Mesoporous Dual-Semiconductor ZnS/CdS Nanocomposites as Efficient Visible Light Photocatalysts for Hydrogen Generation

The development of functional catalysts for the photogeneration of hydrogen (H2) via water-splitting is crucial in the pursuit of sustainable energy solutions. To that end, metal-sulfide semiconductors, such as CdS and ZnS, can play a significant role in the process due to their interesting optoelectronic and catalytic properties. However, inefficient charge-carrier dissociation and poor photochemical stability remain significant limitations to photocatalytic efficiency. Herein, dual-semiconductor nanocomposites of ZnS/CdS nanocrystal assemblies (NCAs) are developed as efficient visible light photocatalysts for H2 generation. The resultant materials, synthesized via a polymer-templated self-polymerization method, comprise a unique combination of ~5–7 nm-sized metal-sulfide nanoparticles that are interlinked to form a 3D open-pore structure with large internal surface area (up to 285 m2 g−1) and uniform pores (circa 6–7 nm). By adjusting the ratio of constituent nanoparticles, the optimized ZnS/CdS catalyst with 50 wt.% ZnS content demonstrates a remarkable stability and visible light H2-evolution activity (~29 mmol g−1 h−1 mass activity) with an apparent quantum yield (AQY) of 60% at 420 nm. Photocatalytic evaluation experiments combined with electrochemical and spectroscopic studies suggest that the superior photocatalytic performance of these materials stems from the accessible 3D open-pore structure and the efficient defect-mediated charge transfer mechanism at the ZnS/CdS nanointerfaces. Overall, this work provides a new perspective for designing functional and stable photocatalytic materials for sustainable H2 production.


Introduction
The exponential growth of urbanization and population has led to a significant surge in the consumption of resources, giving rise to global challenges such as energy scarcity and environmental deterioration. At present, over 80% of the world's energy supply still comes from the combustion of non-renewable fossil fuels, such as oil, coal and natural gas, leading to the release of CO 2 and other harmful gases which contribute significantly to climate change and generate adverse effects on the environment and human health [1,2]. Addressing this issue is undeniably a complex challenge, as it is imperative to establish ecofriendly and renewable technological solutions to foster a more sustainable future. In this context, photocatalysis has gained significant importance in the development of alternative energy sources, particularly in the areas of green energy conversion and the production of clean fuels. Among the various photocatalytic processes, the production of hydrogen (H 2 ) via semiconductor-based photochemical water-splitting has been regarded as one of the "holy grails" in the future energy portfolio. This is because water is a renewable resource, and H 2 possesses the advantages of having a high energy content (~122 kJ g −1 ) and being a clean (zero-carbon emission) energy carrier [3,4]. Key to this approach is the development of new photocatalytic materials that should combine cost-efficiency (i.e., be inexpensive and synthesized via "green" and economically viable processes) with high

Synthesis of Mesoporous ZnS, CdS and ZnS/CdS NC Assemblies (NCAs)
The mesoporous CdS and ZnS NC assemblies (NCAs) were prepared according to our previously reported method [28], with slight modifications. In brief, 300 mg of thiolcapped CdS (or ZnS) NCs were dispersed in 5 mL of DI water containing~0.1 mL ammonia solution, forming a clear colloidal suspension (sol). Afterwards, 300 mg of Brij 58 was added, and the mixture was left under vigorous stirring for 1 h at RT, resulting in a stable colloidal dispersion. Next, 1 mL of 3% (v/v) aqueous H 2 O 2 solution was added and, after stirring for an additional 5 min, the resultant solution was left under static conditions until gelation was observed (after~1 h). After gelation, the mixture was placed in an oven at 40 • C and left for~3 days to evaporate the solvent. The template removal was achieved via successive washing cycles, which included the soaking and stirring of the dry gel product in 20 mL ethanol for 30 min, followed by vacuum filtration, and repeating this process three more times with DI water. The final mesoporous CdS and ZnS NCAs were obtained after drying the respective washed samples at 60 • C for~12 h.
The dual-semiconductor ZnS/CdS NCAs were prepared following the exact same procedure but by employing appropriate mixtures of thiol-capped CdS and ZnS NCs to achieve the desired mass loadings (wt.%) of ZnS in the final heterostructures. For instance, to maintain the total quantity of metal-sulfide NCs during the reaction fixed at 300 mg, a mixture of 150 mg CdS and 150 mg ZnS NCs was used to prepare the mesoporous ZnS/CdS nanocomposite with 50 wt.% ZnS content.

Synthesis of Bulk ZnS/CdS
For comparison purposes, a ZnS/CdS bulk heterostructure with 50 wt.% ZnS content was prepared by physically mixing two separate 10 mL aqueous dispersions containing the appropriate amounts of pre-formed CdS and ZnS microparticles. The CdS and ZnS microparticles were synthesized via direct precipitation of CdCl 2 and ZnCl 2 with equimolar amounts of Na 2 S in water, respectively. After mixing, the resulting ZnS/CdS suspension was stirred for about 3 h at RT, followed by centrifugation and drying at 100 • C overnight.

Physicochemical Characterization
Energy-dispersive X-ray spectroscopy (EDS) and field-emission electron microscopy (FE-SEM) were conducted using a JEOL JSM-IT700HR microscope equipped with a JED-2300 detector (JEOL Ltd., Tokyo, Japan). EDS data acquisition was carried out at least ten times (at different locations) for each sample using an accelerating voltage of 20 kV and a 60 s accumulation time. X-ray diffraction (XRD) patterns were obtained with a PANanalytical X' pert Pro MPD diffractometer (Malvern PANalytical Ltd., Almelo, The Netherlands) equipped with a Cu Kα (λ = 1.5418 Å) radiation source in Bragg-Brentano geometry (45 kV and 40 mA). Transmission electron microscopy (TEM) imaging was performed with a JEOL JEM-2100 microscope (JEOL Ltd., Tokyo, Japan) equipped with a LaB 6 filament, using an acceleration voltage of 200 kV. TEM samples were prepared by depositing few drops of an ethanolic dispersion containing the respective materials onto a perforated carbon-coated Cu grid. X-ray photoelectron spectroscopy (XPS) measurements were taken with a SPECs spectrometer (SPECS Surface Nanon Analysis, Berlin, Germany), using a Phoibos 100 1D-DLD electron analyzer and Al Kα monochromatic radiation (1486.6 eV). In all cases, the binding energies were corrected with respect to the C1 signal of adventitious carbon at 284.8 eV. Thermogravimetric analysis (TGA) was performed with a Perkin-Elmer Diamond system under a nitrogen flow of 100 mL min −1 with a heating rate of 5 • C min −1 . N 2 physisorption (adsorption-desorption) isotherms were recorded at −196 • C with a Quantachrome NOVA 3200e sorption analyzer (Quantachrome Instruments, Boynton Beach, FL, USA). Before measurement, the samples were degassed at 80 • C under low pressure (<10 −5 Torr) for 12 h. The specific surface areas were estimated from the adsorption data in the relative pressure (P/P 0 ) range of 0.04-0.22 using the Brunauer-Emmett-Teller (BET) method. The total pore volumes were determined from the amount of adsorbed N 2 at P/P 0 = 0.98. The pore size distributions were derived from the adsorption branch of the isotherms using the nonlocal density functional theory (NLDFT) fitting model. A Shimazu UV-2600 spectrophotometer (Shimadzu Co., Kyoto, Japan) was employed to acquire the UV-vis/near-IR diffuse reflectance spectra, using BaSO 4 powder as the 100% reflectance reference. The conversion of the diffuse reflectance data to absorbance (α/S) was attained using the Kubelka-Munk function: α/S = (1 − R) 2 /(2R), where R represents the measured reflectance, while α and S denote the absorption and scattering coefficients, respectively. The energy band gaps (E g ) of the samples were determined from Tauc plots for direct allowed transitions, i.e., the plot of (αhv) 2 vs. hv, where α is the absorption coefficient and hv is the energy of incident photons. Photoluminescence (PL) and time-resolved photoluminescence (TR-PL) spectra were acquired at RT using an Edinburgh FS5 spectrofluorometer equipped with a 150 W CW ozone-free xenon arc lamp and a 375 nm EPL picosecond pulsed diode laser (Edinburgh Instruments Ltd., Livingston, UK).

