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# Photovoltaic organic interface for neuronal stimulation in the near-infrared

## Abstract

Organic materials, such as conjugated polymers, are attractive building blocks for bioelectronic interfaces. In particular, organic semiconductors show excellent performance in light-mediated excitation and silencing of neuronal cells and tissues. However, the main challenges of these organic photovoltaic interfaces compared to inorganic prostheses are the limited adhesion of conjugated polymers in aqueous environments and the exploitation of materials responsive in the visible spectrum. Here, we show a photovoltaic organic interface optimized for neuronal stimulation in the near-infrared spectrum. We adjusted the organic materials by chemical modification in order to improve the adhesion in an aqueous environment and to modulate the photoelectrical stimulation efficiency. As proof-of-principle, we tested this interface on explanted degenerated mice retinas, thus providing results on the efficiency and reliability of the device as an implant for neural stimulation.

## Introduction

Organic technology has proven to be an efficient tool in bioelectronic interfaces and neuroprostheses for neuronal activity modulation by converting light pulses into electrical or thermal stimulation1,2,3,4,5,6,7,8,9,10,11,12,13. Flexibility, lightweight and biocompatibility are among the main advantages of using organic technology in bioelectronic interfaces. Nevertheless, compared to their inorganic counterparts (e.g. silicon), some challenges about functional organic materials remain open. First, water-induced swelling, degradation and delamination are among the most critical aspects of organic interfaces implanted into the body. Second, in the case of photovoltaic interfaces, the electrical properties of the photovoltaic cell must be tailored to meet the desired conditions of electrical stimulation. Last, organic semiconductors used in photovoltaic bioelectronic interfaces typically have low photoconversion efficiency, and high sensitivity only in the visible spectrum. However, the use of near-infrared (NIR) light would be preferable in bioelectronic interfaces: for example, because of its higher penetration into the tissue.

A notable example of the use of organic technology in bioelectronic interfaces is the exploitation of conjugated polymers in photovoltaic retinal prostheses, which were proposed to induce artificial vision in blind patients5,14,15,16,17. Since photovoltaic retinal prostheses wirelessly convert the light entering the pupil into electrical stimuli, they act as artificial photoreceptors to activate surviving retinal cells. In the past years, conjugated polymers (i.e. poly(3,4-ethylenedioxythiophene)-poly(styrenesulfonate), PEDOT:PSS; regioregular poly(3-hexylthiophene-2,5-diyl), P3HT) and other organic semiconductors ([6,6]-phenyl-C61-butyric acid methyl ester, PC60BM) were successfully exploited to build an organic photovoltaic subretinal interface able to improve visual acuity in dystrophic rats5,7,15,18,19. More recently, our group described a novel foldable and photovoltaic wide-field epiretinal prosthesis (POLYRETINA) based on the P3HT:PC60BM bulk heterojunction (BHJ), with the capability to activate retinal ganglion cells with short pulses of green light14. In the recent years, several organic photovoltaic retinal prostheses were developed based on PEDOT:PSS and P3HT:PC60BM BHJ; however, this BHJ system might not be the optimal choice for photovoltaic retinal stimulation, because of its absorption spectrum limited to the visible range.

In humans and primates, colour vision is based on three types of opsins associated to three different cones: the short (S-), the medium (M-) and the long (L-) wavelength sensitive cones having distinct but overlapping absorption spectra (Fig. 1a)20. The L-cone has the most red-shifted spectral absorbance with a maximum around 564 nm (Fig. 1a, circles). The absorbance spectra of the P3HT:PC60BM BHJ and the retinal photoreceptors largely overlap; thus, the green light used to excite the P3HT:PC60BM BHJ may not be optimal due to the possible activation of remaining cones and rods in patients with residual natural vision, such as in age-related macular degeneration. Moreover, the irradiance levels typically required to stimulate retinal neurons with photovoltaic prostheses (hundreds of µW mm−2) may still be perceived (when visible light is used) even in blind patients without residual vision. NIR illumination activates photovoltaic retinal prostheses without interfering with the residual natural vision. Also, according to the standard for optical safety, the maximum permissible exposure (MPE) for ophthalmic applications increases in the NIR spectrum21.

In this article, we demonstrate that implantable stimulating devices based on conjugated polymers can operate in the NIR spectrum (i.e. wavelength longer than 700 nm). We also document the relevance of the electrical and adhesive properties of the conjugated polymers in the fabrication of a photovoltaic implant with optimised photovoltaic characteristics to achieve an efficient neural stimulation. As proof-of-principle, we designed an organic photovoltaic interface for retinal stimulation, based on the poly[2,6-(4,4-bis-(2-ethylhexyl)-4H-cyclopenta [2,1-b;3,4-b′]dithiophene)-alt-4,7(2,1,3-benzothiadiazole)] blended with PC60BM (PCPDTBT: PC60BM) BHJ1,22. We demonstrate that this BHJ can generate electrical responses at safe irradiance levels suitable for retinal stimulation. Furthermore, we investigate the impact of a cross-linking molecule on adhesive properties and morphology of the organic interface. Last, we also verify that this BHJ is not cytotoxic. These results enable the development of a NIR-sensitive foldable and photovoltaic wide-field epiretinal prosthesis, here called nirPOLYRETINA.

