The Structural and Electrochemical Properties of CuCoO2 Crystalline Nanopowders and Thin Films: Conductivity Experimental Analysis and Insights from Density Functional Theory Calculations

A novel manufacturing process is presented for producing nanopowders and thin films of CuCoO2 (CCO) material. This process utilizes three cost-effective synthesis methods: hydrothermal, sol-gel, and solid-state reactions. The resulting delafossite CuCoO2 samples were deposited onto transparent substrates through spray pyrolysis, forming innovative thin films with a nanocrystal powder structure. Prior to the transformation into thin films, CuCoO2 powder was first produced using a low-cost approach. The precursors for both powders and thin films were deposited onto glass surfaces using a spray pyrolysis process, and their characteristics were examined through X-ray diffraction, scanning electron microscopy, HR-TEM, UV-visible spectrophotometry, and electrochemical impedance spectroscopy (EIS) analyses were conducted to determine the conductivity in the transversal direction of this groundbreaking material for solar cell applications. On the other hand, the sheet resistance of the samples was investigated using the four-probe method to obtain the sheet resistivity and then calculate the in-plane conductivity of the samples. We also investigated the aging characteristics of different precursors with varying durations. The functional properties of CuCoO2 samples were explored by studying chelating agent and precursor solution aging periods using Density Functional Theory calculations (DFT). A complementary Density Functional Theory study was also performed in order to evaluate the electronic structure of this compound. Resuming, this study thoroughly discusses the synthesis of delafossite powders and their conversion into thin films, which hold potential as hole transport layers in transparent optoelectronic devices.


Introduction
In recent decades, there has been a significant demand for advancements in the integration of high-efficiency p-type transparent conductive oxides (TCOs) into industrial applications, particularly in the past few decades [1][2][3][4][5]. However, the research community is keen on exploring alternative TCOs and enhancing their electrical and optical properties to improve device efficiency [6][7][8]. Among various delafossite oxides, copper-based delafossite oxides stand out as promising candidates due to their desirable electrical and optical characteristics. The copper-based delafossite oxide, specifically CuMO 2 (where M drate (Co(NO 3 ) 2 , 6H 2 O; 98%) was used as the Co 2+ source; and sodium hydroxide (NaOH) was obtained from Sigma-Aldrich. As a solvent, deionized water (DW) was utilized. At room temperature, all chemicals were added. The amount of each precursor was 2 mM of each of the copper and cobalt sources, 4.40 g of sodium hydroxide, and 70 mL of deionized water (DW), respectively. All of the precursors were measured and mixed in a reasonable amount of solvent for three hours. For hydrothermal synthesis: method 1 (sample named CuCoO 2 _H), the liquid was placed in a 100 mL Teflon autoclave and autoclaved at 100 • C for 24 h; we washed the obtained solution several times with distilled water. Method 2: solid-state reaction (sample named CuCoO 2 _SSR); stoichiometric amounts of the abovementioned powders were ground with ethanol solution (95%) for 24 h. The ground powder was calcined at 800 • C for 5 h. Method 3: sol-gel (sample named CuCoO 2 _SG); copper(II) nitrate and cobalt(II) nitrate were mixed in ethylene glycol. The solution was agitated at room temperature for 1 h in a beaker before being dried at 150 • C for 5 h. On a heated plate with a magnetic stirrer, gelation took place until a purple color emerged. The amorphous powder was heated incrementally from 50 • C to 800 • C.

Synthesis of the CuCoO 2 Thin Films
The glass substrate cleaning process was performed by ultrasonically cleaning and drying the substrate. The dissolved nanocrystal precursor solution was then converted into a thin film. CuCoO 2 /glass films were produced using spray pyrolysis technology. First, we dispersed 1 mg of CuCoO 2 powder in 10 mL of ethanol/water mixture and sonicated for 30 min to form homogeneous slurry. The CuCoO 2 slurry was then deposited on the glass film ( Figure 1). The resulting film was annealed in air at 350 • C for 40 min to form a CuCoO 2 -coupled glass film.

Synthesis of CuCoO2 Powders
CuCoO2 was produced using three different methods. The grains of copper(II) nitrate trihydrate (Cu(NO3)2, 3H2O; 99%) were used as the Cu +2 source; cobalt(II) nitrate hexahydrate (Co(NO3)2, 6H2O; 98%) was used as the Co 2+ source; and sodium hydroxide (NaOH) was obtained from Sigma-Aldrich. As a solvent, deionized water (DW) was utilized. At room temperature, all chemicals were added. The amount of each precursor was 2 mM of each of the copper and cobalt sources, 4.40 g of sodium hydroxide, and 70 mL of deionized water (DW), respectively. All of the precursors were measured and mixed in a reasonable amount of solvent for three hours. For hydrothermal synthesis: method 1 (sample named CuCoO2_H), the liquid was placed in a 100 mL Teflon autoclave and autoclaved at 100 °C for 24 h; we washed the obtained solution several times with distilled water. Method 2: solid-state reaction (sample named CuCoO2_SSR); stoichiometric amounts of the abovementioned powders were ground with ethanol solution (95%) for 24 h. The ground powder was calcined at 800 °C for 5 h. Method 3: sol-gel (sample named CuCoO2_SG); copper(II) nitrate and cobalt(II) nitrate were mixed in ethylene glycol. The solution was agitated at room temperature for 1 h in a beaker before being dried at 150 °C for 5 h. On a heated plate with a magnetic stirrer, gelation took place until a purple color emerged. The amorphous powder was heated incrementally from 50 °C to 800 °C.