Photocatalytic Study
The photocatalytic hydrogen evolution experiments were performed in an airtight Pyrex glass reactor, which was placed in a water-bath cooling system to ensure a constant reaction temperature of 20 ± 2 • C. In a typical experiment, 20 mg of catalyst was dispersed in a 20 mL aqueous electrolyte solution containing 0.35 M Na 2 S and 0.25 M Na 2 SO 3 (except when otherwise noted). Prior to measurement, the reaction mixture was thoroughly deaerated via purging with argon (Ar) for at least 30 min, and then irradiated with visible light using a 300 W Xe lamp (Variac Cermax) equipped with a UV cut-off filter (Asahi Techno Glass, λ ≥ 420 nm). The amount of evolved H 2 was determined by extracting 100 µL gas samples from the headspace of the reactor at specific time intervals (using a gastight syringe) and analyzing them on a Shimadzu GC-2014 gas chromatograph (using Ar as a carrier gas) equipped with a thermal conductivity detector (TCD).
Photocatalytic stability tests were carried out under visible light irradiation by performing consecutive photocatalytic H 2 -evolution runs over specific time periods (cycles). After each cycle, the catalyst was collected via centrifugation and then redispersed in a fresh Na 2 S/Na 2 SO 3 solution. Additionally, prior to each catalytic run, the reaction mixture was thoroughly deaerated with Ar gas for at least 30 min until no H 2 , O 2 or N 2 gases were detected via gas chromatography (GC).
The apparent quantum yield (AQY) was estimated by analyzing the average rate of hydrogen evolution obtained under monochromatic LED light (λ = 420 ± 10 nm) irradiation according to the following equation: where N H2 is the flux of evolved H 2 molecules (i.e., the number of evolved H 2 molecules per unit time) and N hv is the flux of incident photons at λ = 420 nm (i.e., number of photons per unit time). The average intensity of incident light was determined using a StarLite power meter equipped with a FL400A-BB-50 fan-cooled thermal sensor (Ophir Optronics Ltd., Jerusalem, Israel) and was found to be 11.7 mW cm −2 . This corresponds to a flux of incident photons of approximately 7.6 × 10 16 s −1 .

Electrochemical Measurements
Electrochemical Mott-Schottky and Nyquist impedance measurements were performed using a VersaSTAT 4 single-channel potentiostat-galvanostat electrochemical workstation (Princeton Applied Research, Princeton, NJ, USA). All experiments were conducted in a 0.5 M Na 2 SO 4 electrolyte (pH = 7), using a custom-made three-electrode electrochemical cell consisting of a sample-coated fluorine-doped tin oxide (FTO, 10 Ω sq -1 ) working electrode, a Ag/AgCl (saturated KCl) reference electrode, and a graphite-rod counter-electrode. For the preparation of the working electrodes, 10 mg of each sample was first dispersed in 1 mL of absolute ethanol using ultrasonication for 30 min, followed by vigorous stirring for 1 h at RT to form uniform suspensions. Then, each sample suspension was gradually drop-cast onto the conductive surface of FTO glass substrates (working surface area of 1 cm 2 ) under mild heating conditions (50-60 • C) to produce thick films in order to ensure that the width of the depletion layer did not exceed the thickness of the semiconductor layer [33].
To obtain the Mott-Schottky plots, the interfacial capacitance (C) of the samples was measured at a frequency of 1 kHz using a 10 mV AC voltage amplitude. All the measured potentials were converted to the reversible hydrogen electrode (RHE) scale at pH = 7 using the equation: where E RHE is the potential in the RHE scale and E Ag/AgCl is the measured potential in the Ag/AgCl scale. The flat-band potential (E FB ) and donor density (N D ) of the samples were estimated from the linear portion of the Mott-Schottky curves according to the Mott-Schottky equation [33,34]: where C is the measured interfacial capacitance, E is the applied potential, E FB is the flat band potential, A is the working area of the electrode (1 cm 2 ), ε is the relative dielectric constant of the material (8.9) [35,36], ε o is the dielectric permittivity under vacuum (8.8542 × 10 -14 F cm -1 ), e o is the elementary charge (1.602 × 10 -19 C), k B is the Boltzmann constant, and T is the temperature. Note that, under normal conditions, the term "k B T/e o " is usually negligible [37] and the Mott-Schottky relation can be simplified as shown in Equation (3). Thus, the corresponding E FB values were determined from the linearly extrapolated intercepts with the x-axis (1/C 2 = 0), while N D values were calculated from the reciprocal of the slopes of the Mott-Schottky plots and using Equation (3). The Nyquist impedance measurements were conducted in 0.5 M Na 2 SO 4 electrolyte (pH = 7) using an applied DC bias of −1.3 V (vs. Ag/AgCl, saturated KCl) and the data were recorded over a frequency range from 1 Hz to 100 KHz. ZView software was used to fit the experimental data to a simplified Randles circuit model, consisted of an electrolyte resistance (R s ), a charge transfer resistance (R ct ) and a double-layer capacitance (C dl ).

Materials Synthesis and Characterization
The synthesis of mesoporous ZnS/CdS nanocomposites was accomplished via an evaporation-induced self-assembly (EISA) sol-gel method, in which ZnS and CdS colloidal NCs self-organized into 3D mesoporous gel-like networks with the aid of block copolymer (POE 20 -b-C 16 ; Brij 58) micelles, as illustrated in Figure 1a. To synthesize the CdS and ZnS colloidal NCs, a thiol-terminated ligand (3-mercaptopropionic acid) was employed, which can exert control over the nanoparticle growth by binding to the NC surface via the thiol group and can facilitate enthalpic interactions with the polar POE fragments of the polymer template via the propionic acid end-group [28]. The pre-formed NCs were subsequently utilized as building-block units that co-assemble with the polymer micelles under solvent evaporation conditions to create hybrid NC/polymer mesostructures. Key to this step is the addition of a small amount of dilute H 2 O 2 solution (3% v/v) to the NC/polymer dispersion (as outlined in the experimental section), which instigates the gradual oxidation and stripping of the thiolate ligands from the NCs' surface and prompts the oxidative polymerization of metal-sulfide NCs into a 3D network (on the surface of the polymer template) via interparticle disulfide or polysulfide linking bonds [38][39][40]. It is noteworthy that the oxidant concentration and the related oxidation rates of the stabilizing thiolate capping groups constitute critical parameters that play a pivotal role in the controlled aggregative assembly of colloidal NCs and the preparation of robust gel-like porous frameworks. This observation builds upon earlier research into the formation of metal chalcogenide gels and aerogels, where it was demonstrated that the addition of a small quantity of oxidant (e.g., H 2 O 2 ) below a specific threshold value (minimum ratio of oxidant/thiolate, X min ) did not lead to sufficient removal of thiolate capping groups to initiate the gelation-polymerization of NCs [41]. Above X min , efficient oxidation of surface thiolate ligands was achieved, resulting in interparticle linking and the assembly of stable gel networks, which can only be disassembled under (electro)chemical reductive environments [38,40]. Conversely, the utilization of a high amount of oxidant (~5X min ) triggered a rapid loss of surface thiolate groups, resulting in uncontrolled NC agglomeration and the precipitation of densely packed aggregates [41][42][43]. Therefore, by employing the appropriate amount of H 2 O 2 , the creation of an interconnected NC-network provided sufficient structural stability to enable the effective removal of the organic template from the hybrid mesostructures via a gentle post-preparative treatment with ethanol and water (as detailed in the experimental section), thus yielding mesoporous ZnS/CdS NCAs. Consequently, via this procedure and the concentration of the colloidal CdS and ZnS nano-building blocks were appropriately adjusted, a series of mesoporous ZnS/CdS nanocomposites with varying mass loadings (wt.%) of ZnS were prepared, designated as x-ZnS/CdS (x = 10, 30, 50, 70 and 90 wt.% ZnS). Additionally, single-component mesoporous CdS and ZnS NCAs were prepared using the same synthetic process and extensively studied for comparison purposes. The chemical composition of the resultant materials was determined via energy-dispersive X-ray spectroscopy (EDS), and the obtained results are summarized in Table S1 (in Supplementary Materials). For the CdS NCAs, EDS analysis revealed the presence of Cd and S elements with a Cd:S atomic ratio very close to the 1:1 stoichiometry of CdS. In contrast, the corresponding Zn:S atomic ratio in the ZnS NCAs sample was found to be~1:0.86, implying a small sulfur deficiency (approximately 14%) in the lattice of constituent ZnS NCs. The EDS results of the ZnS/CdS nanocomposites indicated the presence of Cd and Zn atoms at varying Cd/Zn ratios, based on which the ZnS loading amounts were estimated and found to be very close to the nominal compositions of 10-90 wt.% (see Table S1).
