nm and 48 nm, and for the native bulk diamond, as a direct comparison. Additionally, we internalized NDs in macrophage cells to study the effects of laser power under the typical conditions of a bioassay and in the cellular environment. Experiments were performed with a house-built wide-field microscope at sub-micrometric spatial resolution (1 pixel corresponding to 160 nm) to account for the intrinsic heterogeneity in NDs behavior and to study the microenvironment in different cellular compartments. Our findings highlight the importance of surface effects on photoconversion and provide useful information on the optimization of experimental conditions for biosensing or polarization transfer applications involving fluorescent NDs.
Samples
Bulk 13C-enriched diamond grown by the high-pressure, high-temperature (HPHT) technique was acquired from ElementSix. These samples have a concentration of NVs of ≈10 ppm, and 13C enrichment ranged from 5 to 10% (≈5 * 104 - 105 ppm), depending on the position within the diamond stone; concentration of substitutional nitrogen (P1 centers) was approximately 200 ppm. The fraction of 13C was provided by the vendor, while the concentrations of nitrogen and NV centers were estimated through spectroscopic measurements on the bulk diamond before milling [28]. Attrition milling was used to prepare samples with varying size distribution with a procedure adapted from [49]. The whole process is exemplified in Fig. 1a. The sample material (62 mg) was added to a stainless-steel milling cup, which was filled up to one third of its height with 5 mm diameter stainless steel milling balls. The bottom third of the milling cup was then filled with isopropanol that had been dried using molecular sieve. The sample was milled for six hours at 50 swings per second. At the end of the process, the sample contained a significant amount of metallic debris caused by the milling. To clean the diamond material, the sample was flushed out of the milling cup with distilled water into a 250 ml round bottom flask. The remaining steel balls were removed using a magnet. To dissolve metallic impurities, 50 ml of concentrated hydrochloric acid was added. The mixture was stirred overnight at room temperature. After settling, the supernatant was decanted and 50 ml 96% of sulfuric acid was added. The resulting mixture was heated to 120 °C bath temperature without a reflux condenser to remove any remaining isopropanol. After one hour, a reflux condenser was attached to the flask and 20 ml of nitric acid (65%) slowly added while monitoring the reaction mixture carefully to prevent a violent reaction. It is important to note that any remaining isopropanol might violently react with concentrated nitric acid, thus it is important to remove it carefully before adding HNO3! The solution was stirred overnight at 120 °C. After the solution had cooled down to room temperature, the supernatant acid mixture was removed using a pipette and the solution was transferred to centrifugation tubes. To wash the diamond material, centrifugation at 15000 rpm was used over one hour to settle the diamond material at the bottom. The supernatant was removed and replaced with distilled water. The diamond material was then dispersed using sonication. This process was repeated until the supernatant showed a neutral pH. After reaching neutral pH, centrifugation was used to separate the particles by size. Two fractions were selected, corresponding to the biggest and the smallest particles in the suspension, and their size distribution measured using dynamic light scattering (DLS), giving a median value of the volume distribution (D50 value) of 156 nm and 48 nm, respectively. NDs were suspended in deionized water and stored in glass vials. Data of DLS and scanning electron microscopy can be found in the Supplementary Material.
Prior to the FL and ODMR experiments, suspensions of NDs were sonicated, and 10 µL were deposited either on a circular glass slide or in an Ibides (Ibidi GmbH, Planegg/Martinsried, Germany) and allowed to dry. In a separate set of experiments, NDs were internalized into cells following the procedure described below.
Cell line
Murine (RAW 264.7) cell line was purchased from American Type Culture Collection (ATCC LGC Standards, Sesto San Giovanni, Italy) and cultured in DMEM supplemented with 10% (v/v) of fetal bovine serum (FBS), 2 mM L-glutamine, 100 U/mL penicillin and 100 μg/mL streptomycin at 37 °C in a humidified atmosphere with 5% CO2.
In vitro NDs uptake experiments
For uptake experiments, RAW 264.7 cells were seeded in an Ibidi at a density of 3 × 104 cells/ well and incubated at 37° C for 24 h, to allow them to adhere to the slide surface. Incubation of cells with NDs (size 156 nm and 48 nm) was performed for 24 h at 37 °C in a humidified atmosphere with 5% CO2. At the end of the incubation, cells were washed three times with phosphate buffered saline (PBS) and fixed in 4% paraformaldehyde (PAF) at room temperature for fifteen minutes.
