ZnO Nanowire Networks as Photoanode Model Systems for Photoelectrochemical Applications

In this work, the fabrication of zinc oxide (ZnO) nanowire networks is presented. By combining ion-track technology, electrochemical deposition, and atomic layer deposition, hierarchical and self-supporting three-dimensional (3D) networks of pure ZnO- and TiO2-coated ZnO nanowires were synthesized. Analysis by means of high-resolution transmission electron microscopy revealed a highly crystalline structure of the electrodeposited ZnO wires and the anatase phase of the TiO2 coating. In photoelectrochemical measurements, the ZnO and ZnO/TiO2 nanowire networks, used as anodes, generated higher photocurrents compared to those produced by their film counterparts. The ZnO/TiO2 nanowire network exhibited the highest photocurrents. However, the protection by the TiO2 coatings against chemical corrosion still needs improvement. The one-dimensionality of the nanowires and the large electrolyte-accessible area make these 3D networks promising photoelectrodes, due to the improved transport properties of photogenerated charge carriers and faster redox reactions at the surface. Moreover, they can find further applications in e.g., sensing, catalytical, and piezoelectric devices.


Introduction
In recent years, the fabrication and development of semiconductor three-dimensional, hierarchical nanowire assemblies has attracted increasing interest. The compact design, mechanical stability, and high surface area of 3D nanowire-based networks can be advantageous in enhancing the performance of gas sensors [1,2], batteries [3,4], and supercapacitors [5], as well as facilitating efficient light absorption and charge carrier transport in photoelectrodes [6][7][8][9][10][11][12][13][14] and optical elements [15,16]. Photoelectrodes can be applied, for example, in water splitting devices for the generation of H 2 as renewable solar fuel. In 1972, Fujishima and Honda successfully demonstrated light-assisted water splitting using an n-type TiO 2 photoanode connected with a platinum black electrode in a photoelectrochemical (PEC) cell for hydrogen production [17]. Since then, increasing the efficiency of both photon-to-current conversion and hydrogen generation has remained a major challenge for scientists. Improvements have been obtained by combining several materials in a tandem cell and adding co-catalysts to open the door for more efficient reduction and oxidation reactions, as well as designing different configurations of photoelectrochemical cells [18]. Besides efficiency, also cost, ease of fabrication, and robustness are also essential requirements that photoelectrodes need to fulfil.
In this work, we investigated the possible path of enhancing the efficiency of photoelectrochemical water splitting by using nanostructured materials [19]. In particular, nanowire-based photoelectrodes are of interest due to the properties arising from their one-dimensional geometrical orientation, which is expected to better facilitate charge carrier separation and transport to the surface of the electrode, compared to bulk materials [20]. Also, the reduced dimensions and large surface area of the photoelectrode/electrolyte interface may lead to shorter diffusion paths for the generated charge carriers, minimized recombination, and faster redox reactions. In addition, nanomaterials can be synthesized in the form of single-crystals, thus significantly decreasing carrier recombination such as at grain boundaries, and potentially also exhibiting increased optical absorption compared to their bulk counterparts [8].
Among the various methods currently available for synthesizing nanowires, electrochemical deposition in porous membranes is highly flexible, allowing the synthesis of a variety of materials including metals, semimetals, metal oxides, and semiconductors [21][22][23][24][25][26][27][28][29]. In particular, the electrodeposition of ZnO nanowires in polymer etched ion-track templates has been reported by several authors employing various electrolytes [30][31][32]. TiO 2 nanowires have been also synthesized by applying a combination of sol-gel methods and polymer track-etched membranes [33]. The nanowires fabricated using this technique typically exhibit a high aspect ratio. The control over size, geometry, and surface area allows us to develop nanowire-based electrodes and to systematically investigate size-effects that influence processes such as electrical resistivity, wettability, surface reactivity, etc.
Here, we present the synthesis of three-dimensional (3D) networks of ZnO nanowires by electrodeposition inside the interconnected, etched ion-track channels of polycarbonate membranes. The presence of junctions between wires from different directions confer enhanced mechanical stability to the assemblies of high aspect ratio nanowires [27], thus providing self-supporting n-type ZnO nanostructured electrodes. The 3D nanowire networks were optimized in terms of integration density and wire diameter. To improve their chemical stability during measurements in aqueous media, the ZnO networks were coated with 20 nm TiO 2 by atomic layer deposition (ALD). Pure ZnO and core/shell ZnO/TiO 2 nanowire networks were employed as model systems to study the photoelectrochemical performance of such hierarchical nanowire structures, as compared to their film counterparts.