Cd and S elements with a Cd:S atomic ratio very close to the 1:1 stoichiometry of CdS. In contrast, the corresponding Zn:S atomic ratio in the ZnS NCAs sample was found to be ~1:0.86, implying a small sulfur deficiency (approximately 14%) in the lattice of constituent ZnS NCs. The EDS results of the ZnS/CdS nanocomposites indicated the presence of Cd and Zn atoms at varying Cd/Zn ratios, based on which the ZnS loading amounts were estimated and found to be very close to the nominal compositions of 10-90 wt.% (see Table  S1). The crystallinity of the as-prepared materials was characterized via powder X-ray diffraction (XRD). As seen in Figure 1b The morphology of the ZnS/CdS nanocomposite with 50 wt.% ZnS content (50-ZnS/CdS), which is the most active catalyst in this study, was assessed via field emission scanning electron microscopy (FE-SEM) and transmission electron microscopy (TEM). The representative FE-SEM image in Figure 2a reveals an agglomerated morphology comprising small-sized nanoparticles within the range of 5 to 10 nm. In Figure 2b, the SEM-EDS elemental mapping shows a uniform dispersion of Cd, Zn and S elements, indicating that the ZnS and CdS nanoparticles are evenly distributed throughout the assembled structure. The TEM image in Figure 2c further reveals an open-pore structure configuration, while the high magnification image (Figure 2c inset) also demonstrates that the pore walls consist of approximately 5-6 nm-sized CdS and ZnS nanoparticles that are in intimate contact, which is advantageous for promoting efficient interfacial charge transfer and separation. Furthermore, the high-resolution TEM (HRTEM) image in Figure 2d displays distinct lattice fringes with interplanar spacings of 3.4 Å and 3.1 Å, corresponding to the (111) crystal planes of the cubic CdS and ZnS, respectively, in agreement with the The crystallinity of the as-prepared materials was characterized via powder X-ray diffraction (XRD). As seen in Figure 1b The morphology of the ZnS/CdS nanocomposite with 50 wt.% ZnS content (50-ZnS/CdS), which is the most active catalyst in this study, was assessed via field emission scanning electron microscopy (FE-SEM) and transmission electron microscopy (TEM). The representative FE-SEM image in Figure 2a reveals an agglomerated morphology comprising small-sized nanoparticles within the range of 5 to 10 nm. In Figure 2b, the SEM-EDS elemental mapping shows a uniform dispersion of Cd, Zn and S elements, indicating that the ZnS and CdS nanoparticles are evenly distributed throughout the assembled structure. The TEM image in Figure 2c further reveals an open-pore structure configuration, while the high magnification image (Figure 2c inset) also demonstrates that the pore walls consist of approximately 5-6 nm-sized CdS and ZnS nanoparticles that are in intimate contact, which is advantageous for promoting efficient interfacial charge transfer and separation. Furthermore, the high-resolution TEM (HRTEM) image in Figure 2d displays distinct lattice fringes with interplanar spacings of 3.4 Å and 3.1 Å, corresponding to the (111) crystal planes of the cubic CdS and ZnS, respectively, in agreement with the XRD results. Taken together, the above findings attest to the successful synthesis of porous ZnS/CdS nanocomposites, comprising small-sized ZnS and CdS nanoparticles that are linked together to form a robust 3D network. XRD results. Taken together, the above findings attest to the successful synthesis of porous ZnS/CdS nanocomposites, comprising small-sized ZnS and CdS nanoparticles that are linked together to form a robust 3D network. The chemical state of elements in the 50-ZnS/CdS material was analyzed via X-ray photoelectron spectroscopy (XPS). The XPS spectra of pure CdS and ZnS NCAs were also obtained as reference. Typical survey spectra are shown in Figure S1 in Supplementary Materials, while high-resolution spectra of the Cd 3d, Zn 2p and S 2p regions are shown in Figure 3. The Cd 3d spectra show strong signals at binding energies of 412.2 and 405.5 eV for CdS NCAs and 411.9 and 405.2 eV for the 50-ZnS/CdS nanocomposite (Figure 3a), which are respectively assigned to the Cd 3d3/2 and Cd 3d5/2 core-levels of CdS [45,46]. The Zn 2p XPS spectrum of ZnS NCAs in Figure 3b presents two peaks at 1045.0 and 1022.0 eV that correspond to the Zn 2p1/2 and Zn 2p3/2 core-levels of ZnS, respectively [47,48]. The respective Zn 2p binding energies of 50-ZnS/CdS are located at 1045.3 and 1022.3 eV. Furthermore, the high-resolution S 2p spectra (Figure 3c) of all the examined samples display a prominent peak at 161.8-162.2 eV that is characteristic of the S 2− valence state in metal sulfides [45][46][47][48]. The additional small S 2p XPS peaks observed at higher binding energies (168.5-169 eV) can be attributed to some oxidized sulfur species (SOx 2− ) formed on the particle surface during the synthesis process and/or air handling of the samples [45,49]. The chemical state of elements in the 50-ZnS/CdS material was analyzed via X-ray photoelectron spectroscopy (XPS). The XPS spectra of pure CdS and ZnS NCAs were also obtained as reference. Typical survey spectra are shown in Figure S1 in Supplementary Materials, while high-resolution spectra of the Cd 3d, Zn 2p and S 2p regions are shown in Figure 3. The Cd 3d spectra show strong signals at binding energies of 412.2 and 405.5 eV for CdS NCAs and 411.9 and 405.2 eV for the 50-ZnS/CdS nanocomposite (Figure 3a), which are respectively assigned to the Cd 3d 3/2 and Cd 3d 5/2 core-levels of CdS [45,46]. The Zn 2p XPS spectrum of ZnS NCAs in Figure 3b presents two peaks at 1045.0 and 1022.0 eV that correspond to the Zn 2p 1/2 and Zn 2p 3/2 core-levels of ZnS, respectively [47,48]. The respective Zn 2p binding energies of 50-ZnS/CdS are located at 1045.3 and 1022.3 eV. Furthermore, the high-resolution S 2p spectra (Figure 3c) of all the examined samples display a prominent peak at 161.8-162.2 eV that is characteristic of the S 2− valence state in metal sulfides [45][46][47][48]. The additional small S 2p XPS peaks observed at higher binding energies (168.5-169 eV) can be attributed to some oxidized sulfur species (SO x 2− ) formed on the particle surface during the synthesis process and/or air handling of the samples [45,49]. Noticeably, the binding energies of Cd 3d in the 50-ZnS/CdS nanocomposite are shifted by 0.3 eV towards lower energy in comparison with those of pure CdS NCAs, while the respective Zn 2p binding energies exhibit an upshift of 0.3 eV relative to the pure ZnS NCAs. These particular shift patterns in binding energies can be attributed to the altered chemical environment at the ZnS/CdS interface resulting from an electron transfer from ZnS to CdS upon hybridization, indicating the strong electronic interaction between the CdS and ZnS components. Noticeably, the binding energies of Cd 3d in the 50-ZnS/CdS nanocomposite are shifted by 0.3 eV towards lower energy in comparison with those of pure CdS NCAs, while the respective Zn 2p binding energies exhibit an upshift of 0.3 eV relative to the pure ZnS NCAs. These particular shift patterns in binding energies can be attributed to the altered chemical environment at the ZnS/CdS interface resulting from an electron transfer from ZnS to CdS upon hybridization, indicating the strong electronic interaction between the CdS and ZnS components. The ideal outcome of the employed polymer-templated oxidative polymerization process would be the creation of materials with a porous interconnected network of NCs devoid of any organic molecules. In practice, however, it is common to observe a certain quantity of residual organics (<8 wt.%) on the surface of the NC-assembled structure, even after thorough washing procedures to remove the polymer template [28]. The presence of residual organics can influence factors such as wetting properties (hydrophobicity) and accessible surface area, and hence, the photocatalytic activity of the resulting porous structures [39]. In light of this, we assessed the efficiency of organic matter removal from the fabricated mesoporous NCA structures via thermogravimetric analysis (TGA). Αn illustrative example of TGA characterization performed on the mesoporous 50-ZnS/CdS nanocomposite (which is the best-performing catalyst of this work) is presented in Figure S2. In the TGA profile, the initial weight loss (~2.4%) observed in the temperature range of 50-200 °C can be attributed to the removal of adsorbed water, indicating the hydrophilic nature of the surface. Furthermore, the analysis revealed that approximately 7.4 wt.