Synthesis of the CuCoO2 Thin Films
The glass substrate cleaning process was performed by ultrasonically cleaning and drying the substrate. The dissolved nanocrystal precursor solution was then converted into a thin film. CuCoO2/glass films were produced using spray pyrolysis technology. First, we dispersed 1 mg of CuCoO2 powder in 10 mL of ethanol/water mixture and sonicated for 30 min to form homogeneous slurry. The CuCoO2 slurry was then deposited on the glass film ( Figure 1). The resulting film was annealed in air at 350 °C for 40 min to form a CuCoO2-coupled glass film.

The Four-Probe Method
The measurement of conductivity in powders and polymeric thin membranes is a complex task that is influenced by various factors, including sample casting preparations, thermal/hydrothermal treatments, relative humidity, and the cell configuration used for film resistance measurements, as well as the pressure applied between the probe electrodes [77]. The four-probe method is commonly used to measure sample sheet resistance and estimate in-plane conductivity, but it may result in inaccuracies, particularly for materials with morphological anisotropy [78,79]. According to this method in which four probes are arranged equidistantly in a straight line and pushed against the film as shown in Figure 2, the resistivity may be calculated through determining the potential difference

The Four-Probe Method
The measurement of conductivity in powders and polymeric thin membranes is a complex task that is influenced by various factors, including sample casting preparations, thermal/hydrothermal treatments, relative humidity, and the cell configuration used for film resistance measurements, as well as the pressure applied between the probe electrodes [77]. The four-probe method is commonly used to measure sample sheet resistance and estimate in-plane conductivity, but it may result in inaccuracies, particularly for materials with morphological anisotropy [78,79]. According to this method in which four probes are arranged equidistantly in a straight line and pushed against the film as shown in Figure 2, the resistivity may be calculated through determining the potential difference between the RE and S electrodes, due to current passing via an easily identifiable connection between the WE and CE electrodes ( Figure 2). Knowing the resistivity, the sheet conductivity can be calculated from the inverse of the sheet resistivity as between the RE and S electrodes, due to current passing via an easily identifiable c tion between the WE and CE electrodes ( Figure 2). Knowing the resistivity, the she ductivity can be calculated from the inverse of the sheet resistivity as where ρ is the sheet resistivity, Rs the in-plane resistance, and t is the sheet sample ness. In our samples, the thickness values are 140 nm, 136 nm, and 142 nm for CuCo CuCoO2_SG, and CuCoO2_SSR, respectively.

Electrochemical Impedance Spectroscopy (EIS) Measurements
The conductivity was measured through the samples with a Novocontrol broa dielectric spectrometer (BDS) equipped with an SR 830 lock-in amplifier and an dielectric interface in the frequency interval from 10 −1 to 10 7 Hz with 0.1 V amplit the signal at temperatures ranging from 20 to 120 °C in increments of 20 °C. The sa were airbrushed before being tested, and their thicknesses were determined via a m eter, averaging 10 readings from various sections of the surface. The samples were in a vacuum cell and placed between two gold round electrodes that served as bl electrodes before being heated in the Novocontrol system in a neutral nitrogen-fre ronment. A temperature cycle from 20 to 120 °C in 20 °C increments was performed collecting the dielectric spectra at every step to ensure uniformity and reduce interf from remaining water. During the testing, the electrodes were kept completely wet 100 °C and replicated a 100% relative humidity environment above 100 °C in a BD liquid device that was attached to the spectrometer and contained deionized wa accurately control the temperature conditions, the temperature was kept co throughout the conductivity measures (isothermal investigations) or shifted ste from 20 to 120 °C using a nitrogen jet (QUATRO from Novocontrol), alongside a te ature error of 0.1 K throughout each frequency sweep.
The frequency dependence of complex impedance Z*(ω) = Z′(ω) + j . Z″(ω) yie real component of conductivity as where L and S represent the thickness and area of the sample in contact with th trodes, and R0 represents its resistance.