Materials and Methods
Series of ZnO and ZnO/TiO 2 nanowire networks were synthesized by schematically following the steps presented in Figure 1.
Polymer templates with highly interconnected cylindrical nanochannels were fabricated by using the ion-track technology, which is based on the irradiation of MeV-GeV heavy ions creating ion-tracks that completely penetrate through the polymer foil. Chemical etching converts the ion-tracks into open nanochannels (Figure 1a,b). Subsequently, a working electrode is prepared on one side of the template ( Figure 1c) and ZnO is electrodeposited inside the channels (Figure 1d). The polymer membrane is then dissolved in an organic solvent ( Figure 1e). Finally, the resulting three-dimensional nanowire network is conformally coated by atomic layer deposition with a 20 nm layer of TiO 2 (Figure 1f). To synthesize a ZnO/TiO 2 nanowire network, approximately~13 h are required-5 for the synthesis and 8 for the TiO 2 ALD coating. The irradiation is performed in sequential steps from different angles of beam incidence; (b) chemical etching in 6M sodium hydroxide (NaOH) at 50 °C converts the ion-tracks into open nanochannels; (c) gold sputtering followed by electrochemical deposition provides a stable gold back-electrode; (d) electrodeposition of zinc oxide (ZnO) inside the membrane channels; (e) release of the ZnO networks by dissolution of the polymer template; (f) atomic layer deposition (ALD) of a titanium dioxide (TiO2) thin film conformally coating the wires and the gold substrate.
Polymer templates with highly interconnected cylindrical nanochannels were fabricated by using the ion-track technology, which is based on the irradiation of MeV-GeV heavy ions creating ion-tracks that completely penetrate through the polymer foil. Chemical etching converts the iontracks into open nanochannels (Figure 1a,b). Subsequently, a working electrode is prepared on one side of the template (Figure 1c) and ZnO is electrodeposited inside the channels (Figure 1d). The polymer membrane is then dissolved in an organic solvent ( Figure 1e). Finally, the resulting threedimensional nanowire network is conformally coated by atomic layer deposition with a 20 nm layer of TiO2 (Figure 1f). To synthesize a ZnO/TiO2 nanowire network, approximately ~13 h are required-5 for the synthesis and 8 for the TiO2 ALD coating.

Membrane Fabrication
Polycarbonate foils (Makrofol N, Bayer AG) (30 µm thick, 30 mm diameter) were irradiated with ~2 GeV Au ions at the universal linear accelerator (UNILAC) of GSI in Darmstadt. Each ion passing through the foil creates, along its trajectory, a cylindrical damage zone known as an ion track. Intersecting tracks were obtained by irradiating the foils four times in consecutive steps, each time from a different direction under an angle of 45°, with respect to the surface normal of the polymer foil [24]. The foils were irradiated with a fluence of 4 × 5 × 10 8 , 4 × 10 9 or 4 × 2 × 10 9 ions/cm 2 (2 × 10 9 , 4 × 10 9 and 8 × 10 9 ions/cm 2 in total, respectively). Irradiation took place through a 5 mm diameter circular aperture (see details in Figure S1 of the Supplementary Information). To selectively remove the ion tracks, the irradiated foils were immersed in a 6 M sodium hydroxide (NaOH) solution at 50 °C. Under these conditions, the radial etching rate was ~11 nm/min. Prior to the etching, the foils were exposed to UV light (30 W, 312 nm T-30M, Vilber Lourmat, Eberhardzell, Germany) from both sides for 1 h to improve the etching of the tracks and the homogeneity of the diameter distribution [34]. To visualize the interconnected nanochannels and to analyze their geometry, membranes were additionally irradiated with high fluence heavy ions (10 10 cm −2 ). The additional radiation damage combined with UV light exposure embrittled the samples and allowed us to break them in liquid nitrogen. This preparation process was applied to obtain the cross-section images shown in Figure 2.