% of organic residue remains within the assembled structure, as indicated by the weight loss in the temperature range of 200-400 °C. This observation aligns with our earlier findings regarding a CdS NCA structure [28]. Nevertheless, as we show below (in N2 physisorption and photocatalytic H2 production experiments), this small percentage of residual organic content does not exert any significant constraints on pore accessibility or adversely impact the catalytic surface properties of the synthesized mesoporous nanocomposites. The porosity of the prepared materials was examined via N2 physisorption measurements conducted at −196 °C. Figure 4a presents a comparison of the N2 adsorption-desorption isotherms and the corresponding pore size distribution plots for the mesoporous CdS and ZnS NCAs, along with those of the 50-ZnS/CdS nanocomposite. The corresponding plots for the other ZnS/CdS NCAs (with 10, 30, 70 and 90 wt.% ZnS content) are provided in Figure S3. All the isotherms feature typical type-IV curves with H2-type hysteresis loop, which are characteristic of porous solids with interconnected pores [50]. Additionally, all the N2 adsorption isotherms exhibit a small but distinguishable capillary condensation step in the relative pressure (P/Po) range of ~0.4-0.6, suggesting N2 condensation in nar- The ideal outcome of the employed polymer-templated oxidative polymerization process would be the creation of materials with a porous interconnected network of NCs devoid of any organic molecules. In practice, however, it is common to observe a certain quantity of residual organics (<8 wt.%) on the surface of the NC-assembled structure, even after thorough washing procedures to remove the polymer template [28]. The presence of residual organics can influence factors such as wetting properties (hydrophobicity) and accessible surface area, and hence, the photocatalytic activity of the resulting porous structures [39]. In light of this, we assessed the efficiency of organic matter removal from the fabricated mesoporous NCA structures via thermogravimetric analysis (TGA). An illustrative example of TGA characterization performed on the mesoporous 50-ZnS/CdS nanocomposite (which is the best-performing catalyst of this work) is presented in Figure S2. In the TGA profile, the initial weight loss (~2.4%) observed in the temperature range of 50-200 • C can be attributed to the removal of adsorbed water, indicating the hydrophilic nature of the surface. Furthermore, the analysis revealed that approximately 7.4 wt.% of organic residue remains within the assembled structure, as indicated by the weight loss in the temperature range of 200-400 • C. This observation aligns with our earlier findings regarding a CdS NCA structure [28]. Nevertheless, as we show below (in N 2 physisorption and photocatalytic H 2 production experiments), this small percentage of residual organic content does not exert any significant constraints on pore accessibility or adversely impact the catalytic surface properties of the synthesized mesoporous nanocomposites. The porosity of the prepared materials was examined via N 2 physisorption measurements conducted at −196 • C. Figure 4a presents a comparison of the N 2 adsorption-desorption isotherms and the corresponding pore size distribution plots for the mesoporous CdS and ZnS NCAs, along with those of the 50-ZnS/CdS nanocomposite. The corresponding plots for the other ZnS/CdS NCAs (with 10, 30, 70 and 90 wt.% ZnS content) are provided in Figure S3. All the isotherms feature typical type-IV curves with H2-type hysteresis loop, which are characteristic of porous solids with interconnected pores [50]. Additionally, all the N 2 adsorption isotherms exhibit a small but distinguishable capillary condensation step in the relative pressure (P/P o ) range of~0.4-0.6, suggesting N 2 condensation in narrowsized mesopores [51]. The Brunauer−Emmett−Teller (BET) surface area (S BET ) and total pore volume (V p ) of the mesoporous ZnS/CdS NCAs were measured to be in the range of 243-285 m 2 g −1 and 0.29-0.32 cm 3 g −1 , respectively, which fall between those of pure CdS (S BET = 234 m 2 g −1 , V p = 0.28 cm 3 g −1 ) and ZnS (S BET = 334 m 2 g −1 , V p = 0.33 cm 3 g −1 ) NCAs. As shown in Table 1, the S BET and V p of the ZnS/CdS nanocomposites progressively increased as the ZnS content increased from 10 to 90 wt.%. This trend is likely attributed to the relatively lower density of ZnS (4.09 g cm −3 ) compared to that of CdS (4.29 g cm −3 ). Moreover, the pore width of the as-prepared mesoporous materials was estimated by applying the non-local density functional theory (NLDFT) fitting model to the adsorption data [52]. The NLDFT analysis indicated that all the samples have quite narrow pore-size distributions (insets of Figure 4a and Figure S3a-d) with an average pore size (D p ) of~6.8 and~5.8 nm for the CdS and ZnS NCAs, respectively, and in the range of~5.8-6.3 nm for the ZnS/CdS nanocomposites (see Table 1).

Photocatalytic Hydrogen Evolution Study
Owing to their intriguing optoelectronic properties and unique mesoporous nanoarchitecture, the present mesoporous NC-based materials are expected to promote photocatalytic reactions. For this purpose, the photocatalytic performance of the synthesized materials was evaluated for the H2 evolution reaction from water. The effect of ZnS content  Table 1. Textural parameters and energy band gap values for the mesoporous CdS, ZnS and ZnS/CdS NCAs. The respective data for the physical mixture of bulk ZnS and CdS microparticles with 50 wt.% ZnS (ZnS/CdS bulk) are also shown, determined from the N 2 physisorption and optical absorption measurements presented in Figure S4. The effect of ZnS loading on the electronic structure and optical absorption properties of the synthesized ZnS/CdS nanocomposites was examined via UV-visible/near-IR diffuse reflectance spectroscopy (UV-vis/NIR DRS). The optical absorption spectra (Figure 4b) of the reference CdS and ZnS NCAs, obtained by transforming the diffuse reflection data using the Kubelka-Munk function, indicate sharp absorption onsets at 495 and 322 nm that correspond to the interband (i.e., from valence band to conduction band) electron transitions in CdS and ZnS, respectively. Interestingly, the spectra of the heterostructured ZnS/CdS samples display two well-defined absorption onsets, one in the visible light range (400-500 nm) and the other in the UV range (260-360 nm). These distinct absorption bands correspond to the respective light absorption from the constituent CdS and ZnS NCs, thereby signifying the dual-semiconductor nature of the as-synthesized ZnS/CdS NCAs. Additionally, a noticeable trend is observed in the absorption edges of the CdS and ZnS components of the ZnS/CdS nanocomposites. Specifically, the absorption edge of CdS shows a consistent blue-shift from 488 nm to 475 nm as the ZnS content increases from 10 to 90 wt.%. Conversely, the absorption edge of ZnS exhibits a red-shift from 327 nm to around 355 nm with the increase in ZnS content. This trend is related to the strong electron interactions between the electronic states in CdS and ZnS NCs, demonstrating their good interfacial connectivity in the assembled frameworks, in line with the results from TEM and XPS analyses. The energy band gaps (E g ) of the CdS, ZnS and ZnS/CdS mesoporous structures were determined from the corresponding Tauc plots for direct band gap semiconductors (i.e., (αhν) 2 vs. hν plots, derived from the UV−vis/NIR DRS spectra), as shown in Figure 4c. The E g values of pure CdS and ZnS NCAs were estimated to be 2.51 ± 0.01 eV and 3.85 ± 0.02 eV, respectively (see Table 1). Compared to the band gap energies of bulk CdS (2.3-2.4 eV) and ZnS (3.6-3.7 eV), both mesoporous samples exhibit a small but resolved blue-shift in E g , which is indicative of a quantum confinement effect in the constituent CdS and ZnS nanoparticles due to their very small size (circa 5-6 nm according to the TEM analysis). Meanwhile, the strong interfacial interactions between CdS and ZnS NCs are also reflected in the band gaps of the ZnS/CdS nanocomposites, where their E g values systematically vary from 2.54 eV to 2.61 eV with increasing the ZnS content from 10 to 90 wt.% ( Table 1). Note that the referred E g values for the ZnS/CdS nanocomposites were estimated from the respective absorption bands in the visible light region of the Tauc plots, as shown in the inset of Figure 4c. Despite the widening of the band gap, however, all the prepared mesoporous ZnS/CdS NCAs exhibit visible light semiconducting properties, allowing them to effectively absorb a significant portion of the solar spectrum.