## Results

### Optimization of the bulk heterojunction

To evaluate the performance of the BHJs in the NIR spectrum, we fabricated chips embedding six photovoltaic pixels, each composed of three layers: an anode made of PEDOT:PSS (HTL Solar), the BHJ (P3HT:PC60BM or PCPDTBT: PC60BM), and a cathode made of titanium (Ti). The cathode of each photovoltaic pixel was contacted to measure its output signal referenced to a platinum counter electrode immersed in saline solution (Fig. 1b). We measured the responses of photovoltaic pixels based on both BHJs upon 10-ms light pulses at two NIR wavelengths (730 and 780 nm, where the response of cones should be minimal) and compared them to the ones obtained upon green light illumination (565 nm). In all the experiments, for each chip, the responses from the six electrodes were measured, and the peak amplitudes were quantified and averaged.

As expected, the P3HT:PC60BM BHJ showed the strongest photo-current density (PCD) at 565 nm (Fig. 2a, white circles). However, to evaluate the responsivity at the three wavelengths, we should take into account the theoretical MPE for each wavelength, which is dependent on the pulse duration, the illumination rate, and the angle of illumination (fixed to 46.3°, according to the design of the POLYRETINA device14). For chronic illumination, the MPEs are 384.75 µW mm−2, 2.40 mW mm−2 and 3.03 mW mm−2, respectively for 565, 730 and 780 nm. In case of 10-ms pulsed illumination (Fig. 1c), the theoretical MPE is increased by a factor of 5 for 20 Hz repetition rate (1.92, 12.00 and 15.15 mW mm−2 respectively for 565, 730 and 780 nm), by a factor of 10 for 10 Hz repetition rate (3.85, 24.00, and 30.30 mW mm−2, respectively for 565, 730 and 780 nm), and by a factor of 20 for 5 Hz repetition rate (7.70, 48.00, and 60.60 mW mm−2 respectively for 565, 730 and 780 nm). Therefore, we set the irradiance levels to the following normalized values: 1, 6, and 7.5 mW mm−2, respectively for 565, 730 and 780 nm. These normalized irradiance levels correspond to ~50% of the theoretical MPEs at 20 Hz, 25% at 10 Hz and 12.5% at 5 Hz.

For the P3HT:PC60BM BHJ, the mean PCD obtained at 565 nm with pulses of 1 mW mm−2 (white circles, green line) is 1.85 times higher than the mean PCD obtained at 730 nm (black circles, red line) with pulses of 6 mW mm−2 (Fig. 2a). At 780 nm (black/white circles) the maximal irradiance obtained from the LED was 5.35 mW mm−2, which is lower than the normalized irradiance (7.5 mW mm−2). Therefore, the theoretical PCD value was computed using the interpolating curve (R2 = 0.74). In both cases (730 and 780 nm), the PCD obtained at the normalized irradiance levels is largely lower than the one obtained with a green light (565 nm). The photo-voltage (PV) had a similar behaviour (Fig. 2b). The theoretical PV at 780 nm and 7.5 mW mm−2 (black/white circles, magenta line) was computed using the interpolating curve (R2 = 0.91). Based on these results, we decided to investigate a different BHJ based on the PCPDTBT:PC60BM blend, which might be more efficient for a NIR-responsive retinal prosthesis.

In this case, the wavelength with the highest PCD (Fig. 2c) and PV (Fig. 2d) is 730 nm (black circles). Moreover, if compared at the normalized irradiance levels, the PCD obtained at 730 nm with HTL/PCPDTBT:PC60BM/Ti is 1.4 times higher than the PCD obtained at 565 nm with HTL/P3HT:PC60BM/Ti (Fig. 2e, g; two-tailed t-test, p = 0.1571). On the other hand, the PV is slightly lower (Fig. 2f, g; two-tailed t-test, p = 0.0158). These results suggest that the PCPDTBT:PC60BM BHJ (at 730 nm) should be as efficient as the P3HT:PC60BM blend (at 565 nm) previously used in the POLYRETINA device, considering irradiance levels adjusted to their respective theoretical MPEs. Also, as well as HTL/P3HT:PC60BM/Ti pixels, the photovoltaic electrodes based on the PCPDTBT:PC60BM BHJ are fully discharged in <40 ms from the pulse offset (Fig. 2f), allowing a stimulation pulse rate up to 20 Hz.