Membrane Fabrication
Polycarbonate foils (Makrofol N, Bayer AG) (30 µm thick, 30 mm diameter) were irradiated with~2 GeV Au ions at the universal linear accelerator (UNILAC) of GSI in Darmstadt. Each ion passing through the foil creates, along its trajectory, a cylindrical damage zone known as an ion track. Intersecting tracks were obtained by irradiating the foils four times in consecutive steps, each time from a different direction under an angle of 45 • , with respect to the surface normal of the polymer foil [24]. The foils were irradiated with a fluence of 4 × 5 × 10 8 , 4 × 10 9 or 4 × 2 × 10 9 ions/cm 2 (2 × 10 9 , 4 × 10 9 and 8 × 10 9 ions/cm 2 in total, respectively). Irradiation took place through a 5 mm diameter circular aperture (see details in Figure S1 of the Supplementary Information). To selectively remove the ion tracks, the irradiated foils were immersed in a 6 M sodium hydroxide (NaOH) solution at 50 • C. Under these conditions, the radial etching rate was~11 nm/min. Prior to the etching, the foils were exposed to UV light (30 W, 312 nm T-30M, Vilber Lourmat, Eberhardzell, Germany) from both sides for 1 h to improve the etching of the tracks and the homogeneity of the diameter distribution [34]. To visualize the interconnected nanochannels and to analyze their geometry, membranes were additionally irradiated with high fluence heavy ions (10 10 cm −2 ). The additional radiation damage combined with UV light exposure embrittled the samples and allowed us to break them in liquid nitrogen. This preparation process was applied to obtain the cross-section images shown in Figure 2.

ZnO Electrodeposition
The track-etched membranes with three-dimensional networks of channels subsequently served as templates for the electrochemical deposition of ZnO nanowire networks. First, one side of the template was sputtered with ~100 nm Au to make a conductive layer serving as an electrical contact to the polymer. The sputtered Au layer was then reinforced with a ~7 µm thick Au layer, which was

ZnO Electrodeposition
The track-etched membranes with three-dimensional networks of channels subsequently served as templates for the electrochemical deposition of ZnO nanowire networks. First, one side of the template was sputtered with~100 nm Au to make a conductive layer serving as an electrical contact to the polymer. The sputtered Au layer was then reinforced with a~7 µm thick Au layer, which was electrodeposited in a two-electrode arrangement at U = −0.7 V using a commercial gold sulphite electrolyte (Gold-SF, 15 g Au L −1 , METAKEM, Usingen, Germany) and an Au rod as anode. This layer served as a working electrode for the ZnO electrodeposition process, and later as a substrate for the nanowire networks.
ZnO was electrochemically deposited with a three-electrode setup, consisting of the Au back layer as a working electrode, a Pt spiral as a counter electrode, and Ag/AgCl (sat. KCl) (Sensortechnik Meinsberg GmbH, Waldheim, Germany) as a reference electrode. An aqueous electrolyte containing 0.1 M Zn(NO 3 ) 2 ·6H 2 O was used, and a constant potential ranging between U = −1 V and U = −1.4 V vs. Ag/AgCl at 60 • C was applied. Previously, electrodeposition of ZnO in etched ion-track membranes with parallel nanochannels was performed at U = −0.8 and −1 V vs. Ag/AgCl at 80 • C [35]. However, these depositions yielded very low filling rates in the interconnected pores. Cyclic voltammetry revealed a shift of the reduction peak to more negative potentials, namely, around U = −1.4 V versus Ag/AgCl. ZnO nanowire networks with a wire diameter of 150 nm were achieved by applying U = −1.4 V at 60 • C. Among a series of samples electrodeposited at 60, 70, and 80 • C, electrodeposition at T = 60 • C provided the most homogeneous fillings, which was most probably due to the reduced deposition rates. The process was monitored by recording the current-versus-time curve, and the deposition was stopped before the material reached the top of the channels [36]. Thus, the networks were grown until the channels were almost completely filled. As the material electrodeposited inside the channels replicate their shape, the deposition resulted in the growth of a 3D nanowire network. To release the network from the template, the polymer was carefully dissolved in a dichloromethane bath (CH 2 Cl 2 , Merck, Darmstadt, Germany).
In addition to the network structures, ZnO films were electrochemically deposited onto unirradiated PC films using the same electrolyte at 60 • C and applying cyclic voltammetry. First, metallic substrates were prepared by sputtering the polymer foils with~100 nm Au, followed by electrodeposition of~7 µm Au and~3 µm Cu on top. Afterwards, the polymer was removed by immersing the sample for 2 h in acetone (Sigma Aldrich, Steinheim, Germany 99.99%), which enables easy detachment of the metallic layer from the polymer. Finally, the samples were cleaned with dichloromethane to remove any remaining polymer residues. The deposition of the ZnO films was carried out onto the sputtered Au layer by applying 10 cycles of cyclic voltammetry. The voltage was swept between 0 and −1.5 V versus Ag/AgCl with a scan rate of 10 mV/s.

