Investigation into the Re-Arrangement of Copper Foams Pre- and Post-CO2 Electrocatalysis

the Re-Arrangement of Copper Foams and Post-CO2 The utilization of carbon dioxide is a major incentive for the growing field of carbon capture. Carbon dioxide could be an abundant building block to generate higher value products. Herein, we fabricated a porous copper electrode capable of catalyzing the reduction of carbon dioxide into higher value products such as ethylene, ethanol, and propanol. We investigated the formation of the foams under different conditions, not only analyzing their morphological and crystal structure but also documenting their performance as a catalyst. In particular, we studied the response of the foams to CO 2 electrolysis, including the effect of urea as a potential additive to enhance CO 2 catalysis. Before electrolysis, the pristine and urea-modified foam copper electrodes consisted of a mixture of cuboctahedra and dendrites. After 35-minute electrolysis, the cuboctahedra and dendrites underwent structural rearrangement affecting catalysis performance. We found that alterations in the morphology, crystallinity, and surface composition of the catalyst were conducive to the deactivation of the copper foams. Experimental details Electrocatalysis experiments: CH440c (CH Instruments, USA) and Ivium-n-stat (Ivium Technologies B. V., Netherlands) potentiostat instruments were used for electrochemical measurements and electrolysis. Ivium-n-stat was used for electrochemical impedance spectroscopy for ohmic drop measurements, which was measured at a sinusoidal potential frequency of 10 kHz with 5 mV amplitude centered on the electrolysis potential (-1.6 to -1.4 V vs Ag/AgCl) just before electrolysis. A total of 85% of the measured ohmic drop was compensated for using the potentiostat control software; the remaining 15% (R u ) was manually adjusted for during data treatment usi ng Ohm’s law. Due to variations in ohmic drop and current between experiments, the actual potential difference also varied from run to run. A three-electrode setup was used with a leak-free reference electrode based on Ag/AgCl in 3.4 M KCl (+0.210 V vs SHE; Innovative Instruments Inc., USA), and the counter electrode was a 2.5 cm × 5 cm piece of platinum mesh electrode (99.9% Goodfellow, UK). Potentials are converted to the reversible hydrogen electrode (RHE) scale using eq 1. The pH was measured at Abstract: The utilization of carbon dioxide is a major incentive for the growing field of carbon capture. Carbon dioxide could be an abundant building block to generate higher value products. Herein, we fabricated a porous copper electrode capable of catalyzing the reduction of carbon dioxide into higher value products such as ethylene, ethanol, and propanol. We investigated the formation of the foams under different conditions, not only analyzing their morphological and crystal structure but also documenting their performance as a catalyst. In particular, we studied the response of the foams to CO 2 electrolysis, including the effect of urea as a potential additive to enhance CO 2 catalysis. Before electrolysis, the pristine and urea-modified foam copper electrodes consisted of a mixture of cuboctahedra and dendrites. After 35-minute electrolysis, the cuboctahedra and dendrites underwent structural rearrangement affecting catalysis performance. We found that alterations in the morphology, crystallinity, and surface composition of the catalyst were conducive to the deactivation of the copper foams.

For 35 minute electrolysis experiments a custom-made H-cell was used, constructed as described previously. 1 The cell was filled with 3.5 mL electrolyte on the cathode side and 40 mL electrolyte on the anode side. Carbon dioxide gas was flowed into the electrolyte and maintained at a constant rate of 40 mL/min during electrolysis using a mass flow controller GFCS-010058 (Cole-Parmer, USA). Gas inlet and outlet streams were added to the cell to allow CO2 to enter and escape while keeping the internal pressure of the cell at ambient levels. To take a gaseous measurement 2.5 mL of experimental gas exhaust was injected in the GC, of which 0.4 mL was analyzed.
