Plasmonic Au–Pd Bimetallic Nanocatalysts for Hot ‐ Carrier ‐ Enhanced Photocatalytic and Electrochemical Ethanol Oxidation

: Gold–palladium (Au–Pd) bimetallic nanostructures with engineered plasmon ‐ enhanced activity sustainably drive energy ‐ intensive chemical reactions at low temperatures with solar simu ‐ lated light. A series of alloy and core–shell Au–Pd nanoparticles (NPs) were prepared to synergisti ‐ cally couple plasmonic (Au) and catalytic (Pd) metals to tailor their optical and catalytic properties. Metal ‐ based catalysts supporting a localized surface plasmon resonance (SPR) can enhance energy ‐ intensive chemical reactions via augmented carrier generation/separation and photothermal con ‐ version. Titania ‐ supported Au–Pd bimetallic (i) alloys and (ii) core–shell NPs initiated the ethanol (EtOH) oxidation reaction under solar ‐ simulated irradiation, with emphasis toward driving carbon– carbon (C–C) bond cleavage at low temperatures. Plasmon ‐ assisted complete oxidation of EtOH to CO 2 , as well as intermediary acetaldehyde, was examined by monitoring the yield of gaseous prod ‐ ucts from suspended particle photocatalysis. Photocatalytic, electrochemical, and photoelectro ‐ chemical (PEC) results are correlated with Au–Pd composition and homogeneity to maintain SPR ‐ induced charge separation and mitigate the carbon monoxide poisoning effects on Pd. Photogener ‐ ated holes drive the photo ‐ oxidation of EtOH primarily on the Au ‐ Pd bimetallic nanocatalysts and photothermal effects improve intermediate desorption from the catalyst surface, providing a method to selectively cleave C–C bonds.

EtOH is an attractive nontoxic chemical fuel owing to its existing supply chain, carbon-neutral production from agricultural biomass, high theoretical energy density (~8 kWh•kg −1 ), and simple storage and infrastructure [2,[30][31][32]. Further, the EOR has the capability for H2 generation via catalytic deprotonation under neutral to acidic conditions. The desired EOR pathway is a high-energy (ΔG = −1326.7 kJ/mol), 12-electron process that requires multiple electron transfer steps for the C1-overall reaction(s) in low and high pH [2]: [High pH] CH CH OH 16OH  2CO 11H O 12e (2) Breaking the carbon-carbon (C-C) bond has been found to be the rate-limiting step, as the EOR is interrupted by the production of two C2-intermediates: acetaldehyde (CH3CHO, n = 2e − ) first, and then further by acetic acid (CH3COOH, n = 4e − ). The C2-intermediate(s) can obstruct active sites by adsorbing in inactive orientations and possess high energetic barriers for cleaving the C-C bond (>1.0 eV); limiting further oxidation [30,[32][33][34].
[Low pH]  2 2 (3) CH CH OH O CH COOH 4 4e (4) [High pH] CH CH OH 2OH  CH CHO 2H O 2e (5) CH CH OH 5OH  CH COO 4H O 4e (6) Alkaline media (pH ≥ 14) enables preferred deprotonation of the sterically hindered acetaldehyde intermediate to the [CH2CHO] − anion (pKa = 13.6) and facilitates proper surface alignment for C-C bond cleavage [2,25,30,32,34]. Therefore, the complexity of the EOR necessitates that the catalyst of interest can selectively activate C-C bond cleavage for complete oxidation. The reaction rate for Au is dependent on the deprotonation step, whereas further oxidation is deterministic for catalytic metals (i.e., Pd). Therefore, Pd is one of the most active catalysts for the EOR, while Au is considered to have poor activity [25,30,33,34]. However, the catalytically active Pd lacks a strong SPR absorption for visible-light excitation and is susceptible to catalyst poisoning. Alloying or coupling Pd with plasmonic metals has shown improved catalytic reactivity compared to mono-metallic alternatives [5,20,28], and is hypothesized to enhance the EOR activity.
The coupling of plasmonic and catalytic metals to semiconductive TiO2 is a cost-effective alternative to using pure Pd catalysts to address challenges associated with product selectivity and total conversion of EtOH. This work leverages high-resolution electron imaging techniques (i.e., STEM), photocatalytic and PEC measurements of EOR, and discrete dipole approximation (DDA) computation to provide new, quantitative insights into understanding the role of plasmonic "hot" carriers in C-C bond cleavage during the EOR [35,36]. The synthetic preparation of bimetallic nanoparticles synergistically couples Au plasmonic absorbers with catalytic Pd, with the goal of tailoring their optical and catalytic properties. The effects of composition (i.e., Au1-xPdx) and nanostructuring of the bimetallic nanoparticles (i.e., alloy vs. core-shell) on the plasmonic enhancement of the wide band gap TiO2 are presented. Low-temperature photo-oxidation of EtOH was studied via suspended particle photocatalysis and electrochemical methods, with EOR performance directly correlated to alloy homogeneity. Plasmonic catalyst structural and elemental morphologies were optimized to improve "hot" carrier generation and separation.