### Optoelectronic optimization of the anodic layer

Photovoltaic organic retinal prostheses typically rely on a bottom anode made of PEDOT:PSS5,14,15,16,18. We therefore investigated the optoelectronic effect of its conductivity by using two formulations from Clevios Heraeus: HTL Solar (0.47 S mm−1, average of 5 measures from 1 sample; film thickness of 60 nm) and PH1000 (1.17 S mm−1, average of 5 measures from 1 sample; film thickness of 90 nm). At 730 nm, the mean PCD obtained with the PH1000/PCPDTBT:PC60BM/Ti pixel (grey squares) is considerably higher than the HTL/PCPDTBT:PC60BM/Ti pixel (black circles), while the mean PV increases with a lower rate but it reaches the same value at the normalized irradiance for 730 nm (Fig. 3a, b). To summarize our findings (Fig. 3d, e), the PV and PCD values obtained with the three configurations presented were compared at their best operational wavelengths (565 nm for P3HT and 730 nm for PCPDTBT) and at the normalized irradiance levels (1 mW mm−2 for 565 nm and 6 mW mm−2 for 730 nm). The PH1000/PCPDTBT:PC60BM/Ti pixels (grey squares) showed the highest PCD (one-way ANOVA, p = 0.0018, F = 15.48; Tuckey’s multiple comparisons test: HTL/P3HT:PC60BM/Ti vs HTL/PCPDTBT:PC60BM/Ti p = 0.9235, HTL/P3HT:PC60BM/Ti vs PH1000/PCPDTBT:PC60BM/Ti p = 0.0024, HTL/PCPDTBT:PC60BM/Ti vs PH1000/PCPDTBT:PC60BM/Ti p = 0.0062). On the other hand, the HTL/P3HT:PC60BM/Ti pixels (white circles) showed the highest PV (one-way ANOVA, p = 0.0019, F = 15.21; Tuckey’s multiple comparisons test: HTL/P3HT:PC60BM/Ti vs HTL/PCPDTBT:PC60BM/Ti p = 0.0070, HTL/P3HT:PC60BM/Ti vs PH1000/PCPDTBT:PC60BM/Ti p = 0.0024, HTL/PCPDTBT:PC60BM/Ti vs PH1000/PCPDTBT:PC60BM/Ti p = 0.8937). The HTL/PCPDTBT:PC60BM/Ti pixels (black circles) showed the lowest PCD and PV. Interestingly, the different configurations also have different photovoltage discharge rates at the offset of the light pulse (Fig. 3f). The PH1000/PCPDTBT:PC60BM/Ti pixel showed the faster discharge rate, probably because of the higher electrical conductivity of PH1000 (two-phase exponential decay; HTL/P3HT:PC60BM/Ti: τfast = 4.59 ms and τslow = 33.36 ms, R2 = 0.93; HTL/PCPDTBT:PC60BM/Ti: τfast = 1.03 ms and τslow = 11.31 ms, R2 = 0.95; PH1000/PCPDTBT:PC60BM/Ti: τfast = 0.47 ms and τslow = 3.58 ms, R2 = 0.82).

### Optimization of the anodic layer adhesion

Strong adhesion between materials is a prerequisite for the long-term functioning of an implantable device. However, in organic-based prostheses, the adhesion of the PEDOT:PSS layer over a substrate in aqueous environment is limited by the delamination and solubility of PSS. A common strategy to obtain water-stable thin films of PEDOT:PSS is to add the (3-glycidyloxypropyl)trimethoxysilane (GOPS) crosslinker (typically 1 v/v%), which prevents both dissolution and delamination of PEDOT:PSS films23. On the other hand, it was reported that the electrical conductivity of PEDOT:PSS films decreases as a function of the GOPS content23,24. We found that the addition of 1 v/v% of GOPS to PH1000 reduces the PCD (Fig. 4a, c) and increases the PV (Fig. 4b, d) generated by the PH1000/PCPDTBT:PC60BM/Ti pixels at 730 nm. Moreover, it causes a very slow photovoltage discharge (two-phase exponential decay, τfast = 11.21 ms and τslow = 72.52 ms, R2 = 0.96). Indeed, such configuration does not allow a full discharge and recharge of the electrode voltage between each pulse during 20 Hz train stimulation (Fig. 4e), in contrast to the case when GOPS is not added (Fig. 4f). This slower discharge rate is very likely caused by the reduction of the electrical conductivity due to the addition of 1 v/v% of GOPS (0.21 S mm−1, average of 5 measures from 1 sample; film thickness of 170 nm).

Hence, we investigated which concentration of GOPS could simultaneously increase the adhesion of the PEDOT:PSS film (PH1000) while preserving the photovoltaic performance. We fabricated a set of samples with five concentration of GOPS (0, 0.1, 0.25, 0.5 and 1 v/v%) and measured the PCD and PV. The mean PV (730 nm, 6 mW mm−2) increased immediately upon addition of GOPS, and it remained stable regardless of the concentration (Fig. 5a). Conversely, the mean PCD peak remains high up to 0.1 v/v% of GOPS, and then it decreased. Therefore, one can designate a concentration of 0.1 v/v% as the best compromise, since higher concentration would induce a strong reduction of the PCD generated by the photovoltaic pixels. In parallel, the increase in the concentration of GOPS increases the decay time at the offset of the light pulse (Fig. 5b). The fitting with a two-phase exponential decay function showed that both τfast and τslow increase with the GOPS concentration (Fig. 5c). However, with 0.1 v/v% of GOPS, the electrode is fully discharged (i.e., the PV returns to baseline) in 40 ms from the pulse offset (Fig. 5d), allowing a stimulation pulse rate up to 20 Hz. In summary, the chemical modification of PEDOT:PSS with 0.1 v/v% of GOPS allowed the optimization of the photovoltaic performance for an efficient stimulation. Both the resistance (Fig. 5e, white circles) and the thickness (Fig. 5f) of the PEDOT:PSS thin film are affected by the GOPS concentration. Accordingly, the film conductivity (computed by normalizing the average film resistance by the average film thickness) decreases with the increase of the GOPS concentration (Fig. 5e, black circles). This confirms that the conductivity of the PEDOT:PSS films plays a significant role in the optoelectronic properties of photovoltaic pixels.