Gaseous products were quantified using Agilent 7820A gas chromatograph (Agilent Technologies, UK) equipped with a thermal conductivity detector and flame ionization detector coupled to a methanizer, with argon used as the carrier gas. The following gaseous products of CO2 electrolysis were quantified; hydrogen, carbon monoxide, methane, ethylene and ethane as well as oxygen, nitrogen and carbon dioxide. The method was also able to quantify propane, butane, pentane and hexane but these peaks were not present or near the limits of detection. The GC had two columns, HP-PLOT Q which separates hydrocarbons and CO2, followed by HP-PLOT 5A (molecular sieve) column which separate other permanent gases. The two columns were connected by valves which could be programmed to be run in series or bypass mode. The sample peak areas were compared to calibration gases (Calgaz, USA), and quantified according to the equation below. Single point calibration was used to quantify product concentration. Linearity between hydrogen and ethylene concentration and peak area was tested using two mass flow controllers connected to a source of calibration gas and argon carrier gas, the two were mixed before injection into the GC sampling tube.
Faradaic Efficiency = nFPsccν 1000PcCT Faradaic efficiency is given in decimals, n is the number of electrons needed to reduce CO2 to a given product, F is the Faraday constant (96485 Cmol -1 ), Ps and Pc are the peak areas of the sample and the calibration gas respectively, cc is the calibration gas concentration in mol dm -3 ,  is the total volume of gas flowed through the electrolysis cell during electrolysis in cm 3 and CT is the total charge passed through the system during electrolysis in Coulombs.      Figure S5. SEM of CF-18H-100U. a) x75 magnification, b) x3,500 magnification of one of the "cracks" depicting the change in structure with depth. c), cuboctahedra structures interspersed with dendrites from a site below the "crack".      Figure S10. Representative NMR spectrum depicting the peaks attributed to n-PrOH, i-PrOH, EtOH, and acetate. CF-18H at -0.83 V vs RHE. The broad peak at 1.2 ppm could be due to diethyl ether but this peak alone is not enough to report the electroreduction of CO2 to diethyl ether so no such claim has been made.

Introduction
As the concentration of carbon dioxide (CO2) in the atmosphere increases daily, scientists are searching for a way to stem the tide. Carbon capture is becoming ever more efficient and has recently been commercialized by companies such as Climeworks [1,2], and Carbon Engineering [3,4]; however, captured CO2 has marginal commercial value ($3-35 per ton) [5,6]. Therefore, research is being carried out on the sustainable conversion of CO2 into higher-value fuels and related carbon-based products, such as methane, ethylene, and propanol [7][8][9][10]. Nevertheless, it is important to note that currently only CO2 obtained through direct air capture, coupled with electrochemical conversion using renewable energy can be viewed as sustainable [11].
Copper foams have shown good tolerance against minor contaminants as they remain active without electropolishing or scavenging the reaction solution [34,36,39]. The fabrication of copper foams has been previously reported, using electrodeposition. The electrodeposition using the soft templating effect of hydrogen bubbles has been used to generate highly porous copper foam structures on the surface of a copper disc electrode [40,41]. Shin et al. [42] and Kim et al. [43] reported that the addition of chemical additives such as hydrochloric acid (HCl), ascorbic acid, and others could change the size and morphology of the pores. However, in order to be used as an electrocatalyst, the morphology of the microstructures and crystal facets need to be investigated, ensuring that they are optimum for CO2 reduction.