Gold-Palladium Alloys
Gold-palladium bimetallic alloy nanoparticles (Au1-xPdx NPs) were prepared with the compositions Au, Au0.9Pd0.1, Au0.75Pd0.25, Au0.5Pd0.5, Au0.25Pd0.75, Au0.1Pd0.9, and Pd using a protocol reported in Reference [5]. First, the dark orange Pd precursor solution, 10 mM H2PdCl4, was prepared following our previously reported methodology [5,28]. Briefly, the desired compositions of the Au1-xPdx NP growth solutions were achieved by appropriately adjusting the mole ratio of 10 mM HAuCl4•3H2O and/or 10 mM H2PdCl4. Surfactant solution utilized to direct bimetallic alloy NP growth was 25 μM PVP-40 in 20% EtOH/80% deionized water. Precursors were combined with the surfactant solution to yield an orange-colored growth solution. A fresh solution of 0.100 M ascorbic acid was prepared and 110 μL was added to the growth solution as a weak reducing agent, which was stirred for 60 min at 100 °C. The solution colors ranged from red to brown, yielding the desired Au1-xPdx NP compositions [5].

Deposition of Au-Pd on Catalyst Supports
After purification, the Au-Pd NP samples were deposited onto TiO2 and carbon supports. TiO2 was mixed with 1 wt.% Au-Pd NPs, sonicated to thoroughly disperse, and the well-mixed slurry was stirred for 48 h. Au-Pd NPs dispersed on TiO2 were collected using a centrifugation and washing procedure (at 8500 rpm for 45 min). Supernatant was tested via ultraviolet-visible (UV-Vis) spectroscopy after washing to confirm the complete deposition of Au-Pd NPs onto TiO2. Samples were dried at 80 °C for 24 h to remove excess solvent, yielding uniform powders ranging from purple to dark gray in color. Au-Pd NP samples were deposited onto XC-72 carbon supports via ligand-exchange-induced destabilization. An NP loading of 1-20 wt.% by total mass of Au and/or Pd (assuming a theoretical yield of 100%) was used for each XC-72 support. XC-72 carbon powder was added to 15 mL of t-BuNH2 and thoroughly dispersed via ultrasonication. Previously prepared Au-Pd NP samples were redispersed in EtOH, mixed with XC-72/BuNH2 suspension, and stirred magnetically for 24 h for ligand exchange and NP deposition. Au-Pd NPs on carbon supports were isolated via 30 mL EtOH addition and centrifugation (8500 rpm for 45 min) and dried at 80 °C.

Working Electrode Preparation
Catalyst suspensions were prepared by dispersing the TiO2-and carbon-supported Au-Pd in 1:1 EtOH:H2O and 1 vol% Nafion solution via ultrasonication for 15 min to obtain a final catalyst concentration of 6 μg•μL −1 . The catalyst suspension (10 μL) was dropcast onto a glassy carbon electrode (0.196 cm −2 ). After excess solvent evaporation, 3 μL of a diluted Nafion solution (20% v/v in EtOH) was deposited onto the catalyst layer to improve its physical stability and electrical conductivity. Electrode surfaces were allowed to completely dry prior to EOR electrochemical measurements.

UV-Vis Spectroscopy and Electron Microscopy
Absorbance spectra collected from UV to near-infrared (NIR) for the Au1-xPdx and AuCore-Au1-xPdx.Shell NPs in solution were obtained with an AvaSpec-ULS2048L spectrometer fiber-coupled deuterium and halogen light source, while diffuse reflectance measurements of the Au-Pd on TiO2 powders required the addition of an Avasphere-30 PTFE integrating sphere. Bright-field TEM and high-angle annular dark-field imaging scanning TEM (HAADF-STEM) was performed in JEOL 2100F (Peabody, MA, USA) at 200 kV equipped with an EDAX Octane T Optima system (Mahwah, NJ, USA) energy dispersive X-ray spectrometer (EDXS) to map the elemental distribution on the Au-Pd on TiO2 composites. Principal component analysis differentiated raw EDS spectra into six uncorrelated variables: Au, Pd, Ti, O, C (the support film), and background (surfactant, residual solvent, etc.). Samples were prepared by drop-casting onto solid carbon films for the Au1-xPdx and AuCore-Au1-xPdx.Shell NPs and lacey carbon films for the Au-Pd on TiO2 powders.

X-ray Photoelectron Spectroscopy
X-ray photoelectron spectroscopy (XPS) was carried out on a Physical Electronics VersaProbe III (East Chanhassen, MN, USA) with a monochromated Al Kα source with a 100 μm diameter 25 W beam, 55 eV pass energy, and a take-off angle of 45°. Surface charging was neutralized by a low-voltage Ar-ion beam and a barium oxide neutralizer. Spectra were energetically corrected to a 284.8 eV C 1s line and baseline corrected to a Shirley model. Peak fitting was performed with Physical Electronics' MultiPak software v9.6.0.15. Samples were prepared by drop-casting 5 μL of NP−solvent solution onto glass substrates.