Photocatalytic Hydrogen Evolution Study
Owing to their intriguing optoelectronic properties and unique mesoporous nanoarchitecture, the present mesoporous NC-based materials are expected to promote photocatalytic reactions. For this purpose, the photocatalytic performance of the synthesized materials was evaluated for the H 2 evolution reaction from water. The effect of ZnS content on the photocatalytic H 2 evolution activity of the nanocomposites was investigated under visible light irradiation (λ ≥ 420 nm), using 20 mg of catalyst dispersed in an aqueous solution (20 mL) containing 0.35 M Na 2 S and 0.25 M Na 2 SO 3 as sacrificial reagents. Figure 5a compares the rates of H 2 evolution (averaged over 3-h reaction period) obtained for the pure CdS and ZnS NCAs, along with the different ZnS/CdS catalysts. It is evident that the pure ZnS NCAs demonstrate nearly negligible H 2 production activity (~4 µmol h −1 ), which is attributed to the insufficient visible light absorption due to the wide band gap of ZnS NCs (E g = 3.85 eV). Additionally, despite the visible light response of the CdS NCAs (E g = 2.51 eV), their H 2 production performance was relatively poor (~30 µmol h −1 ), primarily due to the rapid recombination of photo-excited electron-hole pairs. Conversely, ZnS and CdS hybridization has a significant impact on the photocatalytic performance, markedly improving the H 2 evolution rate. In particular, the photo-activity of ZnS/CdS NCAs was remarkably enhanced with increasing the loading amount of ZnS NCs, reaching a maximum H 2 -evolution rate of~0.32 mmol h −1 at 50 wt.% ZnS content (50-ZnS/CdS catalyst). This activity is about 10.7 and 80 times higher than that of single CdS and ZnS NCAs, respectively (Figure 5a). Further increase in the ZnS content to 70 wt.% leads to a small decrease in the H 2 evolution activity (0.27 mmol h −1 for the 70-ZnS/CdS catalyst), while the H 2 evolution rate of the 90 wt.% ZnS-loaded sample (90-ZnS/CdS) was significantly reduced to 0.1 mmol h −1 . As we will discuss in more detail later, the noticeably lower catalytic activities observed in the ZnS/CdS samples with low (10 wt.%) and high (90 wt.%) ZnS content can be attributed to the poorer charge transfer and separation ability, likely due to inadequate interfacial connectivity between unevenly distributed ZnS and CdS NCs in these assembled structures. The above findings thus indicate that the even (~1:1) mass distribution of ZnS and CdS NCs in the assembled structures plays a prominent role in the H 2 -evolution performance of the resulting materials. Consequently, we focused our further catalytic studies on reactions with the 50-ZnS/CdS catalyst. Note that blank experiments conducted in the absence of light or catalyst did not exhibit any evolution of H 2 , indicating that the observed production of H 2 is exclusively attributed to photocatalytic reactions.
is attributed to the insufficient visible light absorption due to the wide band gap of ZnS NCs (Eg = 3.85 eV). Additionally, despite the visible light response of the CdS NCAs (Eg = 2.51 eV), their H2 production performance was relatively poor (~30 µmol h −1 ), primarily due to the rapid recombination of photo-excited electron-hole pairs. Conversely, ZnS and CdS hybridization has a significant impact on the photocatalytic performance, markedly improving the H2 evolution rate. In particular, the photo-activity of ZnS/CdS NCAs was remarkably enhanced with increasing the loading amount of ZnS NCs, reaching a maximum H2-evolution rate of ~0.32 mmol h −1 at 50 wt.% ZnS content (50-ZnS/CdS catalyst). This activity is about 10.7 and 80 times higher than that of single CdS and ZnS NCAs, respectively (Figure 5a). Further increase in the ZnS content to 70 wt.% leads to a small decrease in the H2 evolution activity (0.27 mmol h −1 for the 70-ZnS/CdS catalyst), while the H2 evolution rate of the 90 wt.% ZnS-loaded sample (90-ZnS/CdS) was significantly reduced to 0.1 mmol h −1 . As we will discuss in more detail later, the noticeably lower catalytic activities observed in the ZnS/CdS samples with low (10 wt.%) and high (90 wt.%) ZnS content can be attributed to the poorer charge transfer and separation ability, likely due to inadequate interfacial connectivity between unevenly distributed ZnS and CdS NCs in these assembled structures. The above findings thus indicate that the even (~1:1) mass distribution of ZnS and CdS NCs in the assembled structures plays a prominent role in the H2-evolution performance of the resulting materials. Consequently, we focused our further catalytic studies on reactions with the 50-ZnS/CdS catalyst. Note that blank experiments conducted in the absence of light or catalyst did not exhibit any evolution of H2, indicating that the observed production of H2 is exclusively attributed to photocatalytic reactions. In addition to chemical composition, morphological effects may also affect the catalytic performance of ZnS/CdS catalysts. To assess this, we prepared a reference ZnS/CdS bulk catalyst with 50 wt.% ZnS content by physically mixing equal amounts of pre-formed ZnS and CdS microparticles (see experimental section). XRD and EDS characterization results indicated that the bulk reference catalyst consists of a polycrystalline mixture of ZnS and CdS ( Figure S4a) with 50 wt.% ZnS composition (Table S1). Additionally, compared to the mesoporous 50-ZnS/CdS nanocomposite, the bulk ZnS/CdS microparticles possess a significantly lower surface area and pore volume (S BET = 75 m 2 g −1 , V p = 0.15 cm 3 g −1 ) and a smaller energy band gap (E g = 2.32 eV), as determined via N 2 physisorption and UV-vis/NIR DRS measurements (see Figure S4b,c and Table 1). Interestingly, the reference ZnS/CdS bulk sample demonstrated a H 2 evolution rate of only~30 µmol h −1 , which is comparable to that of pure CdS NCAs and considerably lower than that of the mesoporous 50-ZnS/CdS nanocomposite (see Figure 5a). In addition, to better highlight the positive impact of the 3D mesoporous NC network structure on catalytic activity, we also prepared an untemplated reference nanocomposite, ZnS/CdS RNAs (RNAs: random NC-aggregates) containing 50 wt.% ZnS and compared its photocatalytic performance with that of the polymer-templated 50-ZnS/CdS catalyst. ZnS/CdS RNAs was synthesized following a template-free oxidative coupling of ZnS and CdS NCs, where the evaporation of solvent in the absence of polymer template resulted in the formation of close-packed NC-aggregates. EDS analysis indicated a ZnS content of 49.82 wt.% (Table S1), which closely aligns with that of the 50-ZnS/CdS sample. However, in contrast to the polymer-templated nanocomposite, the ZnS/CdS RNAs exhibited a different isotherm profile, resembling a combination of type-I and type-IV with an H3 hysteresis loop, indicative of a dense microporous structure (S BET~1 14 m 2 g −1 , V p = 0.07 cm 3 g −1 ) with small interstitial voids (~1.5 nm) (see Figure S5). Under the same reaction conditions (i.e., 20 mg of catalyst dispersed in a 0.35 M Na 2 S and 0.25 M Na 2 SO 3 solution), the ZnS/CdS RNAs catalyst yielded a visible light H 2 -evolution rate of~0.21 mmol h −1 (see Figure 5a), which is approximately 1.5 times lower than that of the mesoporous 50-ZnS/CdS nanocomposite. Therefore, based on the above results, it can be deduced that the 3D open-pore morphology with high surface area and the NC-network structure with nanoscale interfaces are contributing factors that enhance mass transport phenomena and the number of accessible active sites and thus play a crucial role in boosting the H 2 production performance of our mesoporous ZnS/CdS nanocomposite catalysts.