The microstructures and crystal facets of copper strongly contribute to the CO2 reduction mechanism and product distribution [44,45]. Theoretical and experimental research has demonstrated that the cube-like structures such as Cu(100) facet promote the production of ethylene and the Cu(111) facet the production of methane [13]. Moreover, cube-like structures have been found to promote the formation of propanol. Propanol is an interesting CO2 reduction product with current efficiencies and current densities that are commonly low due to the intrinsic complexity of C-C bond formation, [20,46,47] translating into high economic barriers to the commercialization of this process [48]. Kim et al. reported the development of copper nanoparticle ensembles loaded onto carbon paper which rearranged during catalysis into cube-like particles. These particles could convert CO2 into a mixture of n-propanol, acetone, and allyl alcohol with a combined faradaic efficiency of 5.9% at -0.81 V vs RHE [47]. The total current density was 12.7 mA/cm 2 , corresponding to a partial current density jn-propanol ∼ 0.75 mA/cm 2 . Ren et al. designed a copper catalyst with a "high surface population of defects" by electroreducing anodized Cu nanoparticles, leading to nanocrystals in a rough, square shape [49]. Using this catalyst n-propanol was generated with 10.6% faradaic efficiency at -0.85 V vs RHE. Longterm electrolysis was also carried out at −0.95 V, and n-propanol could be continuously produced with a current density of jn-propanol ∼ -1.74 mA/cm 2 for 6 hours. Grosse et al. reported copper nanocubes that underwent structural change during catalysis [50], a small quantity of n-propanol was produced ~1.8% at -0.96 V vs RHE.
Considering the importance of the copper microstructure on CO2 electroreduction, we turned our attention to the fabrication of copper foams under various conditions, aiming to tune the microstructure of the copper foam and its capabilities as an electrocatalyst. In the past, we have reported that the impregnation of a copper foam with poly(acrylamide) enhanced the production of ethylene, reaching faradaic efficiencies of 26% and an overall reduction current density of 60 mA/cm 2 [51] . Therefore, in this work, we further investigated the addition of nitrogen-containing moieties, using urea. The addition of nitrogen-containing moieties can tune the properties of the copper catalyst to potentially give higher current densities, promote C-C bond formation, and lead to greater product selectivity [46,52,53]. We expected the modification of copper foam with the simplest amide, i.e., carbamide, also known as urea, could stabilize carbon monoxide adsorbed intermediates *CO on copper promoting C-C bond formation. Urea was previously used with copper [54] or to electrodeposit copper [55], but not to change the properties of the copper in the attempt to promote C-C bond formation in CO2 reduction. We wanted to establish whether the addition of urea would promote the formation of n-propanol and increase the current density of copper foam catalysts. Interestingly, we found that whilst urea did not enhance selectivity for n-propanol, it instead improved the lifetime of the copper foam impacting on CO2 catalysis.

Copper Foam Preparation
The preparation was adapted from our previous work ACS Catalysis, 2018, 8, 5, 4132-4142 (Ahn et al. [51]). A 3 mm diameter copper rod (99.99%, Goodfellow, UK) was cut into cylindrical pieces and embedded into a polycarbonate body with Araldite epoxy (Huntsman Advanced Materials, Switzerland). The electrode was mechanically polished with 0.3 μm alumina slurry followed by rinsing and ultrasonication in deionized water for 1 min. Copper foam was electrodeposited on the copper disc by submerging in 0.2 M CuSO4, 1.5 M H2SO4(aq) and 4 -73 mm HCl(aq) and applying a fixed cathodic current of 3 A cm -2 for 15 s. Urea modified copper foam was synthesized by (i) dissolving a mass of urea corresponding to 10 -100 mM concentration (ii) dip-coating unmodified electrodeposited copper foam in an H2O solution of 100 mM concentration urea for 1 minute. The electrodeposited foams were submerged in deionized water for 5 min to remove traces of electrodeposition solution before electrochemical measurements.
The foams are denoted as follows: CF-xH, CF-18H-xU, CF-18H-DCU where CF = copper foam, xH = concentration in millimoles of HCl added to electrodeposition bath, xU = concentration in millimoles of urea added to deposition bath, DCU = dip-coated in aqueous 100 mM urea solution.

Material Characterization
Scanning electron microscopy images were taken using field emission gun scanning electron microscopy (FEG-SEM JEOL 7800F). XPS was performed using a Kratos Axis Supra (Kratos Analytical, Japan) utilizing a monochromated Al-Kα X-ray source, 15 mA emission current, magnetic hybrid lens, and slot aperture. Region scans were performed using a pass energy of 40 eV and step size of 0.1 eV. Prior to XPS analysis, the copper foams were dried in a vacuum desiccator for 24 hours. Scans were run of the copper foams after initial synthesis and again after their use as catalysts. It was possible to preclude the presence of CO2 catalysis contaminants such as zinc and lead potentially deposited onto the surface from the electrolyte during electrolysis [56]. XRD measurements were carried out on a Bruker D8 Discover diffractometer with Cu-Kα source radiation (λ = 0.15418 nm). Data were recorded in the 2θ range from 35° -100° in 0.04° increments with a step time of 0.5 seconds.