Numerical Computation
Electric near-field enhancements and SPR properties were studied and quantified using the discrete dipole approximation (DDA) package DDSCAT v7.3 by Draine and Flatau [37][38][39]. DDA uses Maxwell's equations to quantify absorption and scattering of an electric plane wave incident upon a subwavelength NP, discretized into a three-dimensional ensemble of point dipoles susceptible to electric polarization according to their specified dielectric response [6,28,29,40]. Nanoparticle targets were generated using a custom MATLAB (v9.2, MathWorks, Natick, MA, USA) script based on Reference [29] according to the TEM-measured mean dimensions, with a 10 nm diameter Au1-xPdx NP and 24 nm AuCore-Au1-xPdx.Shell NP in the presence and absence of contacting anatase TiO2 (25 nm diameter) in water (n = 1.33). The inter-dipole spacing was 0.5 nm. The DDA models presented herein consider only the anatase phase of TiO2 owing to both the anatase and rutile phases of TiO2 exhibiting a nearly identical dispersive dielectric behavior in the sub-band gap visible spectrum [6]. Therefore, under sub-band gap visible-light irradiation, the anatase and rutile forms are optically equivalent as they both screen the plasmon resonance.

Photocatalytic Measurements
Gas chromatography-mass spectrometry-multiple headspace extraction (GC-MS-MHE) was performed on an Agilent Technologies 5975C Series GC/MSD, with Triple-Axis HED-EM Detector coupled to an Agilent 7697A Headspace Sampler utilized to perform headspace analysis of the photo-oxidation experiments. Sample vials were equilibrated at 60 °C under dark conditions for 20 minutes, and the headspace was extracted for the dark/thermal background [6]. Catalyst supports were used in all photocatalytic experiments. Photocatalytic EOR measurements of 1 wt.% Au-Pd cocatalysts loaded on TiO2 samples (5 mg total) were performed in 0.010 M HClO4 + 0.50 M EtOH. NP suspensions were irradiated in purged GC-MS-MHE glass vials excited with solar-simulated light (i.e., denoted AM1.5G) using a 300 W Xe arc-lamp. The power density for the AM1.5G experiments (> 350 nm) was set to 100 mW•cm −2 (i.e., ®∼1 Sun). Photoreactor cells were irradiated for 1-4 h under constant stirring, and gaseous products were detected post-irradiation.

Electrochemical Measurements
Catalyst supports (i.e., TiO2 and C) were used in all electrochemical experiments. Electrochemical rotating disk electrode (RDE) hydrodynamic measurements were performed in a three-electrode custom-made quartz cell on a Solartron potentiostat. The three electrodes utilized were an Ag/AgCl reference electrode (4 M KCl with AgCl solution), a Pt coil counter electrode (4.7 cm 2 ), and the Au-Pd NPs on TiO2 and carbon support deposited on polished glassy carbon (i.e., 0.196 cm −2 ) as the working electrodes. All measurements were temperature-controlled at 25 °C with water circulated through the outer jacket of the quartz cell. Prior to electrochemical measurements, N2 was bubbled in solution for 30 min and then placed in the headspace to maintain the sparged solution. A sequential cycling method was used to measure the Au-Pd working electrodes in 1 M KOH supporting electrolyte at 200, 100, 50, 20, and 5 mV•s −1 , with the addition of 0.50 M EtOH for the EOR measurements. For the 200, 100, and 50 mV•s −1 scan rates, the working electrodes were cycled 25 times each, whereas for the 20 and 5 mV•s −1 scan rates, the electrodes were cycled 10 and 3 times each, respectively, under rotating conditions (ω = 400 rpm) to achieve reproducible cyclic voltammograms (CV) [30]. Chronoamperometric (CA) measurements were obtained with an applied bias of + 0.72 V (vs. reversible hydrogen electrode (RHE)) for 2150 s under chopped light irradiation (250 s light on/light off). The RDEs were irradiated with solar-simulated light (i.e., AM1.5G filter).