To further investigate the role of GOPS in the adhesion of the PEDOT:PSS layer, we fabricated on polydimethylsiloxane (PDMS) photovoltaic retinal interfaces using the PCPDTBT:PC60BM BHJ (nirPOLYRETINA). In this case, the photovoltaic retinal interface was not encapsulated to expose the organic layers to direct contact with water and allow faster delamination (Fig. 6a, b). Soaking experiments in saline solution revealed that the addition of 0.1 v/v% of GOPS (Fig. 6c, middle) increases the adhesion of the photovoltaic pixels to the PDMS substrate compared to pristine PEDOT:PSS (Fig. 6c, left). On the other hand, a higher concentration of GOPS (0.25 v/v%; Fig. 6c, right) does not increase adhesion but induces delamination again. The addition of GOPS not only crosslinks the PSS molecules together, but it also anchors them to the substrate (e.g. PDMS). This explains the strengthened adhesion of PEDOT:PSS to PDMS. Nevertheless, a further increase in the GOPS concentration (e.g. from 0.1 to 0.25 v/v% and above) induced delamination again, but at the interface between PEDOT:PSS and PCPDTBT:PC60BM rather than at the interface with PDMS.

We hypothesize that the increase of the cross-linking degree with GOPS could impair the diffusion of the PCPDTBT molecules into PEDOT:PSS during the thermal treatment after deposition. This lower interaction between the two polymeric layers would inevitably decrease the adhesion forces. To verify this hypothesis, we performed depth-profiling measurements with time-of-flight secondary ion mass spectrometry (ToF-SIMS) from the top surface of PCPDTBT:PC60BM to the bottom side of PEDOT:PSS (i.e., to the substrate) at various concentration of GOPS (Fig. 7a). The analysis of the negative polarity spectra indicates that with increasing GOPS concentration, PC60BM molecules (red curve, C60 fragments) tend to accumulate at the interface towards PEDOT:PSS. Furthermore, the depth distribution of the CN fragments (green curve) suggests a penetration of PCPDTBT molecules into the PEDOT:PSS layer when GOPS is not added. Based on the depth profiles of the relevant fragments, we predicted the organization of the organic molecules and represented it for the two extreme GOPS concentrations: 0 and 1 v/v% (Fig. 7b). In Fig. 7c, the normalized intensities of the PCPDTBT signal (CN- fragments) for the three different GOPS concentrations are plotted to efficiently compare their slopes, representing their distinct penetration depths into PEDOT:PSS. Moreover, the slope of the normalized intensities of the PEDOT signal (SC2O fragments) also shows a diffuse interface (slow rise) for 0 v/v% and a sharper one (faster rise) for 1 v/v% (Fig. 7d).

Therefore, we assume that PCPDTBT molecules are more easily able to penetrate the PEDOT:PSS network if the latter is less cross-linked, allowing an adhesive interface against delamination. Conversely, if PEDOT:PSS is supplemented with GOPS, PC60BM is placed at the interface with PEDOT:PSS, creating a brittle and more fragile interface where delamination can occur25. Hence, a concentration of 0.1 v/v% of GOPS is optimal to enhance both the photovoltaic performance and the adhesion of the two interfaces.

### Thermal management

The theoretical MPEs were computed based on safety standards21 without considering the presence of a photovoltaic implant in contact with the retina. When a photovoltaic retinal prosthesis (e.g. nirPOLYRETINA) is implanted, the incident light absorbed by the prosthesis generates additional heat that needs to be considered into the MPE. At 730 nm, the theoretical MPE for continuous illumination is 2.4 mW mm−2. We used a Finite Element Method (FEM) to estimate the temperature increase in the retina upon photovoltaic illumination (Fig. 8). Without the photovoltaic retinal prosthesis, the temperature increase upon chronic illumination (730 nm, 2.4 mW mm−2, 46.3°, 150 s) at the interface between the retina and the retinal pigmented epithelium is stable at 0.78 °C (Fig. 8a, d). This value might not exactly correspond to the real eye temperature increase due to the model approximations, such as the absorption and thermal coefficients of the eye structures, and will therefore only be used as a reference value. In this simulation, the POLYRETINA structure is present in the model, but all its domains were set exactly as the vitreous humour. This solution allows a better comparison with the case when the nirPOLYRETINA is modelled in epi-retinal configuration (Fig. 8b, e). In the latter, the total temperature increase (at the retina-prosthesis interface) reaches a value of 1.36 °C (730 nm, 2.4 mW mm−2, 46.3°, 150 s), which is 1.7 times higher than without the prosthesis. FEM simulations showed that the temperature increase with the photovoltaic retinal prosthesis is lowered back to 0.78 °C (as without the implant) for a continuous irradiance of 1.4 mW mm−2, which is the adjusted MPE with nirPOLYRETINA for chronic photovoltaic stimulations at 730 nm (Fig. 8c, e). In the case of 10-ms pulsed illumination, the adjusted MPEs are 7, 14 and 28 mW mm−2 respectively for an illumination rate of 20, 10 and 5 Hz.