CO2 Electrocatalysis
The electrocatalysis was carried out following the procedure established by Ahn et al. [51] and is detailed in full in the SI. Minor changes to the previously reported procedure are detailed here. The electrolyte solution was prepared by saturating a 0.1 M KHCO3 solution with CO2 by bubbling at 40 mL min-1 for 1 hour prior to use. The pH of the solution was measured at 6.8. The electrolysis cell was saturated with CO2 gas flowing at 40 mL/min for 5 min before a cathodic potential (-0.70 to -1.04 V vs RHE) was applied. Electrolysis was carried out by setting the voltage at reducing potentials for a total of 35 min. Gas headspace samples were taken from the cell using a gastight syringe for manual injection into the GC sampling loop on the 5 th , 20 th , and 35 th minute. The electrolysis run was temporarily stopped after gas sample injection and the ohmic drop remeasured before starting the next segment. Each set of gas-phase product measurements was repeated at least three times.

Electrocatalysis Product Analysis
Liquid phase products were quantified at the end of the 35 min run using a Bruker AV-500 Nuclear Magnetic Resonance (NMR) instrument running a water suppression experiment [51]. A DMSO standard was added to the NMR tube to make a 0.1 mM concentration. Peak areas of the liquid products were then integrated and compared to the standard to obtain concentrations. Gaseous products were quantified using an Agilent 7820A gas chromatograph (Agilent Technologies, UK), equipped with a thermal conductivity detector and flame ionization detector coupled to a methanizer. A dual column setup was utilized, HP-PLOT Q and HP-PLOT 5A (Agilent Technologies, UK), for the separation of hydrocarbons and permanent gases, respectively. For full details see the supporting information.

Effect of HCl on the copper foams
We decided to vary the hydrochloric acid (HCl) concentration and look at the effects of the different foams on CO2 reduction. In our experiments, the sulfuric acid (H2SO4) concentration was fixed at 1.5 M and the copper sulphate concentration was 0.2 M. The HCl concentration was varied from 4 to CuSO4/0.7 M H2SO4 [43]) and Shin et al. (0.4 M CuSO4/1.5 M H2SO4/1-50 mM HCl [42]).
Scanning electron microscopy (SEM) was used to image the foams (SI Figure S1). The concentration of hydrochloric acid added to the electrodeposition bath affected the morphology of the copper foams. Shin et al. reported that increasing the concentration of HCl in the deposition bath from 1-50 mM altered the morphology of the foam walls, making them higher density [42]. Our copper foams, formed in the presence of small amounts of HCl, had thin wall widths and small pore diameters; large amounts of HCl led to thicker wall widths and larger pore diameters. This is summarized in SI Table S1.