Synthesis and Characterization of Au-Pd Bimetallic NPs
Gold-palladium bimetallic nanoparticles (Au1-xPdx and AuCor-Au1-xPdx.Shell NPs) were prepared using stock solutions of Au and Pd chloride precursor salts in a modified colloidal synthetic method with systematic variation of the composition. High-temperature (100 °C) growth conditions were used in the preparation of Au1-xPdx NPs to improve the nucleation and growth of homogeneous alloys. Alloyed Au1-xPdx NPs maintained their integrity after being coupled to the 3.2 eV bandgap semiconductor TiO2 and were character-ized by STEM-HAADF imaging [5] and EDXS elemental maps shown in Figure 1. Monodisperse spherical morphologies exhibited average particle diameters for Au (23.3 ± 8.7 nm), Au0.9Pd0.1 (7.3 ± 5.9 nm), Au0.75Pd0.25 (2.9 ± 0.6 nm), Au0.5Pd0.5 (5.9 ± 3.6 nm), Au0.25Pd0.75 (7.6 ± 4.5 nm), and Pd (1.7 ± 0.6 nm) determined from statistical analysis of TEM images [5]. Elemental analysis of the NPs using STEM-EDXS spectra confirmed the average composition reflects the desired loading after subtracting TiO2 background, as shown in the Supplementary Figure S1. The Au-Pd distribution was synthetically controlled in a heterogeneous manner using core-shell growth techniques. Heterogeneous core-shell NPs were grown at low-temperature conditions (30 °C) in a two-step synthesis method: (1) growth of the Au NP core and (2) deposition of the desired Au1-xPdx shell. Shell thickness was varied by increasing the loading in the second synthesis step from 1 to 10 mol% for a Au0.5Pd0.5 (AuPd) and Pd shell. The two-step coreshell synthesis method resulted in homogenous, faceted icosahedron Au core NPs with thin homogeneous shells that continued the growth pattern, as shown in Figure 2. Elemental mapping of Au and Pd via EDXS, shown in Figure 2, revealed a core-shell structure with 1-2 nm AuPd and Pd thick shells. Compositions of the core-shell NPs were confirmed by STEM-EDXS, shown in Supplementary Figure S2. XPS in Figure 3 and Supplementary Figure S3 confirmed the presence of metallic Au and Pd species for the alloy and core-shell NPs by the Au 4f peaks at 83.7 and 87.4 eV and the Pd 3d peaks at 335 and 340 eV binding energies. Au exhibits convoluting 4d peaks in the binding energy region of Pd 3d as well but is suppressed with increasing Pd content. XPS analysis of the Au and Pd species for the Au0.9Pd0.1 alloy closely resembles both the AuCore NPs with 10% AuPd and 10% Pd shell. XPS-measured valence band (VB) density-of-states (DOS) in Figure 3 and Supplementary Figure S4 revealed a shift in d-band onset toward the EF (i.e., 0 eV binding energy) and an increase in the DOS at the EF with an increase in Pd content, a signature of Pd observed in density functional theory (DFT) calculations and measurements of other Au-Pd bimetallics [30,35,40,41]. Modifying the position of the d-band center relative to the EF for Au-Pd arises owing to the inherent properties of Pd. Additionally, mechanical strain and/or direct charge transfer between the two metals can take place in alloy and core-shell NPs; designated the ligand effect. The ligand effect can impact how molecules adsorb to the catalyst surface and subsequently modify the Au-Pd catalytic activity [18,42]. The EF of both Au and Pd lie lower in energy in relation to the conduction band (CB) minimum of TiO2, with the DOS increasing at the EF with an increase in the Pd content [43].
Compared to the alloyed Au1-xPdx NPs, the AuCore-Au1-xPdx.Shell NPs exhibited facets with expanded average particle diameters due to secondary AuPd and Pd growth. Size distributions were determined from the statistical analysis of HAADF-STEM images and yielded average particle/shell diameters for the AuCore NPs with a 10 mol% AuPdShell (45.5 ± 13.9 nm overall diameter, 1.2 ± 0.5 nm shell thickness) and 10 mol% PdShell (30.5 ± 12.6 nm overall diameter, 1.3 ± 0.6 nm shell thickness). Notably, tensile strain in the epitaxial thin shell enables the ligand effect to aid in modifying the d-band of the core-shell NP, which is absent for thicker shells (i.e., 7-9 nm) [18]. AuPd and Pd shell growth appeared to follow an epitaxial-like Frank-van der Merwe mode over the AuCore NP in Figure 2, and was consistent with related studies [26,29]. AuCore-Au1-xPdx.Shell NPs synthesized using the same procedure using < 10 mol% Pd yielded thinner AuPd and Pd shells with a lack of distinct crystal facets. Overall, chemical reductive deposition of thin AuPd and Pd shells onto AuCore NPs yielded an epitaxial interface for optimal Au-Pd optical characteristics to promote photocatalytic charge excitation and transfer.
UV-Vis spectroscopy was used to characterize the optical properties of the Au1-xPdx and AuCore-Au1-xPdx.Shell NPs in solution, shown in Figure 4 and Supplementary Table S1, Figures S5 and S6. Pure Au NPs exhibited a λMax of 526 nm, but the relative intensity of the plasmonic resonance rapidly decayed by 50% after incorporating 10% Pd. Au is responsible for the plasmonic response at visible wavelengths, while Pd does not support visible SPR [18]. Pd exhibits a d-band center closer to the EF, causing the optical response to be dominated by interband transitions and dampen the localized SPR at all frequencies, making it spectrally broad and lower in intensity [18,28]. Therefore, the rapid dampening of the SPR with increasing Pd observed for the alloys in Figure 4a is indicative of the homogeneous mixing of Pd into Au. In contrast, the core-shell morphologies in Figure 4b retain a strong plasmonic response (λMax) at 530 nm, with linewidth expansion of the SPR peak (λMax) owing to the Pd-containing shell layers. Spectral broadening observed at longer wavelengths (> 650 nm) is attributed to Pd in the alloyed and core-shell compositions. Observable changes in the SPR were ostensibly due to the emergence of additional plasmon damping pathway(s) for the Au1-xPdx and AuCore-Au1-xPdx.Shell NPs [36,44,45].   Figure 4c,d, prepared powders exhibit a red-shifted SPR response compared to the alloys (≥ 50% Au) and core-shell NPs in solution by ~20 and ~15-20 nm, respectively. Interestingly, the plasmonic response was still present on TiO2 composites but appeared more prominent for the alloy NPs (i.e., ≥ 10% Pd) after coupling to TiO2, attributed to the dielectric screening interaction of TiO2 [6]. The λMax of the alloys on TiO2 blue-shifted with increasing Pd content, from 547 nm for Au to 450 nm for Au0.1Pd0.9. For the core-shell NPs, the λMax of AuPdShell red-shifted by ~4 nm in comparison to the PdShell owing to the Au in the shell. DDA was used to model and quantify the plasmonic interactions of metal NPs in physical contact with TiO2 [6]. Local spatial distributions of the enhanced electric field intensity (|E/E0| 2 ) and far-field optical spectra of Au1-xPdx-TiO2 and AuCore-Au1-xPdx.Shell-TiO2 heterodimers are shown in Figure 5, as well as Supplementary Table S1 and Figure  S8. In each case, the strongest near-field enhancement magnitude is depicted at the heterodimers' calculated resonance wavelength for horizontal polarization (i.e., across x-axis). Au1-xPdx NPs were approximated as 10 nm, AuCore-Au1-xPdx.Shell NPs as 30 nm AuCore with 2 nm shells, and P25 as 25 nm in all cases. Composition was varied based on known dielectric functions for Au and Pd, as well as that previously determined for AuPd [30]. In Figure 5a,b, pure Au NPs exhibited the strongest electric field enhancement followed by AuPd and Pd compositions, which exhibited similar intensities. Therefore, the electric field enhancement should not have a pronounced effect on the photocatalytic activity when comparing AuPd and Pd. However, the ligand effect and other SPR properties (hotcarrier injection and photothermal effects) of AuPd will significantly impact their catalytic activity for EOR compared to monometallic Pd. Au-Pd nanomaterials and TiO2 exhibit energy localization at the plasmonic metal-semiconductor interfaces via dipole SPR excitations. DDA-simulated absorbance efficiency spectra of the Au-Pd NPs without TiO2 ( Figure 5c) and with TiO2 ( Figure 5d) were in good agreement with the experimentally determined SPR λMax peak positions shown in Figure 4 and Supplementary Table S1. However, the predicted relative magnitudes for Pd-rich compositions were underestimated, especially with regards to alloy and core-shell NPs in contact with TiO2. Near-field maps and simulated absorbance spectra provide qualitative guides for interpreting measured optical influences at AuPd-TiO2 interfaces for plasmonically driven photocatalytic reactions [6].