Electrochemical Impedance Spectroscopy (EIS) Measurements
The conductivity was measured through the samples with a Novocontrol broadband dielectric spectrometer (BDS) equipped with an SR 830 lock-in amplifier and an Alpha dielectric interface in the frequency interval from 10 −1 to 10 7 Hz with 0.1 V amplitude of the signal at temperatures ranging from 20 to 120 • C in increments of 20 • C. The samples were airbrushed before being tested, and their thicknesses were determined via a micrometer, averaging 10 readings from various sections of the surface. The samples were dried in a vacuum cell and placed between two gold round electrodes that served as blocking electrodes before being heated in the Novocontrol system in a neutral nitrogen-free environment. A temperature cycle from 20 to 120 • C in 20 • C increments was performed before collecting the dielectric spectra at every step to ensure uniformity and reduce interference from remaining water. During the testing, the electrodes were kept completely wet below 100 • C and replicated a 100% relative humidity environment above 100 • C in a BDS 1308 liquid device that was attached to the spectrometer and contained deionized water. To accurately control the temperature conditions, the temperature was kept constant throughout the conductivity measures (isothermal investigations) or shifted stepwise from 20 to 120 • C using a nitrogen jet (QUATRO from Novocontrol), alongside a temperature error of 0.1 K throughout each frequency sweep.
The frequency dependence of complex impedance Z*(ω) = Z (ω) + j·Z (ω) yields the real component of conductivity as where L and S represent the thickness and area of the sample in contact with the electrodes, and R 0 represents its resistance.  Figure 3 were identified as pure phases of CuCoO 2 without secondary phases. The main peak of delafossite CuCoO 2 in the rhombohedral structure (110) is at 2θ = 37.92 • , and the hexagonal structure is at 2θ = 38.27 • .  Figure 3 were identified as pure phases of CuCoO2 without secondary phases. The main peak of delafossite CuCoO2 in the rhombohedral structure (110) is at 2θ = 37.92°, and the hexagonal structure is at 2θ = 38.27°. After characterization of CuCoO2 nanoparticles prepared by three methods: the hydrothermal method, sol-gel method, and solid-state reaction method, we examined their structure following deposition onto glass substrates and thin film synthesis using spray pyrolysis. Figure 4 shows the XRD graphs of the thin films of CuCoO2 on the glass substrates. We observed some of the peaks shown in the XRD pattern, which now appear in the diffractograms of the deposited film. However, the structure did not change, and the material showed two structures containing delafossite: 3R-CuCoO2 (JCPDS#21-0256) and 2H-CuCoO2 (JCPDS#74-1855). Furthermore, it is clear that each XRD pattern begins with a tablet. It belongs to the glass substrate. After characterization of CuCoO 2 nanoparticles prepared by three methods: the hydrothermal method, sol-gel method, and solid-state reaction method, we examined their structure following deposition onto glass substrates and thin film synthesis using spray pyrolysis. Figure 4 shows the XRD graphs of the thin films of CuCoO 2 on the glass substrates. We observed some of the peaks shown in the XRD pattern, which now appear in the diffractograms of the deposited film. However, the structure did not change, and the material showed two structures containing delafossite: 3R-CuCoO 2 (JCPDS#21-0256) and 2H-CuCoO 2 (JCPDS#74-1855). Furthermore, it is clear that each XRD pattern begins with a tablet. It belongs to the glass substrate.

FE-SEM Analysis
We are interested in the morphology and particle size distribution of our compound CuCoO 2 . Observations by scanning electron microscopy (SEM) were carried out on a submicron scale on the three prepared CuCoO 2 nanocrystal powders as shown in Figure 5. A 1 µm magnification is given.
FE-SEM images of the powders show that the submicron CuCoO 2 _H, CuCoO 2 _SG, and CuCoO 2 _SSR are in the form of a powder made up of crystals of different sizes, and they contain agglomerates of hexagonal particles and crystals like rhombohedral shapes. There have been no additional morphologies detected, which confirms the XRD results. Nanomaterials 2023, 13, x FOR PEER REVIEW 6 of 24

FE-SEM Analysis
We are interested in the morphology and particle size distribution of our compound CuCoO2. Observations by scanning electron microscopy (SEM) were carried out on a submicron scale on the three prepared CuCoO2 nanocrystal powders as shown in Figure 5. A 1 µm magnification is given.

FE-SEM Analysis
We are interested in the morphology and particle size distribution of our compound CuCoO2. Observations by scanning electron microscopy (SEM) were carried out on a submicron scale on the three prepared CuCoO2 nanocrystal powders as shown in Figure 5. A 1 µm magnification is given.  FE-SEM images of the powders show that the submicron CuCoO2_H, CuCoO2_SG, and CuCoO2_SSR are in the form of a powder made up of crystals of different sizes, and they contain agglomerates of hexagonal particles and crystals like rhombohedral shapes. There have been no additional morphologies detected, which confirms the XRD results. Figure 6 shows FE-SEM images of produced thin films comprising CuCoO2_H, CuCoO2_SG, and CuCoO2_SSR at 1 µm. After deposition with the spray pyrolysis technique, all films had a uniform distribution of nanocrystalline particles.  Figure 7 shows the characterization of the three samples with transmission electron microscope (TEM) characterization, and the high-resolution transmission electron microscopy (HR-TEM) images of CuCoO2 are illustrated in Figure 7. As a result, we could assume that the crystallinity of CuCoO2 retains a structure mostly constituted of nanocrystals smaller than 15 nm in diameter. HR-TEM d-spacings are likewise consistent with a mixture of rhombohedral and hexagonal CuCoO2 chalcopyrite phases. The results from the FE-SEM agree with the HR-TEM images, which show clearly established small grains of some tens of nanometers.  Figure 7 shows the characterization of the three samples with transmission electron microscope (TEM) characterization, and the high-resolution transmission electron microscopy (HR-TEM) images of CuCoO 2 are illustrated in Figure 7. As a result, we could assume that the crystallinity of CuCoO 2 retains a structure mostly constituted of nanocrystals smaller than 15 nm in diameter. HR-TEM d-spacings are likewise consistent with a mixture of rhombohedral and hexagonal CuCoO 2 chalcopyrite phases. The results from the FE-SEM agree with the HR-TEM images, which show clearly established small grains of some tens of nanometers. and CuCoO2_SSR are in the form of a powder made up of crystals of different sizes, and they contain agglomerates of hexagonal particles and crystals like rhombohedral shapes. There have been no additional morphologies detected, which confirms the XRD results. Figure 6 shows FE-SEM images of produced thin films comprising CuCoO2_H, CuCoO2_SG, and CuCoO2_SSR at 1 µm. After deposition with the spray pyrolysis technique, all films had a uniform distribution of nanocrystalline particles.  Figure 7 shows the characterization of the three samples with transmission electron microscope (TEM) characterization, and the high-resolution transmission electron microscopy (HR-TEM) images of CuCoO2 are illustrated in Figure 7. As a result, we could assume that the crystallinity of CuCoO2 retains a structure mostly constituted of nanocrystals smaller than 15 nm in diameter. HR-TEM d-spacings are likewise consistent with a mixture of rhombohedral and hexagonal CuCoO2 chalcopyrite phases. The results from the FE-SEM agree with the HR-TEM images, which show clearly established small grains of some tens of nanometers.