### Functional validation of the NIR-responsive photovoltaic prosthesis

PCPDTBT was used for bioelectronic interfaces only in few reports1,10. Therefore, we first investigated the in vitro cytotoxicity of the NIR-responsive photovoltaic prosthesis fabricated on a PDMS substrate (Fig. 9a). A mean cell viability (±s.e.m.; n = 4 samples) of 107.725 ± 0.520 was obtained (negative control 100 %, n = 1 sample; positive control 0%, n = 1 sample), thus confirming the non-toxicity of the prosthesis in passive condition (i.e. without pulsed illumination). For each sample the test was performed on triplicate cultures wells and data were averaged (Fig. 9b). A one-way ANOVA analysis (p < 0.0001, F = 223.9) revealed that all the four prostheses tested resulted in a cell viability significantly higher than the positive control (p < 0.0001 for all, Tukey multiple comparisons); similarly, the negative control is significantly higher than the positive control (p < 0.0001, Tukey multiple comparisons). There was no statistically significant difference among the four prostheses and against the negative control (1 vs 2: p = 0.9947; 1 vs 3: p > 0.9999; 1 vs 4: p > 0.9999; 2 vs 3: p = 9989; 2 vs 4: p = 0.9920; 3 vs 4: p > 0.9999; 1 vs negative control: p = 0.5401; 2 vs negative control: p = 0.2888; 3 vs negative control: p = 0.4598; 4 vs negative control: p = 0.5678; Tukey multiple comparisons).

We also verified that the NIR-responsive photovoltaic prosthesis was able to stimulate retinal cells ex vivo. Explanted retinas from 4-months-old retinal degeneration 10 mice, an established model for retinitis pigmentosa26,27,28, were placed onto a microelectrode array and the responses evoked by photovoltaic stimulation (10-ms light pulses, 4.7 mW mm−2) were recorded from retinal ganglion cells (Fig. 9c). At this age, such retinas do not anymore exhibit light responsivity29. NIR light pulses were able to significantly induce firing activity in retinal ganglion cells (Fig. 9d) at a safe irradiance level, compared to equivalent recordings without light pulses (Fig. 9e). We measured the average post-stimulus firing rate in a 300-ms window after the light onset, or in the equivalent window when light pulses were not delivered. This large window compensates for the cell to cell variability in the onset of the spiking response and accounts for both transient and sustained responses, even if the response of transient retinal ganglion cells might result underestimated. NIR light pulses induced a significantly higher response compered to recordings without light pulses (Fig. 9f; p = 0.034, two-tailed paired t-test). This result showed that the NIR-responsive photovoltaic prosthesis can effectively be used for retinal stimulation. The irradiance level used (4.7 mW mm−2) corresponds to 67% of the adjusted MPEs at 20 Hz illumination rate, 33.5% at 10 Hz, and 16.75% at 5 Hz. It remains to determine what will be the optimal illumination rate for photovoltaic retinal prostheses, like POLYRETINA. Clinical results tend to suggest that an increase of the pulse rate above 10 Hz might not necessarily be the most benefiting strategy to elicit relevant perception in implanted patients. A personalized trade-off between high stimulation rates allowing flicker fusion (e.g. 40 Hz in Argus II patients) but affecting the percept strength and duration and lower stimulation rates resulting in sustained but blinking percepts should be determined30. Patients implanted with either subretinal31,32 or epiretinal33,34,35 prostheses tend to prefer low stimulus frequencies. Recent ex vivo evidence also identifies stimulation frequencies from 5 to 10 Hz as the preferred frequency range to activate bipolar cells from the epiretinal side and trigger network-mediated responses in retinal ganglion cells36,37.

## Discussion

Photovoltaics is an attractive approach in bioelectronic medicine and neuroprosthetics to stimulate or modulate neuronal activity. Our results show that organic photovoltaic interfaces can be optimized to achieve higher stability, better optoelectronic performances, and adjusted sensitivity in order to match the desired target application. In a proof-of-concept, we demonstrated the advantage of a NIR-responsive neuroprosthesis for retinal stimulation that allows for higher compliance with the standards for optical safety and reduces the interfering with the residual natural vision.