Photocatalytic Ethanol Oxidation via Au-Pd NPs on TiO2 Supports
Suspended particle photocatalysis of metal-oxide semiconductors is initiated by the absorption of photons to induce charge separation and diffusion of the photogenerated carriers to surface active sites to react with adsorbed chemical species [3,5,6,46]. Metaloxide TiO2 supports were photosensitized with homogeneously alloyed Au1-xPdx and heterogeneous AuCore-Au1-xPdx.Shell NPs to be used as hybrid photoreactors for EtOH photooxidation. Plasmon-mediated photocatalytic EOR performance measurements were conducted under solar-simulated (AM1.5G) irradiation for 1-4 h, while the gaseous oxidation products were measured using a GC-MS-MHE analysis method [5,6]. Thermal background measurements were collected under dark conditions for each sample by heating the photoreactor at 60 °C to thermal equilibrium, which yielded negligible oxidation of EtOH. Plasmonically enhanced photocatalytic mass activities for Au1-xPdx and AuCore-Au1-xPdx.Shell NPs dispersed on TiO2 are shown in Figure 6, Table 1, and in Supplementary Tables S2 and S3 for the oxidation products of EtOH conversion, acetaldehyde (CH3CHO, n = 2e − ) and carbon dioxide (CO2, n = 12e − ). In Figure 6, the mass activity for CO2 is plotted on the left axis represented by purple (1 h) and blue (4 h) bars, while the mass activity for CH3CHO is plotted on the right axis represented by orange diamond (1 h) and green triangle (4 h) markers.
In Figure 6a and Table 1, all of the investigated elemental compositions for the Au1-xPdx alloys (outlined in black) and AuCore-Au1-xPdx.Shell (outlined in red) NPs on TiO2 were irradiated for 1 h under AM1.5G and the primary photocatalytic products detected by GC-MS-MHE were CO2 (purple bars) and CH3CHO (orange diamonds). The activity for TiO2 without a cocatalyst was 87.11 μmol CO2/g and 0.60 μmol CH3CHO/g, as listed in Supplementary Table S2. Mass activity of the Au1-xPdx alloys increased with an increase in the Pd content (x = 0 to x = 0.5) from 132.32 μmol CO2/g and 0.26 μmol CH3CHO/g for Au to 221.67 μmol CO2/g and 0.96 μmol CH3CHO/g for AuPd. However, the mass activity did not significantly increase after increasing the Pd content from x = 0.5 to x = 1, with Pd exhibiting 225.33 μmol CO2/g and 0.89 μmol CH3CHO/g. The observed plateau in mass activity for > 50% Pd can be attributed to a loss in the SPR absorption at low Au content. The AuCore-10% AuPd.Shell NPs on TiO2 exhibited mass activities of 164.99 μmol CO2/g and 0.36 μmol CH3CHO/g, which was between that of the alloy compositions of Au0.9Pd0.1 (147.09 μmol CO2/g) and Au0.75Pd0.25 (176.76 μmol CO2/g). In contrast, the AuCore-10% Pd.Shell NPs exhibited the highest mass activity of all samples with 283.28 μmol CO2/g and 1.06 μmol CH3CHO/g. The Au core maintains SPR absorption with a thin Pd shell at the surface to enhance catalytic EOR. Coupling plasmonic Au to TiO2 improves the chemical energy conversion reactions via plasmon-mediated hot electron transfer (PMET)-injection of hot electrons into the CB of a semiconductor. Detailed spectroscopic studies by Tan et al. have proposed the mechanism for photoenhancement due to PMET charge transfer between Au and TiO2 for EOR: (1) activation of oxygen at oxygen vacancies on TiO2, (2) dehydrogenation of EtOH to form acetaldehyde, (3) cleaving of C-C bond, (4) further oxidation to form CO2, and (5) electron transfer from Au to TiO2 [11,12]. PMET enables Au to accumulate hot holes and stabilize the Pd as a cocatalyst; facilitating the Au-Pd NPs to act as the primary active site for EOR [3,6]. Plasmon-induced heating (photothermal) provides the means to overcome the thermal barrier necessary to selectively cleave the C-C bond and hinder the poisoning effects on Pd [5,6,9]. Addition of Au-Pd cocatalysts with either an alloy or core-shell nanostructure resulted in an increase in the CO2 mass activity, i.e., the complete conversion of EtOH. In Figure 6b, Au, Au0.9Pd0.1, AuPd, Pd, AuCore-10% AuPd.Shell, and AuCore-10% Pd.Shell NPs on TiO2 were further investigated as photocatalysts by comparing product yields under prolonged (4 h) irradiation, listed in Table 2 and Supplementary Table S3. After 4 h irradiation, the yield of CO2 (blue bars) and CH3CHO (green triangles) increased for all compositions in comparison to the yields collected after 1 h irradiation (CO2, purple bars; CH3CHO, orange diamonds). Pd had the lowest EOR activity for complete EtOH conversion of the Pd-containing cocatalysts (328 μmol CO2/g). Initial rate of conversion for Pd diminished by 64% to 82 μmol CO2 • g −1 • h −1 after 4 h irradiation owing to binding of intermediates to its surface active sites [5,25,30]. Plasmonic Au cocatalysts exhibited the lowest overall activity of the cocatalysts after prolonged irradiation (292 CO2/g), with its initial rate of conversion diminished by 45% to 73.09 μmol CO2 • g −1 • h −1 . Notably, the product yields for Au1-xPdx alloy and AuCore-Au1-xPdx.Shell compositions that contained ~5-10 mol% Pd (i.e., Au0.9Pd0.1, Au-10% AuPd, and Au-10% Pd) were relatively similar with regard to complete EtOH conversion (391-403 CO2/g). The rate of complete EtOH conversion (97.68-100.78 μmol CO2 • g −1 • h −1 ) indicated similar reactivity and stability for alloy and core-shell NPs after prolonged irradiation. Therefore, nanostructuring (alloy vs. core-shell) at low Pd content (≤10% Pd) did not have a pronounced effect on the mass activity for long duration photocatalytic measurements. AuPd (1:1 mole ratio) alloy on TiO2 was the most active for complete EtOH conversion after prolonged AM1.5G irradiation (456 μmol CO2/g) and retained 67% of its initial rate of conversion (113.92 μmol CO2 • g −1 • h −1 ). Alloyed NPs can exhibit plasmonic, catalytic, and ligand effects observed in core-shell NPs, with the addition of the atomically distributed surface active sites to inhibit side reactions and poisoning [18,30,47]. The AuPd alloy exhibited SPR absorption and contained a sufficient amount of Pd metal to significantly improve its reactant chemisorption and subsequent EOR activity. Catalytic Pd enabled the retention and utilization of photogenerated carriers generated in Au for photocatalytic EOR.