EDX Analysis
We further investigate the chemical composition of our sample using the EDS technique. In Figure 9 and tables below we show the results of the EDS analysis for the cracked surfaces of the CuCoO2_H, CuCoO2_SG, and CuCoO2_SSR samples. From the table above, the percentages of each Cu and Co in a position are approximately the same, but the percent of oxygen is a bit high. This difference may be due to the oxidation of copper or cobalt.

EDX Analysis
We further investigate the chemical composition of our sample using the EDS technique. In Figure 9 and tables below we show the results of the EDS analysis for the cracked surfaces of the CuCoO 2 _H, CuCoO 2 _SG, and CuCoO 2 _SSR samples. From the table above, the percentages of each Cu and Co in a position are approximately the same, but the percent of oxygen is a bit high. This difference may be due to the oxidation of copper or cobalt.

EDX Analysis
We further investigate the chemical composition of our sample using the EDS tec nique. In Figure 9 and tables below we show the results of the EDS analysis for the crack surfaces of the CuCoO2_H, CuCoO2_SG, and CuCoO2_SSR samples. From the table abo the percentages of each Cu and Co in a position are approximately the same, but the p cent of oxygen is a bit high. This difference may be due to the oxidation of copper or coba

Optical Properties
The transmittance spectra have been used to examine optical qualities. In the area, all of the CuCoO2 thin films displayed extensive absorption. The absorbance cients for thin film samples generated utilizing a spray pyrolysis method containing crystals were determined. In the transmittance spectrum of materials, the absorpti efficient is connected with the optical energy gap or it is in the strong absorption which may be estimated using Tauc's equation [74] = (ℎ − ) ℎ A is a constant, h is the Planck constant, ν is the frequency, and n is an indica the optical absorption process. It equals 2 for directly permitted transitions and indirectly permitted transitions. Figure 10 shows (a) the transmission values and Tauc plot for CuCoO2 thin films. The arrangement of Tauc's figure suggests th CuCoO2 thin film under deposit has a straight band gap. Eg may be estimated by e olating by projecting a horizontal line to the point of zero absorption coefficient ( The band gaps were calculated by graphing (αhν) 2 vs. energy in eV and extrapolati linear portion of the spectrum (hν). According to the transmission graph ( Figure 10 powder CuCoO2_SG has the highest transmission value compared to the two other ders CuCoO2_H and CuCoO2_SSR. The order of the delafossite powders transmis obviously confirmed with the band gap graphs (Figure 10b).
In the Tauc's plot, the "linear part" is selected by examining the absorption d higher photon energies, where the absorption is predominantly governed by indirec sitions, with its absorption coefficient being practically constant. In our study, the lation of band gap values has an error of ±0.10 eV and was obtained by taking the part of the curve (between 4 and 4.5 eV), fitting these points to a straight line, and e olating this line until it intersects the base line (OX axis). The intersection value (in the direct band gap according to Tauc's model [74]. In our study, the values obtain our delafossite material are 3.51 ± 0.10 eV, 3.77 ± 0.12 eV, and 3.87 ± 0.10 eV for Cu

Optical Properties
The transmittance spectra have been used to examine optical qualities. In the visible area, all of the CuCoO 2 thin films displayed extensive absorption. The absorbance coefficients for thin film samples generated utilizing a spray pyrolysis method containing nanocrystals were determined. In the transmittance spectrum of materials, the absorption coefficient is connected with the optical energy gap or it is in the strong absorption zone, which may be estimated using Tauc's equation [74] A is a constant, h is the Planck constant, ν is the frequency, and n is an indicator of the optical absorption process. It equals 2 for directly permitted transitions and 0.5 for indirectly permitted transitions. Figure 10 shows (a) the transmission values and (b) the Tauc plot for CuCoO 2 thin films. The arrangement of Tauc's figure suggests that the CuCoO 2 thin film under deposit has a straight band gap. E g may be estimated by extrapolating by projecting a horizontal line to the point of zero absorption coefficient (α = 0). The band gaps were calculated by graphing (αhν) 2 vs. energy in eV and extrapolating the linear portion of the spectrum (hν). According to the transmission graph (Figure 10a), the powder CuCoO 2 _SG has the highest transmission value compared to the two other powders CuCoO 2 _H and CuCoO 2 _SSR. The order of the delafossite powders transmission is obviously confirmed with the band gap graphs (Figure 10b).
In the Tauc's plot, the "linear part" is selected by examining the absorption data at higher photon energies, where the absorption is predominantly governed by indirect transitions, with its absorption coefficient being practically constant. In our study, the calculation of band gap values has an error of ±0.10 eV and was obtained by taking the linear part of the curve (between 4 and 4.5 eV), fitting these points to a straight line, and extrapolating this line until it intersects the base line (OX axis). The intersection value (in eV) is the direct band gap according to Tauc's model [74]. In our study, the values obtained for our delafossite material are 3.51 ± 0.10 eV, 3.77 ± 0.12 eV, and 3.87 ± 0.10 eV for CuCoO 2 -H, CuCoO 2 -SSR and CuCoO 2 -SG, respectively. Depending on the number of points chosen in the range considered, it works as if it were a transparent layer with a certain uncertainty. This suggests that delafossite is likely to be a good transmitter of charge carriers, leading to a higher band gap value of around 3.5 eV. H, CuCoO2-SSR and CuCoO2-SG, respectively. Depending on the number of points chosen in the range considered, it works as if it were a transparent layer with a certain uncertainty. This suggests that delafossite is likely to be a good transmitter of charge carriers, leading to a higher band gap value of around 3.5 eV.