TiO 2 Atomic Layer Deposition
Some of the prepared films and nanowire networks were conformally coated with~20 nm TiO 2 using a Picosun R200 ALD system. The main role of the TiO 2 film was to protect ZnO from corrosion during photoelectrochemical measurements. The deposition was performed at 250 • C using titanium tetraisopropoxide (TTIP) and Millipore water as precursors, and nitrogen as carrier gas. Exposure times for TTIP and water were 1.6 and 0.1 s, respectively, for the 250 • C process. A few samples were coated with TiO 2 at 110 • C, and used only for TEM analysis. In this case, the exposure times were 5.2 s and 0.4 s. The N 2 purging times were 8 s and 50 s for 250 • C and 110 • C, respectively.

Photoelectrochemical Measurements
ZnO and ZnO/TiO 2 nanowire network structures, as well as their film counterparts, were applied as photoanodes for the photoelectrochemical measurements. The setup available at the University of Twente consisted of an Arc lamp source with an Xe lamp (Newport 66902, 50-500 W, Irvine, CA, USA) calibrated at AM 1.5 (1 sun), a photoelectrochemical cell (PECC-2, ZAHNER-elektrik GmbH & Co. KG, Kansas City, MO, USA) for three-electrode measurements, and a potentiostat (VERSASTAT4, Princeton applied research, AMETEK, Inc., Berwyn, PA, USA). For the three-electrode setup a Ag/AgCl reference electrode was used, where the built-in Pt wire of the PECC-2 cell was the counter electrode, and the nanowire networks and films served as working electrodes. The samples were fixed with a special O-ring, with a pre-defined area of 0.196 cm 2 being exposed to the light source (photoactive area). To turn the light on and off, a shutter was used. The measurements were performed in a 0.1 M K 2 SO 4 (Sigma Aldrich) aqueous solution (pH 5. where E RHE is the converted potential versus RHE, E Ag/AgCl is the potential applied experimentally versus the Ag/AgCl (sat. KCl) reference electrode used, and E o Ag/AgCl = 0.197 V is the standard potential of an Ag/AgCl reference electrode at 25 • C.
One set of linear sweep voltammetry (LSV) measurements ( Figure 9) was performed using a different set-up available at TU-Darmstadt (Group of Prof. W. Jaegermann). In this case, the potentiostate was a GAMRY Interface 1000, and the pH value of the 0.1 M K 2 SO 4 electrolyte was 5.6. The other parts, such as the photoelectrochemical cell, electrodes, and solar simulator, were comparable to the set-up employed at the University of Twente, as described above.

Sample Characterization
The morphology of both films and nanowire networks were characterized before and after ALD coating with a high-resolution scanning electron microscope (HR-SEM, JEOL JSM-7401F, JEOL, Akishima, Tokyo, Japan). In addition, parts of the wires of the networks were transferred onto transmission electron microscopy (TEM) grids. Electron energy loss spectroscopy (EELS) was used for chemical composition analysis. High-resolution transmission electron microscopy (HRTEM, JEOL-ARM200CF, JEOL, Akishima, Tokyo, Japan) and selected area electron diffraction (SAED) were used to analyze the crystallinity of these wires. The crystallographic properties before and after the PEC measurements were analyzed by means of X-ray diffraction (XRD) using a D2 PHASER diffractometer (Bruker, Billerica, MA, US) (Cu Kα, 30 kV, 10 mA). Figure 2 shows representative SEM images of the cross-section of a network template with a channel density of 4 × 5 × 10 8 cm −2 and a channel diameter of~150 nm at low (a) and high (b) magnification. It is evident that the templates are highly porous and consist of well-interconnected cylindrical channels.

Network Analysis
A series of etched ion-track membranes with various channel diameters, and total channel densities varying between 2 × 10 9 (i.e., 4 × 5 × 10 8 ) and 8 10 9 (i.e., 4 × 2 × 10 9 ) cm −2 were employed as templates to investigate and optimize the electrodeposition of ZnO interconnected nanostructures. Because the diffusion and migration of Zn 2+ ions in highly interconnected channels differ to that in parallel channels, more negative potentials need to be applied. We found that the most homogeneous growth occurred under potentiostatic conditions, applying U = −1.4 V vs. Ag/AgCl at 60 • C [35].