Electrochemical Ethanol Oxidation via Au-Pd NPs on Carbon Supports
Photocatalytically active Au1-xPdx alloys and AuCore-Au1-xPdx.Shell NPs were selected for electrochemical measurement of their EOR performance. Figure 7 shows cyclic voltammetry (CV) scans of Au1-xPdx and AuCore-Au1-xPdx.Shell NPs on conductive carbon supports on a rotating disk electrode (RDE) immersed in 0.5 M EtOH (1 M KOH supporting electrolyte, 25 °C) under dark conditions. Onset potentials were identified as the threshold voltage for appreciable positive current, which indicated the start of the electrochemically driven EOR. Onset potentials during the anodic forward scan (i.e., left to right; VF and IF) were found to be reductively shifted from +0.72 V for Au to +0.30 V for Pd, listed in Table  3. Previous studies have reported ~1.25 to 5 mA/cm 2 for pure Au to Pd compositions, respectively [48,49]. Greater overpotential on Au is characteristic of EOR on Au compared with Pd for bulk metal surfaces [25,30,33]. The EOR current peaks for both samples during their anodic scan (VF and IF) were characteristically followed by a decrease in current owing to surface passivation of the active catalytic sites that were covered by EOR intermediate products [25,30,33]. Active sites were cleaned upon the reverse, cathodic scans (i.e., right to left; VR and IR), which resulted in the positive-current takeoff to higher EOR peak current magnitude owing to the freshly renewed catalytic surface [30]. Supplementary Figure S9 compares CVs in the dark immersed in 1 M KOH supporting electrolyte without 0.5 M EtOH. Peak anodic EOR current for the Au1-xPdx alloys increased from 1.51 mA cm −2 for Au, 9.26 mA cm −2 for Au0.9Pd0.1, 29.14 mA cm −2 for AuPd, and to 30.80 mA cm −2 for Pd, with current densities comparable or better than previous studies [48][49][50][51][52]. AuPd alloy exhibited similar electrochemical EOR activity as pure Pd despite 50% less Pd content. Increased EOR activity for the AuPd alloy is in part due to the superior catalytic performance inherent to Pd, as well as the resistance to catalyst poisoning inherent to Au. No significant changes in the onset potential or current density were observed for > 50% Pd alloy composition. In contrast, peak anodic current densities of the core-shell NPs in Figure 7b were lower and anodically shifted to higher onset potentials with 3.37 mA cm −2 at 0.82 V for AuCore-AuPd.Shell and 1.55 mA cm −2 at 0.94 V for AuCore-Pd.Shell. Secondary anodic peaks at higher potential were attributed to the Au signature for the Au0.9Pd0.1 alloy with 3.81 mA cm −2 at 1.17 V, AuCore-AuPd.Shell with 1.60 mA cm −2 at 1.18 V, and AuCore-Pd.Shell with 2.96 mA cm −2 at 1.21 V. Under dark conditions, electrochemical properties were investigated for alloy and core-shell NPs on conductive carbon supports without SPR effects. Homogenous mixing of Au and Pd yielded optimal results, while heterogeneous core-shells separated the metals into defined regions, resulting in lower current densities at analogous compositions.  Table 3. Electrochemical onset potentials, peak potentials, and peak current densities for forward and reverse CV scans of the Au1-xPdx and AuCore-Au1-xPdx.Shell NPs on carbon supports in the dark.