In-Plane Conductivity Measurements
In powders used for solar cells, the four-point probe method is the most often used method for assessing the electrical characteristics of conducting films [78,79]. This approach has been utilized to evaluate the in-plane conductivity of CuCoO 2 films on top of nonconductive substrates (in our instance, glass), which are typically created by spray pyrolysis technology of the dispersions employed in this work. The experimental procedure used is the following. The four-point probe is attached to a source meter that supplies a certain current. A source meter's current (I) flows through the two outer probes, and a voltammeter can measure the voltage (V) across the two inner probes. By plotting the voltage measured for each current intensity, the sheet resistance, Rs, can be determined, as is shown in Figure 11. A close inspection of these figures reveals that sample resistance (R s ) of the CuCoO 2 films is constant, and its values can be obtained from the slope of the experimental fit determined from the plot of the voltage versus intensity, where a clear linearity is observed for all the samples. According to the KIT used to measure the resistance of the film by means of the four-points method, the value of R s is given by The value for said KIT as a consequence of the geometry used in the measurement is the constant 4.532. Therefore, the in-plane conductivity, given in Equation (3), is determined from the sheet resistance from Equation (4). The results of the three produced CuCoO 2 samples using the four-point probe technique and measured at ambient temperature are presented in Table 1. The conductivity values change with the chelating agent and the aging duration. These findings imply that aging period and thickness change have an effect on electrical conductivities.