Confocal microscopy
Cells were rinsed twice with PBS and permeabilized with 0.1 % Triton in PBS for ten minutes. Actin filaments were stained with phalloidin fluorescein isothiocyanate (FITC) (Sigma) for thirty minutes at room temperature. After washing twice with PBS, nuclei were counterstained with 4′,6-diamidino-2-phenylindole (DAPI). Coverslips were mounted with a glycerol/water solution (1/1, v/v). Observations were conducted under a confocal microscopy (Leica TCS SP5 imaging system) equipped with an argon ion and a 561 nm DPSS laser. Cells were imaged using a HCX PL APO 63×/1.4 NA oil immersion objective. NDs were excited by 561 nm laser, while the emission was collected in the 570–760 nm spectral range. Phalloidin was imaged using 458 nm laser and the emission collected in the 498-560 nm range. DAPI was imaged using 405 nm laser and the emission was collected in the 415-498 nm range. Image analysis was performed using ImageJ software.
FL and ODMR experimental setup
Full fluorescence spectra of the NVs were acquired with a confocal microRaman setup (LabRam Aramis, Jobin-Yvon Horiba), equipped with a DPSS laser (532 nm) and an air-cooled multichannel CCD detector in the window range between 535 nm and 935 nm.
Wide-field ODMR imaging was performed with a modified Nikon Ti-E inverted wide-field microscope [Fig. 1b,c] equipped with a microwave channel and a high-sensitivity CMOS camera (Hamamatsu ORCA-Flash4.0 V2) [40]. A 532 nm continuous-wave laser (CNI laser, MGL-III-532/50mW) was used as excitation source, delivering on the sample a power of ~30 mW through a 40X (NA=0.75 and working distance of 0.66 mm) refractive objective. The laser power was modulated by inserting neutral density filters on the optical path. To avoid backscattering of laser light, we used a custom made dichroic beamsplitter. FL was collected in a spectral window ranging from 590 to 800 nm.
The microwave (MW) field source was a WindFreak MW generator (SynthHD v1.4 54MHz-13.6GHz); the signal was amplified by a Mini-Circuits ZVE-3W-83+ 2W amplifier. The MW irradiation was delivered to the sample through a MW single loop terminated with a high-power MW damper.
The temporal sequence of the experiment (camera acquisition and MW delivery) was controlled by a SpinCore 100 MHz TTL generator (Model: TTL: PB12-100-4K). Finally, the image acquisition was processed with the Nikon NIS-Elements Advanced Research software and analyzed with Fiji software.
The home-built instrument used for these experiments makes it possible to extract ODMR spectra pixelwise with sub-micrometric spatial resolution, thus enabling analysis of heterogeneously distributed samples. Indeed, the deposition procedure can result in a non-uniform distribution of NDs, with region-dependent concentration and size of aggregates. NDs uptake from cells is also inhomogeneous, and cells with varying amount and clustering of NDs inside were observed.
ODMR technique description
This modified wide-field microscope was used to perform spatially-resolved continuous wave ODMR (CW-ODMR), a technique that probes the sublevel structure of the ground state. Hence, ODMR spectra are sensitive to changes in level structure induced by external magnetic or electric fields, interactions with paramagnetic substances or temperature. ODMR is therefore useful to exploit the sensing properties on NV- centers in diamond.
Fig. 2 a,b,c show the fluorescence (FL) spectra from the bulk diamond, the 156 nm and the 48 nm NDs. Each NV charge state is characterized by its fluorescence spectrum, with zero-phonon lines (ZPL) at 575 nm and 638 nm for the NV0 and NV-, respectively. In addition, a phonon sideband, peaked around 620 nm for the NV0 and 700 nm for the NV-, is observed, extending up to ≈ 850 nm in both cases. The FL spectra are normalized to the NV- ZPL for comparison. Moreover, NDs showed a larger component from the NV0s with respect to the bulk diamond (represented as black and light red curves, respectively). This is consistent with the idea that surface effects favor the NV0 centers [45,50], thus affecting the relative concentration of the different charge states.
Fig. 2 d,e,f show the ODMR spectra of the bulk diamond and NDs at different laser powers (from 1 to 30.5 mW) at constant MW power of 15 dBm. The ODMR spectra show the NV- central lines (AL and AR) and two side bands (BL and BR), the latter related to the hyperfine interaction between the NV- spins and the 13C nuclear spins [51]. The 13C sidebands are separated from each other by ~130 MHz, consistently with previously reported values [35,51–54]. For all samples, the linewidth of the resonance bands decreases with laser power, in agreement with the line-narrowing effect described by Jensen et al. [55]. Alongside with the increase in signal-to-noise (SNR) ratio, this phenomenon improves resolution of the NV- strain-split doublet (central dips AL and AR). We did not observe any detectable temperature effect on the position of the ODMR resonance that may be caused by absorption of MW or laser power [5].