Photoelectrochemical Ethanol Oxidation via Au-Pd NPs on TiO2 Supports
The selected Au1-xPdx alloys and AuCore-Au1-xPdx.Shell NPs were further investigated by CV and chronoamperometry (CA) for their SPR-induced photoelectrochemical (PEC) EOR by photosensitizing TiO2 supports. CV scans in the dark and under AM1.5G irradiation are shown in Supplementary Figures S10-S12. Catalytic metals like Pt and Pd enhance the extraction and use of plasmonic carriers generated in Au [4,18,20,28,29,43,53,54]. Furthermore, hot electron transfer and photothermal processes can facilitate intermediate removal during irradiation [3,5,9]. Elucidation of the role of SPR effects on EOR motivated solar-simulated CA photocurrent studies. Plasmon-enhanced EOR photocurrents were measured via CA scans on a RDE immersed in 0.5 M EtOH (1 M KOH supporting electrolyte, 25 °C) for current density (Figure 8a) and mass activity (Figure 8b) measurements. CA measurements were held at a bias of appreciable current (+0.72 V vs. RHE), with 250 s on/off chopping of broadband AM1.5G irradiation. Applied potential improves electron transport to the back contact and decreases the surface recombination rate, while demonstrating appreciable EOR current for both alloy and core-shell compositions of interest. Analyses focus on the average photocurrent magnitude measured during the first "light on" step and after 1900 s chopped irradiance, as shown in Figure 8 and in Supplementary Tables S4 and S5. Immediate photocurrent response resulted from the separation of photogenerated electron-hole pairs at the electrode-electrolyte interface. Anodic (positive) spikes in photocurrent indicated accumulation of charge at the electrode-electrolyte interface, while cathodic (negative) transients are indicative of charge recombination. Lack of photocurrent transients indicated unimpeded charge transfer from the electrode to the electrolyte, thereby hole transfer was facilitated at the catalyst surface for EOR [55][56][57]. Average peak EOR photocurrent densities generated under AM1.5G irradiation on TiO2 in Figure 8a were 1.31 μA cm −2 for Au, 1.31 μA cm −2 for Au0.9Pd0.1, 1.43 μA cm −2 for AuCore-AuPdShell, and 1.97 μA cm −2 for AuCore-PdShell. Notably, no photo-induced current enhancement was observed for Au-Pd alloy thin films absent of SPR effects in our previous studies [30]. Au-Pd photosensitized samples were reactivated by successive CV scans to remove surfaceadsorbed intermediates. Au-rich compositions (Au, Au0.9Pd0.1, AuCore-AuPdShell, AuCore-PdShell) act as hole accumulation sites, creating a positively charged surface to promote the adsorption of electron donors such as EtOH [11,12]. However, interband transitions that occur at shorter wavelengths (λ < 600 nm) between filled d-band and empty sp-states dominate for Au-rich NP compositions, resulting primarily in 2e − products rather than complete oxidation [6,11,12]. Appreciable loss in photocurrent during sustained bias holds was observed overtime for all Au-Pd photosensitized samples with photocurrent retention of 47% for Au, 53% for Au0.9Pd0.1, 40% for AuCore-AuPdShell, and 44% for AuCore-PdShell on TiO2 after 1900 s at the sustained bias (0.72 V vs. RHE). Relatively low photocurrents for Au-rich compositions suggest that some excited carriers on the cocatalysts relax via electron-phonon scattering, thereby increasing the surface temperature. While photothermal heating can contribute to photocatalytic activity and gaseous product yields ( Figure  6), higher rates of hot-carrier separation and transfer in Au-rich compositions are necessary for increased photocurrents (Figure 8).
Alloying ≥ 50% Pd with Au had the largest impact on the EOR photocurrent, with a photocurrent density of 8.32 μA cm −2 for AuPd alloy on TiO2. Notably, AuPd alloy on TiO2 retained 72% of its initial photocurrent after 1900 s at the sustained bias. Alloying Au with Pd resulted in an even distribution of metal active sites for reactant binding; reducing the stability of the intermediate and improving activity [58]. The increase in photocurrent was attributed to interband excitations that initiated injection of d-band holes from the Au into the Pd active sites for subsequent reaction with adsorbed species [59]. Slow relaxation of the photocurrent after the "light on" step for AuPd alloy indicated accumulation of holes at the electrode-electrolyte interface, facilitated favorable reaction kinetics, and hindered charge recombination [55][56][57]. In comparison, catalytic Pd on TiO2 generated 4.74 μA cm −2 and retained 84% of its initial photocurrent after 1900 s owing to Pd acting as a hole scavenger, which improved charge separation at the metal-semiconductor interface. Average photo-enhancement in terms of mass activity (mA/mgPd) in Figure 8b showed a moderate improvement for core-shell NPs (10.60-14.70 mA/mgPd) in comparison to the analogous alloy composition of Au0.9Pd0.1 (9.76 mA/mgPd). Photocurrent enhancements were observed for all bimetallic Au-Pd compositions (9.76-14.70 mA/mgPd) compared to pure Pd (3.53 mA/mgPd). Initially, core-shell NPs exhibited high mass activity performance at the first "light on" step but rapidly decayed. AuPd (1:1 mole ratio) alloy retained the highest mass activity (10.20 mA/mgPd) after 1900 s compared to all measured compositions and nanostructured catalysts. Bimetallic AuPd alloy catalysts exhibited the ability to selectively drive photochemical and PEC reactions at improved efficiency with the assistance of their SPR and ligand effects.