After dissolution of the polymer, morphology and mechanical integrity of the nanowire networks were analyzed by high-resolution SEM (HRSEM). Figure 3 shows the SEM images of a representative network with 150 nm diameter wires along 5 directions (number density of wires~5 × 10 9 cm −2 ). The homogeneous growth of the network over the whole sample is visualized in Figure 3a over ã 100 × 120 µm area. Figure 3b,c show zoomed-in SEM images. In the inset, tilted and vertical wires are marked in blue and red, respectively. A higher magnification SEM image of the area marked in orange is shown in Figure 3d, which displays junctions between multiple wires. Regions marked in white illustrate that several wires interconnect at the same position. The advantage of this network structure is that the overlap of wires is mainly limited to junctions, keeping the one-dimensionality of the structure. Figure 3e shows the five different orientations. The total density of the resulting ZnO material can be adjusted by varying the nanowire density and/or the diameter. SEM images of nanowire networks with the same density of wires, namely 4 × 5 × 10 8 cm −2 , and wire diameters of 210, 150, and 90 nm are shown in the Supplementary Information (Figure S2). cylindrical channels.
A series of etched ion-track membranes with various channel diameters, and total channel densities varying between 2 × 10 9 (i.e., 4 × 5 × 10 8 ) and 8 10 9 (i.e., 4 × 2 × 10 9 ) cm −2 were employed as templates to investigate and optimize the electrodeposition of ZnO interconnected nanostructures. Because the diffusion and migration of Zn +2 ions in highly interconnected channels differ to that in parallel channels, more negative potentials need to be applied. We found that the most homogeneous growth occurred under potentiostatic conditions, applying U = −1.4 V vs. Ag/AgCl at 60 °C [35].
After dissolution of the polymer, morphology and mechanical integrity of the nanowire networks were analyzed by high-resolution SEM (HRSEM). Figure 3 shows the SEM images of a representative network with 150 nm diameter wires along 5 directions (number density of wires ~5 × 10 9 cm −2 ). The homogeneous growth of the network over the whole sample is visualized in Figure 3a over a ~100 × 120 µm area. Figures 3b and c show zoomed-in SEM images. In the inset, tilted and vertical wires are marked in blue and red, respectively. A higher magnification SEM image of the area marked in orange is shown in Figure 3d, which displays junctions between multiple wires. Regions marked in white illustrate that several wires interconnect at the same position. The advantage of this network structure is that the overlap of wires is mainly limited to junctions, keeping the one-dimensionality of the structure. Figure 3e shows the five different orientations. The total density of the resulting ZnO material can be adjusted by varying the nanowire density and/or the diameter. SEM images of nanowire networks with the same density of wires, namely 4 × 5 × 10 8 cm −2 , and wire diameters of 210, 150, and 90 nm are shown in the Supplementary Information (Figure S2).  To improve the chemical stability of the ZnO nanowire networks in aqueous solutions, they were coated with a thin layer of TiO 2 using ALD. Figure 4 shows HRTEM images of the segments of (a) bare ZnO, (b) ZnO/TiO 2 coated at 110 • C, and (c) ZnO/TiO 2 coated at 250 • C. The HR-TEM image of the bare ZnO wire (Figure 4a) reveals an ordered set of planes. The measured distance between the displayed planes was 0.26 nm, as expected, which corresponds to (0002) planes of ZnO with a hexagonal wurtzite structure. The TiO 2 layer deposited at 110 • C is amorphous (Figure 4b the bare ZnO wire (Figure 4a) reveals an ordered set of planes. The measured distance between the displayed planes was 0.26 nm, as expected, which corresponds to (0002) planes of ZnO with a hexagonal wurtzite structure. The TiO2 layer deposited at 110 °C is amorphous (Figure 4b) while at 250 °C the anatase phase is formed (Figure 4c). The inset in Figure 4c also reveals an ordered set of planes corresponding to the TiO2 anatase phase (interplanar distance = 0.354 nm). The respective SAED patterns of uncoated ( Figure 4a   Figure 5a displays a superposition of the high-angle annular dark-field (HAADF) image from a junction of two ZnO/TiO 2 nanowires, and the corresponding EELS elemental mapping. All the wires and intersections examined by SEM and TEM after ALD coating evidenced a consistent increase in wire diameter of~40 nm. In particular, the pieces broken for the TEM studies can belong to either the top or the bottom part of the network, strongly indicating the homogeneous and conformal coating of the complete wire surfaces, including narrow geometries at intersections. A compositional line scan across the nanowire confirms the core-shell morphology (Figure 5b). junction of two ZnO/TiO2 nanowires, and the corresponding EELS elemental mapping. All the wires and intersections examined by SEM and TEM after ALD coating evidenced a consistent increase in wire diameter of ~40 nm. In particular, the pieces broken for the TEM studies can belong to either the top or the bottom part of the network, strongly indicating the homogeneous and conformal coating of the complete wire surfaces, including narrow geometries at intersections. A compositional line scan across the nanowire confirms the core-shell morphology (Figure 5b).