To further optimize the reaction conditions, we investigated the effects of different sacrificial electron donors and mass loadings of catalyst on photocatalytic H 2 production performance. To this end, we examined a series of customary sacrificial reagents, including tertiary amines, such as triethanolamine (TEOA) and triethylamine (TEA), lactic acid, methanol and a Na 2 S/Na 2 SO 3 mixture. The experiments were conducted in 20 mL of DI water, using a fixed amount (20 mg) of the mesoporous 50-ZnS/CdS catalyst. As depicted in Figure S6, the most favorable results were achieved when using a mixture of Na 2 S and Na 2 SO 3 as sacrificial reagents. It is generally recognized that the utilization of S 2− /SO 3 2− species as electron donor serves as an effective strategy to enhance the H 2evolution photoactivity of metal-sulfide catalysts. The S 2− /SO 3 2− pairs not only consume the surface-reaching holes but also mitigate the anodic photocorrosion of sulfur-containing catalysts (such as CdS and ZnS) by replenishing the loss of lattice sulfur with S 2− ions from the reaction solution [9, 15,53]. On this basis, the concentration of S 2− /SO 3 2− species during the photocatalytic reaction also plays an important role, as demonstrated by the control experiments performed using different concentrations of the Na 2 S/Na 2 SO 3 mixture (Figure 5b). The results indicate that the H 2 -evolution activity of 50-ZnS/CdS scales almost linearly with the Na 2 S/Na 2 SO 3 concentration and reaches a maximum of 0.58 mmol h −1 in a saturated aqueous electrolyte containing 1.4 M Na 2 S and 1.0 M Na 2 SO 3 . Furthermore, photocatalytic tests using different mass loadings of the 50-ZnS/CdS catalyst (dispersed in a 1.4 M Na 2 S and 1.0 M Na 2 SO 3 aqueous solution) indicated that the rate of H 2 evolution increased with the catalyst concentration, reaching a maximum at 1 g L −1 (Figure 5c). This result can be attributed to the saturation of light absorption by the catalyst particles.
A further increase of the catalyst concentration (to 1.5 and 2 g L −1 ) results in a gradual reduction in H 2 production performance (0.42 and 0.37 mmol h −1 , respectively), likely due to the light-scattering and shielding effects of the excessive number of catalyst particles in the reaction mixture.
Under the optimized reaction conditions (i.e., 1 g L −1 catalyst concentration and 1.4 M Na 2 S and 1.0 M Na 2 SO 3 sacrificial reagents), the 50-ZnS/CdS catalyst also demonstrated excellent photochemical stability. The stability was evaluated by conducting four consecutive 6-h photocatalytic H 2 -evolution runs under visible light irradiation (details shown in Section 2.6). As inferred from the results presented in Figure 5d, the 50-ZnS/CdS catalyst maintains its high H 2 -evolution activity without any signs of decline (within 5% experimental error) even after 24 h of irradiation. After stability tests, we performed EDS, XRD, XPS and N 2 physisorption characterizations to investigate the chemical and structural stability of the reused catalyst. EDS analysis of the retrieved catalyst indicated a Cd/Zn atomic ratio of 15.62:23.42, which corresponds to a ZnS content of 50.29 wt.% (see Table S1), very close to the initial ZnS loading amount of the fresh sample (50.37 wt.%). Additionally, no changes were observed in the crystal structure and chemical state of elements in the reused catalyst, as evidenced by its XRD pattern ( Figure S7a) and XPS spectra ( Figure S7c-e). The obtained results closely resembled those of the as-prepared 50-ZnS/CdS NCAs, substantiating the excellent chemical and structural stability of the catalyst during the examined conditions. However, N 2 physisorption measurements on the reused sample revealed a relatively lower BET surface area (~200 m 2 g −1 ) and pore volume (~0.26 cm 3 g −1 ) compared to the fresh material (S BET = 266 m 2 g −1 , V p = 0.31 cm 3 g −1 ) ( Figure S7b). In addition, pore size analysis indicated a slightly broader pore-size distribution, with a peak maximum at 6.2 nm. These small changes in the textural parameters are probably related to some minor photocorrosion, which leads to a rearrangement of nanoparticles within the porous structure. Regardless, the mesoporosity and surface area of 50-ZnS/CdS NCAs still remain high enough after the prolonged catalytic use. The 4-times reused catalyst also demonstrated a persistent H 2 -evolution activity for two additional photocatalytic cycles (see Figure S8), providing further confirmation of its impressive photocatalytic stability and reusability under the examined conditions. Remarkably, over the 36-h irradiation period, an average H 2 -evolution rate of 0.58 mmol h −1 (or~29 mmol g −1 h −1 mass activity) was achieved, which is associated with an apparent quantum yield (AQY) of 60% at λ = 420 nm, assuming that all incident photons are absorbed by the catalyst. To the best of our knowledge, this efficiency is among the highest reported thus far for CdZnS-based photocatalytic systems, according to previous studies [16][17][18][19][20][21][22][23][24][25][54][55][56][57][58]. A comparison of photocatalytic H 2 -evolution activities of some high-performance CdZnS-based photocatalysts is presented in Table S2. Furthermore, to assess the influence of S 2− /SO 3 2− concentration on the photochemical stability of 50-ZnS/CdS, we also conducted photocatalytic H 2 -evolution recycling tests (i.e., successive 4-h photocatalytic runs) using the typical 0.35 M Na 2 S and 0.25 M Na 2 SO 3 concentrations of sacrificial reagents. As shown in Figure S9, the lower S 2− /SO 3 2− concentration not only yielded an overall lower H 2 -evolution activity but also failed to prevent catalyst photocorrosion, as inferred from the gradual decline in H 2 -evolution rates observed during the second and third catalytic runs. Hence, this observation underscores the profound influence of the S 2− /SO 3 2− concentration on both the photoactivity and stability of the prepared mesoporous nanocomposites. Due to the large surface area and abundance of exposed active sites, the lower S 2− /SO 3 2− concentration is inadequate for the efficient consumption of surface-reaching holes, thus leading to lower rates of H 2 -evolution and gradual photocorrosion of the nanocomposites.

Photocatalytic Mechanism
To clarify our understanding of the interfacial electronic interactions between the CdS and ZnS components and gain insight into the photocatalytic H 2 production mechanism of the CdS/ZnS nanocomposites, we performed electrochemical impedance spectroscopy (EIS) and photoluminescence (PL) measurements. Figure 6a displays the Mott-Schottky (M-S) plots, i.e., the inverse square capacitance (1/C 2 ) versus applied potential diagrams, for the mesoporous CdS, ZnS and ZnS/CdS NCAs. The M-S plot of the bulk ZnS/CdS material with 50 wt.% ZnS is shown in Figure S10a. All the samples showed positive slopes in the M-S plots, indicating n-type conductivity. Furthermore, by extrapolating the linear fits of the M-S curves to 1/C 2 = 0, we determined the flat band potential (E FB ) of all the materials, and the results are compared in Table 2. All the measured potentials are reported relative to the reversible hydrogen electrode (RHE) at pH 7. For single-component CdS and ZnS NCAs, the estimated E FB levels were −0.70 V and −1.12 V, respectively, while the E FB positions of the ZnS/CdS materials range from −0.74 V to −1.06 V. Generally, E FB represents the electrochemical Fermi level energy (E F ) of the materials under the examined conditions, which is approximately 0.1-0.3 eV below the conduction band (CB) edge in highly doped n-type semiconductors [59]. In fact, the location of the CB edge potential (E CB ) can be calculated from E FB using Equations (4) and (5), presuming that the donor dopants are completely ionized [60].