Dielectric Spectra Analysis
The electrical impedance spectroscopy (EIS) measurements were performed on all samples to determine the conductivity measured in the transversal direction, named direct current conductivity (σ dc ). Such measurements were carried out over a temperature interval of 20 • C to 120 • C in two steps to ensure reproducibility within the temperature interval. The experimental data obtained for the samples from the Novocontrol were examined to obtain the complex dielectric permittivity function, denoted as ε*(ω,T); and the complex conductivity function, denoted as σ*(ω,T), where j is the imaginary unit (j 2 = −1), ε 0 is the vacuum permittivity, and ω is the angular frequency of the electric field that was applied (ω = 2πf). Different methods have been used to determine the dc-conductivity of a sample from dielectric spectroscopy data analysis [80][81][82][83][84][85][86][87][88][89][90]. In this work, we have used the Bode diagram obtained from the complex dielectric spectra, where the complex conductivity is given by σ*(ω,T) = j ε 0 ω ε*(ω,T), which can be expressed in terms of the real and imaginary part, σ (ω,T) and σ (ω,T), respectively, and the direct current conductivity σ dc was calculated [91][92][93][94]. This technique was used in this study to examine data for the real component of conductivity in dry conditions by graphing conductivity (in S cm −1 ) vs. frequency (in Hz) using the appropriate Bode diagrams for all temperature ranges.
The Bode diagrams for CuCoO 2 _H, CuCoO 2 _SG, and CuCoO 2 _SSR delafossite materials were investigated at temperatures ranging from −20 • C to 120 • C, with increments of 20 • C, as shown in Figure 12. Additional graphs demonstrating the variation of phase angle (φ) vs. frequency at identical temperatures are included in the Supplementary Materials. Upon closer examination of the figures, it can be observed that the conductivity tends to a constant value (plateau) when the phase angle (φ) approaches zero or reaches a maximum, indicating the direct-current conductivity (σ dc ) of the sample. Furthermore, a decrease in conductivity with decreasing frequency was observed in the high-frequency region, along with a transition zone where the cut-off frequency ranges from 10 5 to 10 6 Hz for CuCoO 2 _SG and CuCoO 2 _SSR samples and starts increasing with frequency. In the case of the hydrothermal sample CuCoO 2 _H, the real part of conductivity remains constant at low frequencies until a cut-off frequency between 10 3 Hz and 10 6 Hz, after which it starts in-creasing with frequency. The initial process is connected to the sample's resistance/stability, but this second process is connected to the dispersion (charge transfer) caused by the charge's mobility, as the sample behaves like a capacitor. The conductivity values presented were derived using the peak frequency when the phase angle approaches 0. caused by the charge's mobility, as the sample behaves like a capacitor. The conductivity values presented were derived using the peak frequency when the phase angle approaches 0. Upon careful examination of Figure 12, it can be observed that samples CuCoO2_SG and CuCoO2_SSR exhibit a nearly constant conductivity across a wide range of frequencies and temperatures; that is standard behavior for a conductive material. Identical be- Upon careful examination of Figure 12, it can be observed that samples CuCoO 2 _SG and CuCoO 2 _SSR exhibit a nearly constant conductivity across a wide range of frequencies and temperatures; that is standard behavior for a conductive material. Identical behavior has been reported in previous studies on nanocomposites of multilayer graphene in polypropylene [95]. This phenomenon is due to Debye relaxation, which occurs as a result of the mobility and redirection of dipoles and localized charges at high frequencies in response to an applied electric field and dominates direct-current conductivity [91,92,96]. The change in dc-conductivity of the samples at various temperatures may be determined from the plateau where the phase angle is zero or tends to zero. For frequencies where the phase is near zero, we have a pure resistive impedance that can be attributed to the ionic conductivity alone. This value is the active phase with high-efficiency electrochemical processes and respects the charge transport into the powders. These phenomena are observed for all the samples at frequencies below 10 4 Hz. Moreover, with rising temperature, the frequency at which the point of equilibrium occurs moves to high frequencies, where a plateau in the Bode diagram from low to high frequencies can be observed, suggesting thermal activation of ionic transport. The constant value of conductivity suggests that the sample solely shows resistive contribution, and the quantity measured represents the sample's electrical conductivity. For example, Figure 12 shows that at 20 • C, the trough plane conductivity values followed the trend: σ CuCoO2_SG (5.2 × 10 −5 S cm −1 ) > σ CuCoO2_SSR (2.9 × 10 −5 S cm −1 ) > σ CuCoO2_H (4.53 × 10 −8 S cm −1 ). Similar trends can be observed for the other temperatures studied (for example, 40 • C, 60 • C, 80 • C, 100 • C and 120 • C). For 120 • C the conductivity values obtained, follow the trend, σ CuCoO2_SG (1.4 × 10 −3 S cm −1 ) > σ CuCoO2_SSR (5.7 × 10 −4 S cm −1 ) > σ CuCoO2_H (1.0 × 10 −5 S cm −1 ), respectively. Among the three samples, the greatest proton conductivity of about 10 −3 S cm −1 at 120 • C was found for the CuCoO 2 _SG sample and was one order of magnitude higher than CuCoO 2 _SSR, where excellent ionic conductivities of about 10 −4 S cm −1 were also shown. These results showed that the preparation method used is very relevant to obtaining excellent results in the measured transversal conductivity; in our case, around of one order of magnitude better than sample CuCoO 2 _H was reached. All these values have better conductivities than CIGS:Cr crystalline nanopowders and CuInGaSe 2 (CIGS) chalcopyrite thin films doped with Cr in varying concentrations [93].
From the plot shown in Figure 13, we observe that dc-conductivity increases with the increase of temperature of all mixtures, following an Arrhenius behavior for the thermal activation energy. The measurements of the activation energy calculated from the slopes follow the trend E act (CuCoO 2 _SSR) = 27.4 kJ/mol < E act (CuCoO 2 _SG) = 30.8 kJ/mol < E act (CuCoO 2 _H) = 52.3 kJ/mol, respectively.
These results indicate that the thin films prepared from hydrothermal synthesis have higher activation energy and lower conductivities than the samples prepared from (a) a solid-state reaction where stoichiometric amounts of the above-mentioned powders have been ground with ethanol solution and, after, calcined at a temperature of 800 • C for 5 h. (b) sol-gel; copper(II) nitrate and cobalt(II) nitrate were mixed in ethylene glycol, and after the gelation occurred, it was placed on a magnetic stirring hot plate until a purple color appeared and the substance become darker. The amorphous powder was heated until 800 • C by steps of 50 • C. Figure 14 shows the relationship between the relaxation time obtained from the cut-off frequency where the conductivity changes from a constant value in the Bode diagram (plateau) to increasing with frequency increase for all temperatures. In such circumstances, such as is observed here in the case of CuCoO 2 _H (see Figure 12c) for all temperatures, according to the power low model, the real part of the conductivity σ (ω,T) can be expressed in terms of dc-conductivity σ dc and the hopping diffusion rate of protons ω H ≈ 1/τ (in this case) as [94] σ (ω, T) = σ dc 1 where n is an exponent with a value between 0 and 1 and is related to interactions between mobile ions (H + in our case) and the dimensionally of the conduction pathway [97]; for instance, this occurs in polymer electrolytes of P  80 -ran-PMMA 20 at (308 K to 378 K), respectively [98]. From the fit of the real part of the conductivity shown in the Bode diagrams in Figure 12, we have obtained the values of sample relaxation time; these values are plotted in Figure 14 for each temperature. Sol-Gel SSR-800 SSR-950 ln σ ( σ: (S/cm) 1000/T (K -1 ) Figure 13. Temperature dependence of conductivity determined using Bode graphs for all samples examined.
These results indicate that the thin films prepared from hydrothermal synthesis have higher activation energy and lower conductivities than the samples prepared from (a) a solid-state reaction where stoichiometric amounts of the above-mentioned powders have been ground with ethanol solution and, after, calcined at a temperature of 800 °C for 5 h. (b) sol-gel; copper(II) nitrate and cobalt(II) nitrate were mixed in ethylene glycol, and after the gelation occurred, it was placed on a magnetic stirring hot plate until a purple color appeared and the substance become darker. The amorphous powder was heated until 800 °C by steps of 50 °C. Figure 14 shows the relationship between the relaxation time obtained from the cutoff frequency where the conductivity changes from a constant value in the Bode diagram (plateau) to increasing with frequency increase for all temperatures. In such circumstances, such as is observed here in the case of CuCoO2_H (see Figure 12c) for all temperatures, according to the power low model, the real part of the conductivity σ′(ω,T) can be expressed in terms of dc-conductivity σdc and the hopping diffusion rate of protons ωH ≈ 1/τ (in this case) as [94] σ'(ω, T) = σ 1 + (5) where n is an exponent with a value between 0 and 1 and is related to interactions between mobile ions (H + in our case) and the dimensionally of the conduction pathway [97]; for instance, this occurs in polymer electrolytes of P[VBTC][Cl]80-ran-PMMA20 at different temperatures (303 K to 363 K) and P[VBTC][TFSIl]80-ran-PMMA20 at (308 K to 378 K), respectively [98]. From the fit of the real part of the conductivity shown in the Bode diagrams in Figure 12, we have obtained the values of sample relaxation time; these values are plotted in Figure 14 for each temperature. From Figure 14, we can see that the relaxation time follows an Arrhenius behavior in all the powders studied, but it is interesting to observe that samples prepared using method 2 (CuCoO2_SSR) and method 3 (CuCoO2_SG) have a relaxation time around one order of magnitude smaller than the sample prepared using he method 1 (CuCoO2_H). This means that the method to produce powders to build thin films is very important to determine their optical and electrical properties. In these results, we observe that delafossites are extremely sensitive to a wide variety of parameters: in particular, the method From Figure 14, we can see that the relaxation time follows an Arrhenius behavior in all the powders studied, but it is interesting to observe that samples prepared using method 2 (CuCoO 2 _SSR) and method 3 (CuCoO 2 _SG) have a relaxation time around one order of magnitude smaller than the sample prepared using he method 1 (CuCoO 2 _H). This means that the method to produce powders to build thin films is very important to determine their optical and electrical properties. In these results, we observe that delafossites are extremely sensitive to a wide variety of parameters: in particular, the method used in its preparation. The results indicate that these materials have potential in thin film solar cells.