Photoelectrochemical Measurements
For the photoelectrochemical measurements, several ZnO nanowire networks of identical characteristics-that is, of channel density 4 × 2 × 10 9 cm −2 , wire diameter 150 nm, and wire length ~35 µm-were prepared. ALD coatings were performed at 250 °C to obtain a 20 nm-thick, crystalline TiO2 layer. Corresponding planar films with thicknesses of 7-10 µm were used as reference samples. SEM images of the various networks and films are displayed in Figure 6. After TiO2 coating, both film and network samples appeared smoother. This morphology change is attributed to being exposed to 250 °C for 7 h during the ALD process. Analysis of the samples on the complete surface shows that the networks are homogeneous over the entire sample area of ~20 mm 2 .

Photoelectrochemical Measurements
For the photoelectrochemical measurements, several ZnO nanowire networks of identical characteristics-that is, of channel density 4 × 2 × 10 9 cm −2 , wire diameter 150 nm, and wire length 35 µm-were prepared. ALD coatings were performed at 250 • C to obtain a 20 nm-thick, crystalline TiO 2 layer. Corresponding planar films with thicknesses of 7-10 µm were used as reference samples. SEM images of the various networks and films are displayed in Figure 6. After TiO 2 coating, both film and network samples appeared smoother. This morphology change is attributed to being exposed to 250 • C for 7 h during the ALD process. Analysis of the samples on the complete surface shows that the networks are homogeneous over the entire sample area of~20 mm 2 . Nanomaterials 2018, 8, x FOR PEER REVIEW 9 of 14       Figure 6. The nanowire density is 4 × 2 × 10 9 cm −2 and the nanowire diameter is ~150 nm, in all cases. The 20 nm thick TiO2 coating layers were prepared by ALD at 250 °C. The LSVs were measured under chopped light illumination (light on areas marked in yellow) with a scan rate of 10 mV/s.  Figure 6. The nanowire density is 4 × 2 × 10 9 cm −2 and the nanowire diameter is~150 nm, in all cases. The 20 nm thick TiO 2 coating layers were prepared by ALD at 250 • C. The LSVs were measured under chopped light illumination (light on areas marked in yellow) with a scan rate of 10 mV/s.
In the dark, the photocurrent density (~few hundreds of nA/cm 2 ) is negligible for four samples for the complete potential range. The bare ZnO network exhibits a higher dark current, as expected. This is probably due to the direct access of electrolyte to the gold substrate at the bottom of the network, where adsorption of SO 4 2− ions takes place [37]. Under illumination, the oxygen evolution reaction occurs at the photoanodes, and the resulting photocurrents are measured. The films exhibit low photocurrents (~0.02 mA/cm 2 for ZnO and~0.06 mA/cm 2 for ZnO/TiO 2 , at 1.5 V vs. RHE) which remain constant or increase very slightly as a function of voltage. In turn, both 3D nanowire network samples (ZnO and ZnO/TiO 2 ) display higher photocurrents which increased significantly with increasing potential, reaching~0.1 and~0.35 mA/cm 2 at 1.5 V vs. RHE, respectively. In addition to its corrosion protection role, the TiO 2 layer also increases the photocurrent for both the nanowire network and the film. This is attributed on the one hand to additional electron-hole pairs generated in the n-type TiO 2 , and, on the other hand, to the contribution of the ZnO-TiO 2 interface to the charge separation, thereby reducing the probability of electron-hole recombination. These conclusions are supported by additional PEC measurements performed on TiO 2 coated Au nanowire networks ( Supplementary Information, Figure S3), as well as XPS measurements (Supplementary Information, Figure S4). Hu et al. discussed the stability and performance of devices coated with amorphous TiO 2 and concluded that thicker (>100 nm) TiO 2 layers provide better results in regard to electrical characteristics and stability [38]. Here, the thickness of the crystalline anatase TiO 2 layer was limited to 20 nm due to the high density of the nanowire network.