The use of NIR light for artificial vision was first introduced with silicon-based photovoltaic retinal prostheses38,39,40, which were considered better suited for photovoltaic stimulation because of the higher NIR photoconversion efficiency of silicon compared to conjugated polymers. In organic technology, previous researches attempted to perform retinal stimulation at longer wavelengths, even if still in the visible spectrum41, and a computational study showed that a photovoltaic interface based on conjugated polymers could operate in the NIR spectrum42; however, in the latter study, an experimental validation was not provided. We demonstrated that also organic photovoltaic interfaces can efficiently stimulate blind retinas at NIR wavelengths (i.e. 730 nm). This represents an important contribution to the development of organic retinal implants. Organic photovoltaic bioelectronic interfaces are facing additional challenges, such as optimizing the electrical properties of the photovoltaic cell to meet the required working conditions and the weak stability of the organic materials due to water-induced swelling, degradation, and delamination. Our study addressed these open challenges to advance the exploitation of conjugated polymers in photovoltaic organic prostheses.

## Methods

### Chip micro-fabrication

Samples were fabricated on 20 × 24 mm2 glass substrates (2947-75X50, Corning Incorporated) cleaned by ultra-sonication in acetone, isopropyl alcohol, and deionized water for 15 min each and then dried with a nitrogen gun. The deposition of the PEDOT:PSS and the preparation of the bulk heterojunctions were performed in a glovebox under nitrogen atmosphere. PEDOT:PSS (HTL Solar and PH1000, Clevios) was filtered (1-μm PTFE filters) then spin-coated at 3000 rpm for 40 s on each sample. Subsequent annealing at 115 °C for 30 min was performed. When present, GOPS was added to the solution before filtering. 20 mg of P3HT (698997, Sigma Aldrich) or PCPDTBT (754005-100MG, Sigma) and 20 mg of PC60BM (M111, Ossila) were dissolved in 1 mL of anhydrous chlorobenzene each and let stirring overnight at 70 °C. The solutions were then filtered (0.45 μm PTFE filters) and blended [1:1 v-v]. The P3HT:PC60BM (nominal thickness 100 nm) and PCPDTBT:PC60BM (nominal thickness 100 nm) blends were then spin-coated at 1000 rpm for 45 s. Subsequent annealing at 115 °C for 30 min was performed. Titanium cathodes (diameter 100 µm, nominal thickness 150 nm) were deposited by DC magnetron sputtering through a shadow mask. A plastic reservoir was then attached to the sample using PDMS as adhesive.

### Measure of photo-voltage and photo-current

Samples were placed on a holder, and each electrode was sequentially contacted. A platinum wire immersed in physiological saline solution (NaCl 0.9%) was used as counter electrode. In all, 10-ms light pulses were delivered by a 565-nm (M565L3, Thorlabs), 730-nm (M730L4, Thorlabs), or 780-nm (M780LP1, Thorlabs) LED focused at the sample level. Photo-voltage and photo-current were measured using respectively a voltage amplifier (1201, band DC-3000 Hz, DL-Instruments) and a current amplifier (1212, DL-Instruments). Data sampling (40 kHz) and instrument synchronization were obtained via a DAQ board (PCIe-6321, National Instruments) and custom-made software. Data analysis was performed in MATLAB (MathWorks). When evaluating the photo-current density generated by the interface, also the area of the connecting line exposed to light has been considered.

### Spectral absorbance

The preparation of the bulk heterojunctions was performed as before. The thicknesses were 80 and 62 nm for P3HT:PC60BM and PCPDTBT:PC60BM respectively. The absorbance spectra of the thin films were measured using a UV-vis-NIR UV-3600 Shimadzu spectrophotometer.

### Resistance measurements

The preparation of the PEDOT:PSS was performed as before. The film resistance was measured with a custom 4-point prober (2.5 mm pitch distance) using a Keithley 2400 source-meter. Each sample was measured on five different locations randomly distributed on the surface.

### Thickness measurements

Thin-film thickness was measured in PeakForce tapping mode (ScanAsyst Air silicon tip, f0 = 70 kHz, k = 0.4 N m−1) with a Dimension Icon AFM (Bruker).

### Time-of-flight secondary ion mass spectrometry measurements

The measurements were performed on a ToF-SIMS.5 instrument (IONTOF, Germany) operated in the spectral mode using a 25 keV Bi3+ primary ion beam with an ion current of 0.81 pA. A mass resolving power in the range of 5000 m ∆m−1 was reached. For depth profiling, a 500 eV Cs+ sputter beam with a current of 43.47 nA was used. The raster area of the sputter beam was 500 µm × 500 µm, and the mass spectrometry was performed on an area of 200 µm × 200 µm in the center of the sputter crater. A low-energy electron flood gun was used for charge compensation.