Theoretical Insight
Theoretical simulations are critical in the understanding of the properties of systems at the atomic level. Therefore, first-principles calculations were performed to complement the experimental results with an insight on the electronic structure and properties. For this purpose, the atomic positions were optimized, and the electronic properties were computed within the Density Functional Theory (DFT) approach. This was conducted based on the framework of the generalized Kohn-Sham scheme [99][100][101] in combination with the projector augmented-wave (PAW) method [102] and the Heyd-Scuseria-Ernzerhof hybrid functional with the modified fraction of screened short-range Hartree-Fock exchange (HSE06) [103][104][105] as implemented in the Vienna ab initio simulation package (VASP) [106][107][108][109][110]. Hybrid functionals allow for a more accurate description of electronic properties of some systems compared to simple DFT calculations with a generalized gradient approximation for the exchange and correlation term in the Kohn-Sham scheme. The higher accuracy, however, is reached at the cost of a higher computational time needed to achieve convergence.
To model the CuCoO 2 in the tetragonal phase, a unit cell with 12 atoms (Co 3 Cu 3 O 6 ) was used, while for the hexagonal cell, a smaller cell with 8 atoms (Co 2 Cu 2 O 4 ) was needed. The electronic wave functions were expanded in a plane wave basis setup to a kinetic energy cutoff of 400 eV. The atomic positions were optimized using the conjugate gradient method up until the forces on each atom were less than 0.01 eV A −1 ; and the energy convergence was less than 10 −8 eV for the optimization and less than 10 −5 eV for calculations with the hybrid functional. For the Brillouin zone integration, a 12 × 12 × 6 Monkhorst-Pack scheme k-point mesh was used [111][112][113][114] both for the optimization and the electronic structure calculation. Figure 15 shows the atom positions and geometrical structure of the converged unit cells. The delafossite structure of this ternary oxide can be appreciated fairly. In the tetragonal structure, an alternate stacking of O-Cu-O dumbbells lie parallel to the z axis, and there is a layer of Co-centered octahedrons in the xy plane. The stacking follows an ABCABC pattern, forming a trigonal system with lattice parameters a = 2.86 Å and c = 16.98 Å, corresponding to a rhombohedral Bravais lattice of volume 120.1 Å 3 , which matches the experimental data [52,99]. In the hexagonal cells, the same layers of O-Cu-O dumbbells and Co-centered octahedron are observed, but with an ABAB stacking pattern. The lattice constant a = 2.83 Å is practically identical, but c = 11.30 Å is significantly lower; the unit cell volume of 78.47 Å 3 is also lower. However, these differences are due to the fact that a smaller distance is enough to represent the structure because of the stacking sequence. Hence, important distances within the unit cell, such as the distances between O atoms in the O-Cu-O dumbbells (3.71 Å for the tetragonal 3.69 Å in the hexagonal) or the distances from a cornered O to a centered Co in the octahedron (1.92 Å for the tetragonal and 1.91 Å in the hexagonal) are practically the same.
The band structure and density of states for the tetragonal phase can be appreciated in Figure 16. Though the inclusion of the hybrid functional allows the possibility of avoiding the typical underestimation of gaps in pure DFT approaches; the bandgap values obtained seems to remain underestimated: 2.31 eV for the tetragonal structure and 2.34 for the hexagonal one (experimental results are between 2.5 to 3.65 eV [77,98,103]). However, the structure of the bands and the form of the density of states of the curves are usually well described in this type of calculations, and despite the small difference in bandgap values for both structures, the form of the density of states is practically the same, so only one of them is plotted. the unit cell volume of 78.47 Å is also lower. However, these differences are due to the fact that a smaller distance is enough to represent the structure because of the stacking sequence. Hence, important distances within the unit cell, such as the distances between O atoms in the O-Cu-O dumbbells (3.71 Å for the tetragonal 3.69 Å in the hexagonal) or the distances from a cornered O to a centered Co in the octahedron (1.92 Å for the tetragonal and 1.91 Å in the hexagonal) are practically the same. The band structure and density of states for the tetragonal phase can be appreciated in Figure 16. Though the inclusion of the hybrid functional allows the possibility of avoiding the typical underestimation of gaps in pure DFT approaches; the bandgap values obtained seems to remain underestimated: 2.31 eV for the tetragonal structure and 2.34 for the hexagonal one (experimental results are between 2.5 to 3.65 eV [77,98,103]). However, the structure of the bands and the form of the density of states of the curves are usually well described in this type of calculations, and despite the small difference in bandgap values for both structures, the form of the density of states is practically the same, so only one of them is plotted.
The obtained gap is an indirect one, which can be appreciated by simple inspection of the bands structure in the left part of Figure 16. The right part shows the density of states in which it is appreciable that the edge of the covalent band is apparently dominated  by Cu-3d states. O states show a wide dispersion through the band, but the presence of Co-3d states is high in this region and, except for the peak at the edge of the band, is comparable with the contribution from Cu states. Also, the first peak in the conduction band is mainly due to Co-3d states followed by a second peak with a structure similar to the one that can be found in CuAlO and CuGaO , as it has been previously reported [98,99,103].