Closer inspection of the structure of CF-18H foam (Figure 1) reveals that the top surface comprises thousands of cube-like structures, technically termed cuboctahedra [57]. Although the electrodeposition of various copper foams has previously been reported, [39, 41-43, 51, 52, 58, 59] to the best of our knowledge, no foams primarily consisting of cuboctahedra agglomerates have previously been observed. The edges of the pores comprise the same type of cuboctahedra interspersed with dendritic structures. Cuboctahedra were also found at the base of the pores (SI Figure S2  In order to investigate the crystal facets of the copper the foams, we have performed an ex-situ Xray diffraction of the foams (XRD, Figure 2). XRD analyses of all of the copper foams show that both Cu metal and Cu2O are present in the foam. The presence of millimolar concentrations of HCl during foam deposition seems not to affect the crystalline orientations of Cu 0 formed. Compared to the Liu foams, ours contained more Cu2O peaks corresponding to different crystalline phases. The same peaks were observed by Dutta et al. in their copper foam electrocatalysts [59]. Our foams have a high surface roughness (vide infra), which would have made them more prone to oxidation. The XRD patterns of our foams show the preferred orientation of Cu(111), with appreciable contribution from Cu(200), and Cu2O(111)/Cu2O(200). To preclude the Cu(111) phase coming only from the copper disc upon which the foam was grown, we also carried out XRD on the copper foam on a carbon tab. The Cu(111) peak is present in the pattern of the copper disc alone, and the copper foam on the carbon tab (SI Figure S3), confirming that the observed peak had contribution from the foam. A preliminary CO2 electrocatalytic activity study of the different copper foams was performed at -0.81 V vs RHE. This potential was chosen as it was the minimum overpotential required to produce appreciable quantities of n-propanol. The liquid products were analyzed, using NMR spectroscopy, to observe which foam was best at converting CO2 to n-propanol. The effect of changing HCl content of copper foam deposition solution, on the electro-catalytic performance of copper foams is shown in SI Figure S4. At -0.81 V vs RHE adding 7 mM HCl into the copper foam deposition bath gave the best faradaic efficiency for n-propanol, about 2.4%. However, the addition of 18 mM HCl gave practically the same (within the experimental error) faradaic efficiency of n-propanol, 2.3%, and greater faradaic efficiency for ethanol production, about 3.3%. Therefore, the 18 mM HCl copper foam was used for further experiments. The gaseous products on 18 mM HCl copper foam were found to be carbon monoxide, ethylene, ethane and the by-product hydrogen (SI Table S2).

Effect of urea on the copper foams
The catalyst fabricated employing 18mM HCl CF-18H, was modified by adding urea in the foam electrodeposition bath to make CF-18H-xU (x represents the concentration in mM of urea employed). The electrodeposited foams were submerged in deionized water for 5 min to remove traces of the electrodeposition solution before electrochemical measurements. The copper foam formed from solutions with added 100 mM urea (CF-18H-100U) has a flattened and less well-defined porous structure compared to CF-18H (SI Figure S5). This indicates that urea affects the deposition of the foam possibly being integrated to form urea-modified copper foams. The wall widths between the pores range from 5.9 -23.5μm, with an average width of 18.2 μm. The pore diameters range from 29.4 -58.8 µm, smaller than CF-18H by 10 µm (data are summarized in SI Table S1).
In Figure 3, the top layer of CF-18H-100U is made of cuboctahedra and the lower layers comprise larger cuboctahedra interspersed with dendritic structures similar to what observed for CF-18H ( Figure  1). The cuboctahedra at the surface are about 180 x 185 nm and the larger cuboctahedra at the bottom of the pores are around 300 x 300 nm. This is a similar size to those reported by Grosse et al. who grew 222 ± 47 nm copper cubes on carbon paper and copper foils [50]. The porous network spreads throughout the structure. Small cracks are observed in the urea-modified copper foam structure and are shown in detail in SI Figure S5. The structure around the crack comprises cuboctahedra interspersed with dendrites and therefore no overall change in the foam is caused as a result of the cracks. The copper foam dip-coated in urea, CF-18H-DCU, exhibited a structure substantially like that of CF-18H confirming that no morphological changes were observed upon wetting with the urea solution. Figure 4 depicts the top, edge and bottom of a pore in CF-18H-DCU. The dendritic copper coats the copper disc electrode at the bottom of the pore, but the cuboctahedra make up most of the pore edge. The cuboctahedra at the top of the pore are approximately 650 x 850 nm (height x width). At the bottom of the pore, the cuboctahedra are smaller, about 500 x 500 nm. These cuboctahedra are comparable in size with the largest of the copper cubes tested by Grosse et al. [50] (580 nm) who demonstrated that a larger cube size leads to greater selectivity for the formation of CO2 reduction products over the competing hydrogen evolution reaction. The 580 nm cube size also leads to the highest faradaic efficiency for n-propanol produced, compared to the other two cube size tested (220 and 320 nm).  