### Fabrication of nirPOLYRETINA prostheses

Prostheses were prepared as previously described14. A thin sacrificial layer of poly(4-styrenesulfonic acid) solution (561223, Sigma-Aldrich) was spin-coated on 4″ Si wafers (1000 rpm, 40 s) and baked (120 °C, 15 min). Degassed PDMS pre-polymer (10:1 ratio base-to-curing agent, Sylgard 184, Dow-Corning) was then spin-coated (1000 rpm, 60 s) and cured in oven (80 °C, 2 h). After surface treatment with oxygen plasma (30 W, 30 s), a 6 µm thick SU-8 (GM1060, Gersteltec) layer was spin-coated (3800 rpm, 45 s), soft-baked (110 °C, 300 s), exposed (140 mJ cm−2, 365 nm), post-baked (90 °C, 1800 s; 60 °C, 2700 s), developed in propylene glycol monomethyl ether acetate (48443, Sigma-Aldrich) for 2 min, rinsed in isopropyl alcohol, and dried with nitrogen gun. After surface treatment with oxygen plasma (30 W, 30 s), a second layer of degassed PDMS pre-polymer (10:1) was spin-coated (3700 rpm, 60 s) and cured in oven (80 °C, 2 h). The PEDOT:PSS (PH1000) film, the PCPDTBT:PC60BM film, and the titanium cathodes were prepared as described above. The photovoltaic membrane was then released from the wafer and plasma bonded to a PDMS dome-shaped support with a 12 mm curvature radius an average thickness of 600 µm.

### Soaking experiments

nirPOLYRETINA devices were soaked in saline solution (NaCl 0.9%) at 37 °C and ultra-sonication was applied for 5 min.

### Cytotoxicity test

The test was conducted according to ISO 10993-5: Biological Evaluation of Medical Devices, in vitro cytotoxicity test. Prostheses were sterilized in a dry oven for 2 h at 120 °C. The test on extraction was performed with samples for a total surface area of 3.54 cm2 each, with a ratio of the product to extraction vehicle of 3 cm2 ml−1. Extraction vehicle was Eagle’s Minimum Essential Medium supplemented with fetal bovine serum, penicillin-streptomycin, amphotericin B, and l-glutamine. The extraction was performed for 24 h at 37 °C. For each sample, the extract was added on triplicate cultures wells containing a sub-confluent L929 cell monolayer. The test samples and the control wells were incubated at 37 °C in 5% CO2 for 24 h. Following incubation, the cell cultures were examined for quantitative cytotoxic evaluation. In all, 50 µl per well of XTT reagent were added to the cells then incubated at 37 °C in 5 % CO2 for further 3–5 h. An aliquot of 100 µl was then transferred from each well into the corresponding wells of a new plate and the optical density was measured at 450 nm.

### Electrophysiology ex vivo

Animal experiments were performed according to the animal authorizations GE3717 approved by the Département de l’Emploi, des Affaires sociales et de la Santé (DEAS), Direction Générale de la Santé of the République et Canton de Genève (Switzerland). Male and female mice from a homozygous colony of retinal degeneration 10 mice (B6.CXB1-Pde6brd10/J, The Jackson Laboratory, Stock number: 004297) were used for the experiments. All animals were kept in a 12 h day/night cycle with access to food and water ad libitum. All the experiments were carried out during the day cycle. Eyes were enucleated from euthanized mice (sodium pentobarbital, 150 mg kg−1) and dissected in carboxygenated (95% O2 and 5% CO2) Ames’ medium (A1420, Sigma-Aldrich) under dim red light. Retinas were placed ganglion cells down and maintained in contact with a transparent microelectrode array with 256 electrodes (256MEA200/30iR-ITO, Multi Channel Systems). The NIR-responsive, polymeric and photovoltaic neuroprosthesis was placed on top of the retina, and both the retina and the prosthesis were kept in position using a 1 mm nylon mesh. Retinas were continuously superfused with carboxygenated Ames’ medium at 32 °C and maintained under dim red light during all the experiments. Light stimuli were generated using a 730-nm light emitting diode (M730L4, Thorlabs) paired to a ×20 objective (CFI Plan Apochromat Lambda, Nikon Instruments). The diameter of the light spot was 4.16 mm. The signal from the 256 recording electrodes was amplified, filtered (300–3000 Hz), and digitalized at 10 kHz (USB-MEA256-System, Multi Channel Systems). Spike detection was performed with the MC_rack software (Multi Channel Systems), and the results were further processed with Neuroexplorer (Neuronexus) and MATLAB. For each cell, the post-stimulus mean firing rate was measured from the PSTH within a 300-ms time window after the light onset.