where E F is the Fermi level energy, N D is the electron donor density and N c is the density of the effective states in the CB, which is given by: where h is the Planck constant, k is the Boltzmann constant, T is the temperature in Kelvin and m * e is the effective mass of electrons in the CB. In Equation (5), assuming that m e * ≈ m o , in which m o is the mass of a free electron, N c, was estimated to be~2.5 × 10 19 cm −3 . In addition, the donor density (N D ) of the studied catalysts was determined from the slope of the Mott-Schottky linear fits (see Table 2). The resultant N D values presented a progressive increase from 2.02 × 10 16 to 4.90 × 10 16 cm −3 with an increase in the ZnS ratio from 0 to 50 wt.%, followed by a relative decrease (to 2.32 × 10 16 and 3.32 × 10 16 cm −3 ) for the samples with higher ZnS contents (70 and 90 wt.%). Therefore, based on the obtained E FB and N D results, the E CB levels of the prepared materials were calculated, and the valence band (VB) edge potentials (E VB ) were subsequently determined by adding the respective optical band gaps (E g ) obtained from UV-vis/NIR spectra. Table 2 summarizes all the calculated band-edge potentials, from which a representative band-edge diagram for each catalyst was constructed, as illustrated in Figure 6b. By analyzing the band diagrams in conjunction with the corresponding electrochemical results, several important conclusions can be drawn. Firstly, the CB edge of all the prepared catalysts is positioned well above the H 2 O/H 2 reduction potential (−0.41 V vs. RHE at pH 7), demonstrating the thermodynamic ability of these materials to drive water reduction. Moreover, a clear cathodic shift is observed in the CB edge of the ZnS/CdS nanocomposites with increasing ZnS content (from 10 to 90 wt.%). This shift can be explained by the higher E FB level of ZnS (−1.12 V) relative to that of CdS (−0.7 V), which creates a built-in potential difference after their contact. As a result, an electron flow from ZnS to CdS will take place at the ZnS/CdS contact interface until thermodynamic equilibrium is reached between the two materials. Consequently, upon enrichment with ZnS NCs, the accumulation of electrons in CdS will progressively shift the CB edge level of the nanocomposites in a more negative (cathodic) direction, positioning it between those of pure ZnS and CdS, as evidenced by the obtained EIS results. The electron transfer from ZnS to CdS in the nanocomposites is also supported by the XPS results as well as the increasing N D values with the loading amount of ZnS. The relatively lower N D values obtained for the nanocomposites with high ZnS content (70 and 90 wt.%) and the ZnS/CdS bulk reference (see Table 2) likely suggest a weaker charge transfer effect between the ZnS and CdS components in these materials. To further elucidate this, the charge-transfer properties of the prepared catalysts were investigated via Nyquist plot analysis. EIS Nyquist measurements were conducted in 0.5 M Na 2 SO 4 electrolyte over a frequency span of 1 Hz-100 kHz using an AC amplitude of 10 mV and a DC bias of −1.3 V (vs. Ag/AgCl, saturated KCl). Figure 6c compares the Nyquist plots of pure CdS and ZnS NCAs with those of the ZnS/CdS nanocomposites with different ZnS content. The corresponding Nyquist plot of the ZnS/CdS bulk analogue is shown in Figure S10b. The charge-transfer resistance (R ct ) of each sample was obtained by fitting the Nyquist plots to a Randles equivalent circuit model (inset of Figure 6c and Figure S10b), and the results are listed in Table 2 and Table  S3. In brief, the simulated results indicate that all the ZnS/CdS nanocomposites possess lower R ct values (~285-747 Ω) than the pure CdS (~1312 Ω) and ZnS (~1362 Ω) NCAs. This suggests more favorable charge-transfer dynamics at the ZnS/CdS heterojunctions, which contribute to their enhanced photocatalytic performance. Among them, the 50-ZnS/CdS catalyst exhibits the lowest R ct (285 Ω), which aligns with its superior charge transfer and photoreduction activity. Comparatively, the bulk reference catalyst (ZnS/CdS bulk) features a significantly higher R ct (1499 Ω), despite having a similar composition and band-edge structure to the 50-ZnS/CdS nanocomposite. Collectively, these findings suggest that, in addition to the chemical composition, the nanoscale dimensionality of the ZnS/CdS contact interfaces plays a prominent role in enhancing the charge transfer dynamics and achieving superior photocatalytic efficiency.
Additional evidence for the importance of ZnS/CdS nanoscale heterojunctions in governing the efficiency of charge carrier transfer and separation processes is provided by time-resolved photoluminescence (TR-PL) measurements. Figure 6d depicts the TR-PL emission spectra of mesoporous CdS and 50-ZnS/CdS NCAs along with that of the ZnS/CdS bulk material, recorded using 375 nm pulse laser excitation. To obtain the carrier lifetimes, the PL decay curves were fitted with a biexponential function: F(t) = y 0 + Σ i A i e −t/τi (i = 1, 2), where A i is the amplitude fraction (Σ i A i = 1) and τ i is the carrier lifetime of each component. The two time-components in the equation reflect the fast radiative charge-carrier recombination at the surface (τ 1 ) and slow recombination of excitons in the bulk (τ 2 ), respectively. The estimated fast and slow lifetimes of carriers are tabulated in Table S4, from which the average lifetimes (τ av ) were calculated to be approximately 3.20 ± 0.017 ns and 3.70 ± 0.025 ns for the mesoporous CdS and 50-ZnS/CdS NCAs, respectively and 3.16 ± 0.011 ns for the ZnS/CdS bulk catalyst. These results attest to an improved interfacial charge transfer and separation process within the ZnS/CdS NCassembled structure and thereby to a more efficient utilization of photo-excited electrons for H 2 evolution. Moreover, as shown in Table S4, 50-ZnS/CdS has a lower percentage (65.0%) of τ 1 -carriers than pure CdS (72.5%), indicating that the surface recombination of electronhole pairs over CdS was inhibited upon hybridization with ZnS NCs. The efficient charge separation in the 50-ZnS/CdS catalyst was also confirmed via steady-state PL emission spectra obtained via excitation at 380 nm. As depicted in Figure S11a, the PL spectrum of pure CdS NCAs exhibits a strong emission at~494 nm (2.51 eV) corresponding to the band-edge excitonic relaxation of CdS NCs. Comparatively, the PL intensity of this peak is almost vanished in the 50-ZnS/CdS sample, indicating that the majority of photogenerated electron-hole pairs are dissociated over the ZnS/CdS structure, thus suppressing their recombination rate. However, this condition implies the spatial separation of charge carriers across the ZnS/CdS junctions, which is not supported by the apparent band-edge alignment between ZnS and CdS in the nanocomposites. In particular, as inferred from the band diagram of Figure 6b, the junction between ZnS and CdS is expected to form a type-I (straddling gap) band-alignment, which cannot promote the spatial separation of charge-carriers. Instead, the type-I junction configuration favours the accumulation of electrons and holes in CdS, thus increasing their recombination probability. Therefore, a more complex charge-dissociation mechanism likely occurs at the ZnS/CdS junctions, potentially involving interfacial charge transfer pathways between the band-edges of CdS and defect-induced energy levels commonly found in ZnS. This assumption is supported by the PL spectrum of ZnS NCAs ( Figure S11b), which exhibits not only an emission peak at 322 nm (3.85 eV) due to the band-edge relaxation but also multiple emission bands with peaks at 398 nm (3.12 eV), 432 nm (2.87 eV), 473 nm (2.62 nm) and 562 nm (2.21 eV) that are attributed to the radiative recombination of excitons through defect states. Typically, four types of point defects can be present in ZnS particles: sulfur vacancies (V S ), zinc vacancies (V Zn ), interstitial zinc atoms (I Zn ) and interstitial sulfur atoms (I S ). These defects introduce energy states within the band gap of ZnS, with the V S and I Zn levels located bellow the CB (donor states), while V Zn and I S create energy levels above the VB (acceptor states) [61]. It has been reported that the energy levels of vacancies are deeper than those of interstitial states, with I Zn situated closer to the CB than V S , and I S closer to the VB than V Zn [62]. In this context, the PL emission bands centered at 3.12 eV and 2.87 eV can be attributed to electron transitions from the I Zn and V S states to the VB of ZnS, while the bands around 2.62 eV and 2.21 eV are likely associated with excitonic relaxations from V S to I S and from I Zn to V Zn , respectively, as illustrated in Figure 7a [63].