The presence of urea on the copper surface was confirmed using X-ray photoelectron spectroscopy (XPS) and the spectra are presented in Figure 6. Nitrogen was detected in both copper foams modified with urea. There was no nitrogen in the CF-18H sample, which had no urea (SI Figure S6). The protonation state appeared to affect the binding of urea on copper. The foam CF-18H-100U deposited from acidified urea solution showed a single nitrogen signal at 400.0 eV (red dotted trace in Figure 6a) possibly corresponding to urea bound to the copper foam through nitrogen. It is known that in acidic media the carbonyl oxygen of urea is protonated [60] leaving the nitrogen-free to interact with copper. This was also observed in the case of CF-18H-DCU, though the XPS signal consisted of the convolution of two peaks at 399.8 eV and 398.9 eV (blue dotted trace in Figure 6a). The peak at 399.8 eV (purple trace) can be assigned to urea bound to copper through nitrogen, related to the 400.0 eV peak of CF-18H-100U. The peak at 398.9 eV (green trace) is tentatively assigned to urea bound to copper through the carbonyl group [51]. The copper 2p signals are consistent for all samples and confirm the presence of copper metal (Fig. 6b). Weak satellite peaks are observed around 947 eV. These are consistent with the presence of Cu2O, which was also observed by XRD. The most intense feature of the copper Auger signal of CF-18H-100U is found at 918.4 eV, consistent with the CF-18H copper Auger (Figure 6c). However, the Auger of CF-18H-DCU shows a stronger feature at 916.1 eV compared to 918.4 eV. The peak at 916.1 eV is dominant and indicates a surface richer in Cu2O over Cu in the case of the dip-coated foam [61].
The electrochemical properties of the CF-18H and CF-18H-100U, in addition to the dip-coated catalyst CF-18H-DCU, were also compared. The double-layer capacitance method of determining the electrochemically active surface area was used [62]. As shown in Table 1, the copper foams have similar electrochemically active surface areas (ECSA) meaning that they are unaffected by the addition of urea in the deposition bath or dip-coating step. The foam surface area is 225 to 240 times larger than the electrode geometric surface area for the sample prepared using 18 mM HCl without and with urea, respectively. This is double that observed in our previous work, [51] and quadruple of that achieved by Dutta et al. [59]. The cyclic voltammograms and corresponding current vs scan rate plots are provided in SI Figure S7, the current density calculations in SI Table S3.

CO2 electrocatalytic activity of foams
The CO2 electrocatalytic activity of the copper foams deposited in the presence of different amounts of urea (CF-18H-xU) was tested at -0.83 V vs RHE. The liquid products of the urea copper foams are depicted in SI Figure S8. The faradaic efficiency increases with the concentration of urea until ~ 60mM, afterwards, a plateau is observed, making CF-18H-100U the foam of choice for further study. The three foams CF-18H, CF-18H-100U, and CF-18H-DCU were then tested for their activity as CO2 reduction catalysts at various potentials in 0.1 M KHCO3 solution while bubbling CO2 at 40 mL/min. All products of electrocatalysis for CF-18H and CF-18H-100U are available in Figure 7 and SI Figure S9. We note that the CO2 electrolysis experiments were affected by significant variability, as also observed in other studies [14,15,63]. In some instances, the values of faradaic efficiency of one material fell within the error bars of the other and vice versa. In such a case no claim could be made for either of the two catalysts, CF-18H and CF-18H-100U, performing better than the other, particularly in the case of n-propanol production (Figure 8c). However, some significant differences could be appreciated such as the CF-18H foam promoting the electroreduction of CO2 to ethylene more effectively than the CF-18H-100U foam at -0.93 V vs RHE. Interestingly, i-propanol was generated using the CF-18H foam, albeit in small quantities -the maximum average faradaic efficiency is 0.87% at -0.93 V vs RHE (SI Table  S4). This was lower for CF-18H-100U, 0.11%. A representative NMR spectrum is depicted in SI Figure  S10 for CO2 electrolysis using CF-18H at -0.83 V vs RHE. The dip-coated catalyst CF-18H-DCU demonstrated a different catalytic trend with n-propanol increasing with more negative potentials (SI Figure S11) compared to CF-18H and CF-18H-100U. For CF-18H and CF-18H-100U, the C1, C2, and C3 product distributions resulting from the electrocatalytic reduction of CO2 are shown in Figure 8. As the potential became more reductive the overall faradaic efficiency for carbon-based products decreased progressively in favor of hydrogen evolution (data are summarized in SI Table S4).