Conclusions
Bimetallic Au-Pd NPs were synthetically modified to influence the plasmonic nearfield enhancement, optical absorption, and catalytic activity resultant from PMET and photothermal effects. TEM imaging and elemental analysis confirmed the composition and nanostructuring (alloy vs. core-shell). XPS revealed a shift in d-band onset toward the EF and an increase in the DOS at the EF with an increase in Pd content. Modifying the Au-Pd composition provides atomic control over tuning the ligand effect to impact reactant adsorption to the catalyst surface, and thereby the catalytic activity. UV-vis spectroscopy revealed the plasmonic response was retained and appreciable for alloys containing ≥ 50% Au and core-shell nanostructures with intact plasmonic Au cores. Au-Pd alloys and coreshells exhibited EF below the CB of TiO2, as confirmed by XPS, and the composites maintained their SPR effect that progressively blue-shifted with increasing Pd, as confirmed by UV-Vis DRS. DDA simulations of the spatial distributions of the electric field enhancement showed pure Au exhibited the strongest SPR response, with AuPd and Pd exhibiting similar intensity responses, localized at the metal-semiconductor interface. Photocatalytic and electrochemical oxidation of EtOH to CO2 under dark and solar-simulated irradiation was studied, with a focus on product selectivity, C-C bond breaking, and mitigating catalyst poisoning. Supported AuPd (1:1 mole ratio) alloy yielded optimal photocatalytic (456 μmol CO2/g), electrochemical (29.14 mA•cm −2 ), and PEC (8.32 μA cm −2 ) results owing to metallic effects (plasmonic, catalytic, ligand effects) and atomically distributed Au and Pd surface active sites to inhibit side reactions and poisoning. The AuPd alloy was found to be the ideal composition and nanostructured bimetallic for complete EtOH conversion. Photogenerated holes drive the photo-oxidation of EtOH primarily on the AuPd alloy and photothermal effects improve intermediate desorption from the catalyst surface, provid-ing a method to selectively cleave C-C bonds. Plasmonic bimetallic nanostructures provide a pathway for driving desired photocatalytic and PEC reactions with superior catalytic activity and selectivity.