In bulk diamond, a monotonic increase in ODMR contrast with laser power was observed, consistent with increasing NV- polarization levels [Fig. 2d and 3a]. Contrast was calculated as the mean value from the central resonances AL and AR. Interestingly, in NDs, a non-monotonic behavior was observed, as shown in Fig. 3 b,c. Up to 8.1 mW of laser power the ODMR contrast increases. At the highest power levels, the trend is the opposite, with a decrease in contrast systematically observed in different sample regions and for both ND sizes [Fig.3 b,c].
In principle, a reduction of the ODMR contrast in NDs observed at the highest laser power might result from the competition between optical and MW irradiation. We note that all experiments were performed at constant MW power, while laser power was varied. As a result, at the highest laser power, the spin system may be optically repolarized, with a net decrease in the observed ODMR contrast. However, this does not appear to be the case in this set of experiments. Indeed, the opposite effect is observed in the native bulk material, which has the same composition and concentration of nitrogen as the NDs, and was studied under identical experimental conditions. Moreover, the laser power density in our experiments is very low (up to 3μW/mm2), and far from saturation at the MW power used. This is orders of magnitude smaller than laser power saturation levels previously reported [56,57].
A practical difficulty in assessing the properties of ensembles of NDs is the large variability of the optical response in heterogeneous samples [42,58–60]. This has been ascribed to inter-aggregate interactions, size distribution and different efficiency in NV center initialization in ND aggregates [60]. To circumvent this problem, we resorted to use a wide-field fluorescence microscope to spatially resolve ODMR spectra in different parts of the sample. The heterogeneity in ND deposition is apparent in Fig.3 b,c, where the wide-field FL images clearly show inhomogeneous aggregation and concentration of NDs. Aggregation is particularly evident for the smallest NDs of 48 nm. ODMR contrast in these samples depends on the selected ROIs, characterized by different levels of FL (see caption of Fig. 3), with lower variability observed in the 156 nm NDs compared to the 48 nm NDs. Conversely, the ODMR contrast from the bulk diamond is uniform throughout the image. Despite region and sample dependent contrast, our data show consistent trends for NDs in different samples and ROIs, thus suggesting that the effect here reported is robust and reproducible.
Charge dynamics and spin properties of NVs also depend on the ND microenvironment. To explore the effects described above in a typical bioassay, we incubated the NDs in cell cultures of macrophages (RAW 264.7). Internalization in macrophages is described in the Methods and illustrated by the confocal images of Fig. 4. The composite panel on the right shows the NDs (orange) internalized in the cells, together with the actine filaments (green) and the nuclei (blue), for both 156 nm NDs (top row) and 48 nm NDs (bottom row). The images show that NDs accumulate in the cytoplasm without accessing the nuclei. The cells underwent a rinsing procedure to remove most of the non-internalized NDs that could otherwise contribute with a confounding background emission. Hence, the signals reported in these images correspond to a large extent to internalized NDs.
The concentration of the 48 nm NDs in the native suspension appears to be too low to provide sufficient fluorescence signal after incubation with cells to measure spatially resolved ODMR spectra. Hence, in the following, we focus only on the 156 nm NDs.
In Fig. 5a we show the fluorescence images using ROIs of different size and location in the cell culture incubated with the 156nm NDs. Representative examples of ODMRs curves extracted from single-cell ROIs (~6x6 µm) or cell-aggregates ROI (from ~40x40 µm to ~100x100 µm) are shown in Fig. 5b and Fig. 5c, respectively. Despite some line broadening, compared to the bare NDs, the NV- central bands and 13C sidebands can still be resolved. As in the case of bare NDs, the linewidth of the resonances decreases with increasing laser power, while the SNR increases, therefore improving the resolution of the NV- doublet. Also in this case, we do not observe any variation depending on temperature (i.e., no shift of central resonances), indicating negligible heating by MW absorption by water in the cells or in the biological environment.
Fig. 5d shows the evolution of ODMR contrast with laser power for different ROIs. Interestingly, the ODMR contrast behavior at high laser power is more variable than in the bare NDs of Fig. 3b,c, ranging from a small reduction, to a plateau-like behavior or even a slight increase. We speculate that this wider heterogeneity may be due to differences in the microenvironment, and particularly to the different pH of various cellular compartments (e.g., pH ≈ 5 in lysosomes compared to pH ≈ 7.2 in the cytoplasm).
Indeed, pH can affect the functional groups at the ND oxidized surface (carboxylic acids, ketones, alcohols, esters, etc.), thus changing the properties and charge stability of shallow NV centers [61,62]. At low pH, e.g., carboxylates will be protonated to a much higher extent than under physiological conditions at pH ≈ 7.2, with potential effects on charge state of nearby NV centers. While plausible, this hypothesis requires further investigation.