On the basis of the above results, a plausible charge transfer and photocatalytic H 2 production mechanism is proposed for the ZnS/CdS nanocomposite catalysts ( Figure 7b). As revealed by the EIS analysis, CdS has a lower E FB level than ZnS and hence, upon hybridization, electrons tend to flow from ZnS to CdS until their electrochemical potentials reach equilibrium. During this process, the loss of electrons from ZnS will result to an upward band bending near the interface (depletion layer), while the simultaneous increase in electron density at the CdS side will lead to a downward bending of the energy bands (accumulation layer). We found that, at optimum ZnS composition (50 wt.%), a built-in potential of about 0.4 V (as determined from Mott-Schottky results) will be established at the ZnS/CdS interfaces, which consequently creates a strong internal electric field with a direction from ZnS to CdS. Upon visible light irradiation, CdS undergoes excitation and generates electron and holes in the CB and VB, respectively. On the other hand, as inferred via PL measurements (see Figure 7a), electrons in ZnS can only be excited to the interband V S and I Zn states through single or multiple visible light-photon absorption, leaving behind holes in the VB, as well as the V Zn and I S acceptor states. Due to the built-in electric field at the ZnS/CdS interfaces, the photoexcited electrons in the CB of CdS will drift towards ZnS and be captured at the V S and I Zn donor states, together with the photogenerated electrons in ZnS. Such electron transfer route is supported by the direction of the internal electric field and the fact that the energy levels of V S and I Zn donor states (ranging from −0.3 to −0.6 V) are located just below the E CB of CdS (−0.7 V), as illustrated in Figure 7b. On the other hand, the holes in the VB, V Zn and I S states of ZnS are driven by the electric field to the VB of CdS, where they accumulate alongside the holes in CdS. This hole transport pathway from ZnS to CdS is not only influenced by the internal electric field but is also thermodynamically feasible, as the E VB of ZnS (2.56 V) as well as the energy levels of V Zn and I S acceptor states (~1.65-2.31 V) are located below the E VB of CdS (1.62 V). Additional indication for the accumulation of holes in CdS was obtained through EDS analysis on the 50-ZnS/CdS catalyst retrieved after the control photocatalytic experiment in which TEOA was used as sacrificial electron donor. Regarding this, because TEOA exhibits a slower scavenging ability for the photogenerated holes compared to the S 2− /SO 3 2− species (see Figure S6), it is not expected to efficiently prevent the anodic photocorrosion of CdS by the accumulated photoholes. Indeed, as shown in Table S1, the EDS results of the retrieved catalyst (50-ZnS/CdS-c) revealed a Zn/Cd atomic ratio of~1.82, representing an increase of approximately 17.6% compared to the fresh sample (Zn/Cd ≈ 1.50). Additionally, the ZnS content increased from 50.34 to 55.14 wt.% after the photocatalytic reaction. Therefore, these results explicitly demonstrate a significant loss of Cd due to the photocorrosion of CdS, further proving its role as the hole acceptor in the ZnS/CdS heterojunctions. Consequently, via this defect-induced quasi-type-II charge transfer scheme, the photogenerated charge carriers in CdS and ZnS can be efficiently separated at the ZnS/CdS nanojunctions. The proposed charge transfer and separation mechanism endows electrons trapped in the donor states of ZnS with prolonged ability to participate in the catalytic reduction of H 2 O to generate H 2 . At the same time, the holes gathered in the VB of CdS can effectively oxidize the sacrificial S 2− /SO 3 2− species, thus increasing the photochemical activity and stability of the catalyst. Such photocatalytic mechanism is consistent with the results from the above electrochemical and spectroscopic studies. In addition, the mesoporous ZnS/CdS NCAs, owing to the 3D open-pore structure and high internal surface area, provide a high density of surface-active sites for redox reactions. As thus, the overall photocatalytic performance of these catalysts is significantly improved, highlighting their potential for efficient solar-fuel production.
reached between the two materials. Consequently, upon enrichment with ZnS NCs, the accumulation of electrons in CdS will progressively shift the CB edge level of the nanocomposites in a more negative (cathodic) direction, positioning it between those of pure ZnS and CdS, as evidenced by the obtained EIS results. The electron transfer from ZnS to CdS in the nanocomposites is also supported by the XPS results as well as the increasing ND values with the loading amount of ZnS. The relatively lower ND values obtained for the nanocomposites with high ZnS content (70 and 90 wt.%) and the ZnS/CdS bulk reference (see Table 2) likely suggest a weaker charge transfer effect between the ZnS and CdS components in these materials. To further elucidate this, the charge-transfer properties of the prepared catalysts were investigated via Nyquist plot analysis. EIS Nyquist measurements were conducted in 0.5 M Na2SO4 electrolyte over a frequency span of 1 Hz-100 kHz using an AC amplitude of 10 mV and a DC bias of −1.3 V (vs. Ag/AgCl, saturated KCl). Figure 6c compares the Nyquist plots of pure CdS and ZnS NCAs with those of the ZnS/CdS nanocomposites with different ZnS content. The corresponding Nyquist plot of the ZnS/CdS bulk analogue is shown in Figure S10b. The charge-transfer resistance (Rct) of each sample was obtained by fitting the Nyquist plots to a Randles equivalent circuit model (inset of Figures 6c and S10b), and the results are listed in Tables 2 and S3. In brief, the simulated results indicate that all the ZnS/CdS nanocomposites possess lower Rct values (~285-747 Ω) than the pure CdS (~1312 Ω) and ZnS (~1362 Ω) NCAs. This suggests more favorable charge-transfer dynamics at the ZnS/CdS heterojunctions, which contribute to their enhanced photocatalytic performance. Among them, the 50-ZnS/CdS catalyst exhibits the lowest Rct (285 Ω), which aligns with its superior charge transfer and photoreduction activity. Comparatively, the bulk reference catalyst (ZnS/CdS bulk) features a significantly higher Rct (1499 Ω), despite having a similar composition and band-edge structure to the 50-ZnS/CdS nanocomposite. Collectively, these findings suggest that, in addition to the chemical composition, the nanoscale dimensionality of the ZnS/CdS contact interfaces plays a prominent role in enhancing the charge transfer dynamics and achieving superior photocatalytic efficiency. (donor states), while VZn and IS create energy levels above the VB (acceptor states) [61]. It has been reported that the energy levels of vacancies are deeper than those of interstitial states, with IZn situated closer to the CB than VS, and IS closer to the VB than VZn [62]. In this context, the PL emission bands centered at 3.12 eV and 2.87 eV can be attributed to electron transitions from the IZn and VS states to the VB of ZnS, while the bands around 2.62 eV and 2.21 eV are likely associated with excitonic relaxations from VS to IS and from IZn to VZn, respectively, as illustrated in Figure 7a [63].

Conclusions
In summary, mesoporous dual-semiconductor ZnS/CdS nanocomposites have been successfully synthesized via a cross-linking polymerization of 5-7 nm-sized CdS and ZnS nanoparticles in the presence of a block-copolymer template. The ZnS/CdS NCAs are composed of tightly interconnected ZnS and CdS NCs that form a 3D open-pore structure with large internal surface area (circa 243-285 m 2 g −1 ) and narrow pore size distribution (circa 5.8-6.3 nm), as confirmed by elemental microprobe analysis, X-ray diffraction, electron microscopy, X-ray photoelectron spectroscopy and N 2 porosimetry measurements. By carefully adjusting the ZnS composition in the ZnS/CdS nanocomposites, we showed that the interfacial electronic connectivity between the ZnS and CdS components can be finely tuned to achieve enhanced charge-carrier separation efficiency. Valuable insights into the charge transfer pathways in the ZnS/CdS heterojunctions were provided by electrochemical impedance spectroscopy and photoluminescence studies. The results corroborate to a quasi-type-II interfacial charge-transfer scheme between the defect states in ZnS and band-edges of CdS, that promote the charge transfer and separation for efficient H 2 production. As a result, the optimized mesoporous ZnS/CdS catalyst with 50 wt.% ZnS content achieved an impressive photon-to-hydrogen conversion efficiency of about 60% at 420 nm, which ranks among the highest reported values compared to other CdZnS-based photocatalytic systems. Moreover, prolonged photocatalytic recycling tests demonstrated the catalyst's exceptional stability for H 2 evolution. Overall, this study not only enhances our understanding of the intricate charge transfer dynamics at the nanoscale ZnS/CdS junctions but also underscores the promising potential of these mesoporous nano-architectures to serve as efficient photocatalysts for solar-to-hydrogen conversion technologies.