Conclusions
In summary, the preparation of delafossite CuCoO2 using three cost-effective techniques yields a well-ordered crystalline mixture comprising two structures: rhombohedral and hexagonal, exhibiting similar properties and favorable band gap values. To ensure the development of an effective coating solution, careful treatment of the resultant nano-sized precursor powder is necessary. The desired thin films, namely CuCoO2_H (produced via hydrothermal method), CuCoO2_SG (produced via sol-gel method), and CuCoO2_SSR (produced via solid-state reaction method), were successfully obtained through the spray pyrolysis process. Electrochemical impedance spectroscopy measurements reveal that the Sol-Gel method yields films with superior conductivity compared to the other preparation methods. As a result, CuCoO2 thin films hold significant potential for solar cell applications. This is supported by the examination of the electronic properties of the rhombohedral CuCoO2 through theoretical simulations. Furthermore, electrochemical impedance spectroscopy measurements demonstrate that the copper cobalt delafossites prepared using different synthesis methods have the potential to serve as semiconductor materials. The conductivity values, measured through the plane, increase with temperature as expected: σcucoo2_sg > σcucoo2_ssr > σcucoo2_h. Among the three samples, Figure 16. Bands structure (left) and states' density (right) acquired by HSE simulations for the tetragonal structure. Energies are expressed with respect to the Fermi energy. Black line accounts for total DOS in the right part, and colored lines accounts for the contribution of every species to the density of states: Co atoms are represented by pink, Cu atoms by red, and O atoms by green.
The obtained gap is an indirect one, which can be appreciated by simple inspection of the bands structure in the left part of Figure 16. The right part shows the density of states in which it is appreciable that the edge of the covalent band is apparently dominated by Cu-3d states. O states show a wide dispersion through the band, but the presence of Co-3d states is high in this region and, except for the peak at the edge of the band, is comparable with the contribution from Cu states. Also, the first peak in the conduction band is mainly due to Co-3d states followed by a second peak with a structure similar to the one that can be found in CuAlO 2 . and CuGaO 2 , as it has been previously reported [98,99,103].

Conclusions
In summary, the preparation of delafossite CuCoO 2 using three cost-effective techniques yields a well-ordered crystalline mixture comprising two structures: rhombohedral and hexagonal, exhibiting similar properties and favorable band gap values. To ensure the development of an effective coating solution, careful treatment of the resultant nano-sized precursor powder is necessary. The desired thin films, namely CuCoO 2 _H (produced via hydrothermal method), CuCoO 2 _SG (produced via sol-gel method), and CuCoO 2 _SSR (produced via solid-state reaction method), were successfully obtained through the spray pyrolysis process. Electrochemical impedance spectroscopy measurements reveal that the Sol-Gel method yields films with superior conductivity compared to the other preparation methods. As a result, CuCoO 2 thin films hold significant potential for solar cell applications. This is supported by the examination of the electronic properties of the rhombohedral CuCoO 2 through theoretical simulations. Furthermore, electrochemical impedance spectroscopy measurements demonstrate that the copper cobalt delafossites prepared using different synthesis methods have the potential to serve as semiconductor materials. The conductivity values, measured through the plane, increase with temperature as expected: σ cucoo2_sg > σ cucoo2_ssr > σ cucoo2_h . Among the three samples, CuCoO 2 _SG exhibits the highest conductivity of approximately 10 −3 S cm −1 at 120 • C, which is one order of magnitude greater than CuCoO 2 _SSR, while still maintaining good ionic conductivities of approximately 10 −4 S cm −1 . This value is approximately two orders of magnitude higher than that of CuCoO 2 _H. These conductivity measurements, obtained through impedance spectroscopy, are in agreement with the values determined using the four-probe method, where resistivity follows the trend of ρ CuCoO2_SG < ρ CuCoO2_SSR ≈ ρ CuCoO2_H . Lastly, our study demonstrates that samples prepared using method 2 (CuCoO 2 _SSR) and method 3 (CuCoO 2 _SG) have relaxation times approximately one order of magnitude smaller than samples prepared using method 1 (CuCoO 2 _H). This result emphasizes the significant impact that the synthesis method and sample preparation can have on producing powders for building thin films to enhance optical and electrical properties, particularly for solar cell applications.

Data Availability Statement:
The data presented in this study are available on request from the corresponding author.

Conflicts of Interest:
The authors declare no conflict of interest.