However, at more negative potentials, there was also a trade-off in the production of more C2+C3 products (ethylene + propanol) in place of C1 products. At -0.70 V vs RHE, only C1 products were detected in the form of carbon monoxide and formate, but no methane. C2 and C3 products were first observed at -0.75 V vs RHE. At -0.83 V vs RHE C2+C3 products were dominant over C1 products, a trend which continued with increasing potential. Trace amounts of methane and methanol were only observed at this potential. n-Propanol was the dominant C3 product and production peaked at -0.83 V vs RHE. i-Propanol and trace amounts of acetone were the other C3 products observed.

Post-catalysis characterization
The CF-18H and CF-18H-100U foams were characterized after catalysis to look at their response to the applied potential. The analysis in this section is based on results gained from ex-situ measurements including SEM, XRD and XPS. SEM revealed that multiple cracks had formed both on the surface and further into the porous network of CF-18H. The cuboctahedra observed before electrolysis (Figure 1), were no longer present after 35 mins of electrolysis ( Figure 9). The dendrites, a minor component in the as-prepared foams, became the only component of the foam after electrolysis, as shown in Figure 9b. This same phenomenon was observed for CF-18H-100U. The cuboctahedra, present as the major component of the foam before electrolysis (Figure 3), are no longer present after 35 mins (Figure 9f). Therefore, we hypothesize that the copper foam responded to the process conditions of CO2 electrolysis by re-arranging in-situ during catalysis.
XRD analysis of the copper foams after electrolysis corroborated the findings in the SEM of less crystalline materials ( Figure 10). For CF-18H the peak intensity was reduced and, as can be observed in Figure 10a, the peaks are generally broader, indicative of smaller crystallite size. The rise of baseline at low diffraction angles suggests that an amorphous phase was also formed upon catalysis. Post-catalysis there was a significant increase in the relative peak intensity for Cu(200); pre-catalysis the Cu(111):Cu(200) ratio was 1:0.14, post-catalysis it was 1:0.39 with a significant loss of Cu(111) domains. There is also a small yet detectable peak at 47.5° tentatively assigned to the presence of trace amounts of CuCl(220) phase [64] (Figure 10a), which is localized on the surfaces of the foam as seen from the Cu LMM Auger spectra discussed later. Although care was taken to avoid any contamination in the CO2 electrolysis cell, there appears to have been a trace amount of chloride ions in solution to form insoluble Cu2O-derived CuCl [64]. It follows that chloride contaminations were introduced during the electrolysis possibly due to the Ag/AgCl reference electrode and the small solution volume in the cathodic compartment (3.5 mL). Comparable changes were observed for CF-18H-100U (Figure 10b). In line with the transition of the copper from cuboctahedra to dendrites, there is also a decrease in the Cu2O(311) facet and an increase of Cu2O(222). CF-18H-100U displays an increased orientation of the Cu(220) phase and a more equal spread of orientations post-electrolysis. Figure 10. The XRD patterns of (a) CF-18H and (b) CF-18H-100U before electrolysis (bottom black pattern) and post 35-min electrolysis (top red pattern), offset for clarity. For each material, both spectra were normalized to their respective Cu(111) peak and scaled to the 'before electrolysis' Cu(111) peak.