### Optical safety

Retinal damage upon light exposure can occur because of three main factors: photo-thermal damage, photo-chemical damage, and thermo-acoustic damage21,43. For 10-ms light pulses delivered at 20 Hz, the MPE could be controlled by the photo-thermal (MPET) or photo-chemical damage (MPEC), according to Eqs. (1) and (2), respectively.

$${{\mathrm{MPE}}_{\mathrm{T}}}\;=\;6.93 \cdot 10^{ - 5}C_EC_T\frac{1}{P}$$
(1)
$${{\mathrm{MPE}}_{\mathrm{C}}}\;=\;5.56 \cdot 10^{ - 10}C_B\alpha ^2$$
(2)

For the POLYRETINA prosthesis, the visual angle of is α = 808.12 mrad with an exposed area of 144.22 mm214. For λ = 565 nm, both limits apply and $$C_E = 6.67 \cdot 10^{ - 3}\alpha ^2;\,C_T = 1;\,P = 5.44;\,C_B = 10^{0.02\left( {\lambda - 450} \right)}$$. The limits are MPET = 55.49 mW and MPEC = 72.45 mW. Therefore, the limiting factor is MPET which results in 55.49 mW and corresponds to 384.75 µW mm−2 for an exposed area of 144.22 mm2. For λ = 730 nm and 780 nm, only the MPET applies and $$C_E = 6.67 \cdot 10^{ - 3}\alpha ^2;\,C_T = 10^{0.002\left( {\lambda - 700} \right)};\,P = 1;\,C_B = 1000$$. Therefore, for λ = 730 nm the MPET is 346.59 mW, which corresponds to 2.40 mW mm−2 for an exposed area of 144.22 mm2. For λ = 780 nm, the MPET is 436.33 mW, which corresponds to 3.03 mW mm−2 for an exposed area of 144.22 mm2.

### Thermal model

COMSOL Multiphysics 5.3 was used with the Bioheat module and the General PDE module for the heat transfer and Beer-Lambert light propagation. A uniform beam with a diameter of 13 mm was used as illumination source. The eye model was built with several spheres representing each component (cornea, aqueous humor, lens, vitreous humor, retina, retinal pigmented epithelium, choroid, and sclera). All the parameters used in the model are listed in Table 1.

The nirPOLYRETINA was divided into six domains with homogeneous properties. For each domain, the heat capacity, the thermal conductivity (thermal resistance circuit), the density, and the absorption coefficient (Beer-Lambert law; for titanium, a reflectance of 0.63 was considered57) were computed (Table 2). In case of domains D1, D3 and D5, the thermal conductivity and absorption coefficient were computed independently for the area with titanium/SU8 and for the area without. The two values were weighted proportionally to their respective area to obtain the final aggregated values listed in Table 2. For the density and the heat capacity, the aggregated values were directly weighted proportionally to the volume of each materials composing the domain. Domains D2 and D4 do not contain titanium nor SU8. Domain D6 is composed by PDMS only.

### Statistical analysis and graphical representation

Statistical analysis and graphical representation were performed with Prism (GraphPad Software Inc.). The normality test (D’Agostino & Pearson omnibus normality test) was performed in each dataset to justify the use of a parametric or non-parametric test. In each figure p-values were represented as: *p < 0.05, **p < 0.01, ***p < 0.001 and ****p < 0.0001.

### Reporting summary

Further information on research design is available in the Nature Research Reporting Summary linked to this article.

## Data availability

All data are present in the paper. Original data related to this paper may be requested from the corresponding author upon reasonable request. Raw data related to ex vivo electrophysiology is accessible at https://doi.org/10.6084/m9.figshare.12018663.

## Change history

• ### 09 July 2020

The original version of this Article was updated shortly after publication following an error that resulted in the ORCID IDs of Marta Jole Ildelfonsa Airaghi Leccardi, Maciej Kawecki and Diego Ghezzi being omitted.

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## Acknowledgements

We would like to acknowledge the EPFL Center of Micronanotechnology and The Neural Microsystems Platform at the Wyss Center for Bio and Neuroengineering for their support. We also acknowledge Prof. Kevin Sivula and Dr. Nestor Guijarro Carratala of EPFL for the support with the UV-Vis spectroscopy measurements. This work was supported by École polytechnique fédérale de Lausanne, Medtronic, European Commission (Project 701632), Fondation Mercier pour la science, Velux Stiftung (Project 1102), Gebert Rüf Stiftung (Project GRS-035/17), the Wyss Center for Bio and Neuroengineering, and Swiss National Science Foundation (Project CR23I2-162828).

## Author information

Authors

### Contributions

M.J.I.A.L. fabricated the samples and devices, recorded the photo-voltage and the photo-current, measured the thickness and resistance, performed the soaking experiments, and performed the thermal simulations. N.A.L.C. performed ex vivo electrophysiology. L.F. fabricated the samples and performed the absorbance measurements. M.K. performed time-of-flight secondary ion mass spectrometry measurements. E.G.Z. performed in vitro cytotoxicity. D.G. supervised the entire study and wrote the paper. All the authors read and accepted the paper.

### Corresponding author

Correspondence to Diego Ghezzi.

## Ethics declarations

### Competing interests

The authors declare that they have no competing interests.

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Reprints and Permissions

Airaghi Leccardi, M.J.I., Chenais, N.A.L., Ferlauto, L. et al. Photovoltaic organic interface for neuronal stimulation in the near-infrared. Commun Mater 1, 21 (2020). https://doi.org/10.1038/s43246-020-0023-4

• Accepted:

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• DOI: https://doi.org/10.1038/s43246-020-0023-4

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