To investigate the morphological stability of the nanowire network samples during the PEC measurements, the photoanodes were imaged again by SEM after the complete PEC characterization. The comparison of each sample before and after the PEC measurements is shown in Figure 8. In the dark, the photocurrent density (~few hundreds of nA/cm 2 ) is negligible for four samples for the complete potential range. The bare ZnO network exhibits a higher dark current, as expected. This is probably due to the direct access of electrolyte to the gold substrate at the bottom of the network, where adsorption of SO4 2− ions takes place [37]. Under illumination, the oxygen evolution reaction occurs at the photoanodes, and the resulting photocurrents are measured. The films exhibit low photocurrents (~0.02 mA/cm 2 for ZnO and ~0.06 mA/cm 2 for ZnO/TiO2, at 1.5 V vs. RHE) which remain constant or increase very slightly as a function of voltage. In turn, both 3D nanowire network samples (ZnO and ZnO/TiO2) display higher photocurrents which increased significantly with increasing potential, reaching ~0.1 and ~0.35 mA/cm 2 at 1.5 V vs. RHE, respectively. In addition to its corrosion protection role, the TiO2 layer also increases the photocurrent for both the nanowire network and the film. This is attributed on the one hand to additional electron-hole pairs generated in the n-type TiO2, and, on the other hand, to the contribution of the ZnO-TiO2 interface to the charge separation, thereby reducing the probability of electron-hole recombination. These conclusions are supported by additional PEC measurements performed on TiO2 coated Au nanowire networks ( Supplementary Information, Figure S3), as well as XPS measurements (Supplementary Information, Figure S4). Hu et al. discussed the stability and performance of devices coated with amorphous TiO2 and concluded that thicker (>100 nm) TiO2 layers provide better results in regard to electrical characteristics and stability [38]. Here, the thickness of the crystalline anatase TiO2 layer was limited to 20 nm due to the high density of the nanowire network.
To investigate the morphological stability of the nanowire network samples during the PEC measurements, the photoanodes were imaged again by SEM after the complete PEC characterization. The comparison of each sample before and after the PEC measurements is shown in Figure 8.    Figure 8a,b display the SEM top-view images of the ZnO and ZnO/TiO 2 nanowire networks, after 1 h and 3 h of PEC measurements, respectively. The corrosion of the uncoated ZnO wires during the PEC measurements resulted in a decrease in wire diameter from~150 nm to~120 nm. Furthermore, in some areas, the morphology of the sample changed dramatically, exhibiting flakes with dimensions in the micrometer range, which we assume to be a result of recrystallization of the ZnO wires into the flake form due to the energy differences among different crystallographic facets [39].
It is well-known that ZnO, as many other candidate materials for water splitting, suffers from photocorrosion in aqueous solutions under ultraviolet illumination by hole-trapping on its surface [40]. ZnO can also decompose when the pH values of the solution are too low or too high, even without illumination [41]. The stability of bare ZnO nanowires during photoelectrochemical water splitting has been investigated by Liu et al. as a function of electrolyte anion and pH value [42].
Additional profilometry measurements (not shown) evidenced a decrease of the average height (thickness) of the nanowire network sample, from the initial 25 µm down to 10-15 µm. This is also consistent with the strong corrosion and recrystallization processes expected for bare ZnO samples. In contrast, the ZnO/TiO 2 nanowire network did not undergo significant changes, demonstrating the protective role of the TiO 2 layer. It is also worth mentioning that (in only on few small spots of the sample) empty TiO 2 tubes were rarely observed (Figure 8b). This could indicate that the core of the ZnO/TiO 2 nanowires in these small sample areas was dissolved, while the TiO 2 shell remained stable. This should be investigated in more detail in future experiments. In this case, the average height of the ZnO/TiO 2 network after PEC measurements remained~25 µm, thus confirming a much higher stability of the TiO 2 -coated nanowire network. Figure 9 shows the LSVs recorded for the networks of ZnO nanowires with diameters of 115, 150, and 190 nm, all ALD coated with a 4 nm-thick TiO 2 layer. The density of the nanowires was 5 × 5 × 10 8 ions/cm 2 , the nanowires being assembled from 5 directions (see Supplementary Information, Figure S2). ZnO was electrodeposited in all membranes under the same conditions, using the same electrolyte and applying U = −1 V vs. Ag/AgCl at 60 • C. After dissolution of the polymer membrane, the nanowires were coated with 4 nm TiO 2 . A network with 150 nm-wide wires remained uncoated. The LSVs were recorded under chopped illumination conditions with a scan rate of 10 mV/s using a 0.1 M K 2 SO 4 (pH = 5.6) solution. ZnO wires into the flake form due to the energy differences among different crystallographic facets [39]. It is well-known that ZnO, as many other candidate materials for water splitting, suffers from photocorrosion in aqueous solutions under ultraviolet illumination by hole-trapping on its surface [40]. ZnO can also decompose when the pH values of the solution are too low or too high, even without illumination [41]. The stability of bare ZnO nanowires during photoelectrochemical water splitting has been investigated by Liu et al. as a function of electrolyte anion and pH value [42].