The presence of chloride contaminations was also observed in the XPS spectra of the foams after electrolysis (Figure 11). Before electrolysis, the Auger signal of CF-18H is typical for copper metal, with its most intense feature centered at 918.7 eV [65]. After 35-min electrolysis, the main feature is found to 915.6 eV, which is attributed to CuCl [66,67]. The Cu Auger of CF-18H-100U displays similar behavior, although it retains a higher Cu metal content post-electrolysis, compared to CF-18H. Corresponding peaks were observed in the Cl 2p spectra (SI Figure S12 for a representative spectrum). Comparatively more CuCl is present in the post-catalysis XPS spectra of CF-18H than for CF-18H-100U. For CF-18H and CF-18H-100U, the Cu 2p peaks were unchanged before and after 35 minutes of electrolysis (SI Figure S13, to be compared with Figure 6b). For CF-18H-DCU, both Cu2O and copper metal are present on the surface of the foam before electrolysis, with the Cu2O Cu(LMM) becoming dominant after 35 minutes (Figure 11c). A key concern of the work was whether the urea would withstand the electrolysis conditions and remain bound to the copper foam surface. XPS analysis after 35 minutes of electrolysis was carried out to verify this. The dip-coated and non-dip-coated foams behaved differently. CF-18H-100H started with all the nitrogen in one environment at 400.3 eV ( Figure 12). However, after electrolysis there were two nitrogen environments, 398.9 eV and 400.3 eV. As stated earlier in the paper, we ascribe the peak at 398.9 eV to urea bound to the copper through the carbonyl, whereas the peak at 400.3 eV is assigned to urea bound through the amine. We assume that the acid present in the formation of CF-18H-100U protonates the carbonyl oxygen of the urea [60], forcing urea to coordinate through the amine groups (giving rise to the single peak at 400.3 eV pre-catalysis). In the alkaline environment during catalysis (due to proton consumption) the urea carbonyl group is de-protonated, allowing the urea to bind to copper in its preferential form, through the carbonyl group, giving rise to the peak at 398.9 eV. Some urea must continue to bind through the amine groups to leave the minor peak at 400.3 eV. In contrast, for CF-18H-DCU, urea is coated onto the copper foam from a pH 7 aqueous solution. Urea in water hydrates on both carbonyl and amine sides [68], leading to a mixture of nitrogen-bound and carbonyl-bound urea on the copper surface before electrolysis ( Figure 12). After catalysis, most of the urea seems instead to be predominantly carbonyl-bound. We tentatively suggest that the difference in reactivity between CF-18H-100U and CF-18H-DCU could in part be due to the binding modes of the urea at the start and during catalysis. The complex and numerous changes observed upon electrolysis have a significant impact on the catalytic activity of the copper foams. CF-18H showed no catalytic activity for n-propanol after 2 hours of electrolysis, whereas CF-18H-100U was still active with a faradaic efficiency of about 1%.

Conclusions
This work describes a procedure for the fabrication of cuboctahedral porous copper electrodes under various conditions. The formation of the foams was analyzed using different concentrations of HCl during electrodeposition. It was confirmed that the concentration of HCl affects the average wall width and pore size of the foam, thereby making them respectively thicker and larger at higher HCl concentrations. The addition of urea did not significantly change the crystalline structure of the resulting urea-modified foams. Correspondingly, we did not observe a significant change in the faradaic efficiency of CO2 conversion to n-propanol between plain and urea modified foams.
After CO2 electrolysis, the foam changed from a cuboctahedral to a dendritic morphology, suggesting that the copper responded to CO2 electrolysis by re-arranging in-situ during catalysis. The re-arrangement of the copper has been characterized ex-situ using SEM and corroborated with XRD. The presence of urea and its method of binding to the copper seems to have affected the catalyst response and structure-activity relationships. Indeed, pristine foams showed no catalytic activity for npropanol after 2 hours of electrolysis, while urea-modified foams continued showing faradaic efficiencies of about 1%.