As a faster method to assess the heterogeneity of the ODMR spectra in cells (Fig. 5 e,f), we set up a simple procedure. Specifically, we acquired two fluorescence images, with MW on- and off- resonance. Taking their difference and then normalizing the fluorescence signals pixelwise, it is possible to reconstruct an ODMR contrast image (Fig. 5g). In these ODMR contrast maps, an average ≈ 4.5% contrast is observed. Moreover, parts with a high (red) and a low (blue) ODMR contrast can be resolved within the cell.
This technique, much faster that the acquisition of the full ODMR spectrum, could prove useful in fast mapping of ODMR, thus paving the way to real-time, spatially resolved imaging of temperature [8,63], magnetic fields [22,31,64] or paramagnetic centers in live-cell bioimaging assays [46,65]. We note that, being based on the ratio between FL levels and not on the absolute FL values, this technique is more affected by noise fluctuations. Here, we applied a 1% contrast threshold in the ODMR contrast mapping to minimize the contributions of undesired spurious signal.
To summarize, we have studied fluorescence and optically detected magnetic resonance in fluorescent NDs obtained by nanomilling and in the native bulk material. A wide-field fluorescence microscope was used to address the problem of a potentially heterogeneous response of NDs within samples.
Our results show markedly different dependencies on laser power for the ODMR contrast in bulk diamond and NDs. While contrast and NV- spin polarization steadily increase with laser power in the bulk diamond, with little to no variation across the sample, a more complex and heterogeneous behavior is observed in the NDs. In bare as-deposited NDs we report a decrease in the ODMR contrast at the highest laser power explored here, possibly reflecting a more efficient NV-→NV0 photoconversion compared to the bulk, and implying a laser-induced depletion of the pool of NV- centers. The non-monotonic behavior in NDs is likely to be determined by the interplay between spin and charge dynamics under continuous laser illumination. For NDs internalized in cells we observed a qualitatively similar trend as in the bare NDs, with a different, more variable behavior at the highest laser power, suggesting that the cellular environment may play a role in the dynamics of NV charges, perhaps due to the different pH or to surface interactions with different proteins in the cytosol.
In conclusion, the large exposed surface area of NDs is greatly beneficial for sensing applications, e.g. in bioimaging assays, but the effects of surface states and surface interactions on the NV charge stability and photoconversion dynamics should be taken into account. Increasing laser power in the native bulk diamond increases ODMR contrast, a measure of the spin polarization of the ensemble of NV-. Conversely, in NDs, surface effects limit the benefits of stronger laser power due to photoconversion between different charge states. The effects reported here highlight a trade off in the use of NDs for sensing and polarization transfer applications.
NDs – Nanodiamonds
NV – Nitrogen-Vacancy center
NV- – Negatively Charged Nitrogen-Vacancy center
NV0 – Neutral Charged Nitrogen-Vacancy center
P1 - Substitutional nitrogen center
CW-ODMR – Continuous wave - optically detected magnetic resonance
FL – Fluorescence
ROI – Region of interest
MW – Microwave
ZPL - Zero-phonon line
CVD – Chemical vapor deposition
HPHT - High-pressure high-temperature
FBS - Fetal bovine serum
PBS - Phosphate buffered saline
FITC - Fluorescein isothiocyanate
DAPI - 4′,6-diamidino-2-phenylindole
WD – Working distance
NA - Numerical aperture
Availability of data and materials
The datasets used and/or analysed during the current study are available from the corresponding author on reasonable request.
Competing interests
The authors declare that they have no competing interests.
Funding
This project was funded by the European Union Horizon 2020 research and innovation program under the MSCA-ITN grant agreement 766402 (ZULF-NMR) and FET-OPEN grant agreement 858149 (AlternativesToGd). J.A. and A.K. acknowledge the funding by the Deutsche Forschungsgemeinschaft (grant KR3316/6-2, within the FOR1493).
Authors' contributions
A.B., D.O. and F.G. conceived the experiments. D.O. and F.G. performed the experiments. V.B., J.A., A.K., D.O. and F.G. prepared the samples. J.A. and A.K. performed the nanomilling. V.B. prepared the cell line and conducted the confocal microscopy measurement. D.O. wrote the manuscript with the input of F.G and A.B. All of the authors interpreted the results and reviewed the manuscript. A.B. supervised the whole project.
Acknowledgements
We thank L. Basso and P. Aprà for Raman spectroscopy in the department of physics at University of Trento (Italy) and University of Torino (Italy), respectively. We also thank Massimo Cazzanelli for the construction of the set-up and Prof. Simonetta Geninatti-Crich for her input and critical reading of the manuscript.
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No competing interests reported.