Additional profilometry measurements (not shown) evidenced a decrease of the average height (thickness) of the nanowire network sample, from the initial 25 µm down to 10-15 µm. This is also consistent with the strong corrosion and recrystallization processes expected for bare ZnO samples. In contrast, the ZnO/TiO2 nanowire network did not undergo significant changes, demonstrating the protective role of the TiO2 layer. It is also worth mentioning that (in only on few small spots of the sample) empty TiO2 tubes were rarely observed (Figure 8b). This could indicate that the core of the ZnO/TiO2 nanowires in these small sample areas was dissolved, while the TiO2 shell remained stable. This should be investigated in more detail in future experiments. In this case, the average height of the ZnO/TiO2 network after PEC measurements remained ~25 µm, thus confirming a much higher stability of the TiO2-coated nanowire network. Figure 9 shows the LSVs recorded for the networks of ZnO nanowires with diameters of 115, 150, and 190 nm, all ALD coated with a 4 nm-thick TiO2 layer. The density of the nanowires was 5 × 5 × 10 8 ions/cm 2 , the nanowires being assembled from 5 directions (see Supplementary Information, Figure S2). ZnO was electrodeposited in all membranes under the same conditions, using the same electrolyte and applying U = −1 V vs. Ag/AgCl at 60 °C. After dissolution of the polymer membrane, the nanowires were coated with 4 nm TiO2. A network with 150 nm-wide wires remained uncoated. The LSVs were recorded under chopped illumination conditions with a scan rate of 10 mV/s using a 0.1 M K2SO4 (pH = 5.6) solution. and ZnO/TiO2 nanowire networks with nanowire density 5 × 5 × 10 8 cm −2 and wire diameters 115 nm (green), 150 nm (blue), and 190 nm (red). The 4 nm TiO2 coating layer was prepared by ALD at 250 °C. Scan rate was 10 mV/s. At a given applied potential, the larger the diameter, the higher the generated photocurrent. This can be explained by the variation in the amount of photoactive ZnO material in the different samples. In addition, the variation of photocurrent as a function of potential increases with increasing nanowire diameter. To elucidate the influence of other effects, such as the wire diameter, compared to the carrier mean free path in such complex nanostructured systems seems challenging. In any case, all three ZnO/TiO2 samples exhibited photocurrent values larger than the corresponding films (see Figure 7). The TiO2 coating led also to larger photocurrents than the uncoated ZnO network. and ZnO/TiO 2 nanowire networks with nanowire density 5 × 5 × 10 8 cm −2 and wire diameters 115 nm (green), 150 nm (blue), and 190 nm (red). The 4 nm TiO 2 coating layer was prepared by ALD at 250 • C. Scan rate was 10 mV/s. At a given applied potential, the larger the diameter, the higher the generated photocurrent. This can be explained by the variation in the amount of photoactive ZnO material in the different samples. In addition, the variation of photocurrent as a function of potential increases with increasing nanowire diameter. To elucidate the influence of other effects, such as the wire diameter, compared to the carrier mean free path in such complex nanostructured systems seems challenging. In any case, all three ZnO/TiO 2 samples exhibited photocurrent values larger than the corresponding films (see Figure 7). The TiO 2 coating led also to larger photocurrents than the uncoated ZnO network.
Please note that ZnO has been used as a model system to investigate the influence of sample geometry on PEC performance. Due to the wide band-gap of ZnO, these networks absorb only UV photons, meaning higher photocurrent values are expected for the nanowire networks of other materials. Also, it is important to emphasize that the samples were measured as-grown, that is, without any post-annealing treatments, optimized ALD coatings, catalysts, or specific surface treatments. Consequently, significantly higher PEC values are expected after optimization of the samples.

Conclusions
In conclusion, three-dimensional nanowire networks of ZnO have been fabricated by electrodeposition in etched ion-track membranes and have been used as photoanodes in photoelectrochemical cells. Their geometrical parameters, such as wire density, wire diameter, and geometrical arrangement, can be easily adjusted by the different steps of the fabrication process. The nanowire networks released from the polymer template can be conformally coated by ALD. The resulting ZnO and ZnO/TiO 2 nanowire networks exhibit high surface areas and increased light-induced photocurrents compared to their film counterparts. PEC characterization of these ZnO/TiO 2 nanostructured model systems demonstrate that the 3D nanowire network geometry is very promising for the synthesis of electrodes for e.g., as water splitting. Finally, their mechanical stability also encourages their application for e.g., gas sensing, piezoelectrics, flexible electronics, etc.