All reagents were analytical grade and were used without further treatment. Hexahydrate nitrate and polyvinylpyrrolidone (PVP) were purchased from Aladdin Reagent (China) Co., Ltd. Anhydrous ethanol, silver nitrate, and acetic acid were purchased from Sinopharm Group Chemical Reagent Co., Ltd.

A total of 3 g of polyvinylpyrrolidone (PVP) was weighed and added to 50 ml of ethanol, then the mixture, known as solution A, was stirred for 3 h until completely dissolved. In total, 2.171 g of cerium nitrate hexahydrate was dissolved in 10 ml of ethanol. After stirring, the solution was slowly added dropwise to solution A and stirred for about 6 h. The solution was spray–coated by the electrospinning method with a temperature of 20°C and a relative humidity of 50%. The film was dried in a vacuum oven at 40°C for 12 h. The dried film was then calcined in a muffle furnace at 550°C and incubated for 0.5 h. And finally a pale yellow cerium dioxide film was obtained.

Solution A and the cerium source solution were prepared under the same conditions and the two solutions were mixed under stirring. A total of 0.017 g of AgNO₃ was added to 5 ml of deionized water and stirred for 20 min. The silver source solution was slowly added dropwise to the above mixed solution and stirred for 2 h. In addition, by changing the content of AgNO₃ in the spinning solution, the morphological characteristics and properties of the spinning film under different silver contents were investigated. The solution of 0.051 and 0.085 g of silver nitrate was prepared by the same method, which means that the molar ratios of AgNO₃/Ce (NO₃)₃ in the spinning solution were 1:50, 3:50, and 5:50. The film was prepared by an electrospinning method. After drying under the same conditions, the film was calcined in a muffle furnace to 600°C for 1 h. Finally, cerium dioxide nanofiber membranes doped with nano-silver were obtained.

The products were characterized by thermogravimetric analysis (TG) and differential scanning calorimetry (DSC). The heating rate, the air flow rate, the injection volume, and the temperature range were 20 K/min, 100 ml/min, 2 mg and 25–800°C, respectively. The composition of membranes was characterized by a Brook D8 Advance X-Ray diffractometer with a scanning angle of 20–80°, a scanning step length of 0.02°, and using Cu target Kα (λ = 0.154056 nm) radiation with a working voltage of 40 kV and a current of 40 mA. The microstructures of membranes were observed by scanning electron microscopy, while the fibers and particles constituting membranes were characterized by scanning electron microscopy (SEM) and transmission electron microscopy (TEM). UV-visible absorption spectra of prepared samples were measured by an ultraviolet and visible spectrophotometer.

In order to investigate the photocatalytic properties of the prepared cerium dioxide fiber membranes and the cerium dioxide fibers doped with different proportions of nano-silver, they were applied to the reaction of photocatalytic degradation of water to produce hydrogen and compared with the bulk pure cerium oxide. The Labsolar H₂ photolysis system was developed by Beijing Prefectlight Technology Co., Ltd., and the detection device was a Shanghai Tianmei GC7900 Gas Chromatograph, with a Microsolar300 high performance analog daylight xenon lamp used as the simulation light source. A 100-mg sample was added to 100 ml of deionized water, and sodium sulfite was added as the sacrificial agent to carry out photocatalytic hydrogen production. The hydrogen production of each material was compared after 6 h of illumination.

Figure 1A shows the TG-DSC curves of PVP/Ce (NO₃)₃ composite membranes prepared by the electrospinning method. It can be seen from the figure that the sample has a large weight loss process at room temperature to 100°C, and the weight loss process is the elimination of the moisture absorbed by the sample and the possible residual solvent (Wang et al., 2013). It can be also proved that membranes have certain water absorption capacities. After that there are two large weight loss processes which correspond to two distinct exothermic peaks, especially the second exothermic peak. The first exothermic peak appears at 327°C, which indicates that from 100 to 400°C, the sample first absorbs heat, and the outer layer of the composite fiber PVP begins to decompose, then the cerium nitrate in the fiber is decomposed into cerium dioxide; the weight loss of the system during this decomposition is 15% (Mohammadiyan et al., 2018). After 550°C, the reaction is basically completed, the sample weight and heat flow curve are stable, and the final quality is about 10% of the original quality. Thus, the calcination temperature of the PVP/Ce (NO₃)₃ composite film can be set at 550°C.

Figure 1B shows the TG-DSC analysis of PVP/Ce(NO₃)₃/AgNO₃ for composite membrane materials. It can be seen from the figure that the final mass of the sample is about 14% of the original mass throughout the reaction. The weight loss phase from room temperature to 100°C is the residual solvent and moisture contained in the sample. There are three exothermic peaks since then, with two adjacent exothermic peaks from 100 to 450°C, then the process undergoes a more complex reaction. As can be seen from Figure 1B, the exothermic peak at 368°C corresponds to the initial decomposition of the polymer template, then cerium nitrate decomposes and oxidizes to cerium oxide. and the weight loss is about 30%. The exothermic peak at 420°C is a sign that the silver nitrate is thermally decomposed into silver nanoparticles with a weight loss ratio of 15%. The complete decomposition of PVP occurs between 450 and 600°C. From the TG-DSC curve, it can be seen that the thermal decomposition has been basically completed at 600°C. After the sample stabilizes, the heat flow curve tends to be smooth. The calcination temperature of the PVP/Ce (NO₃)₃/AgNO₃ composite film can be set at 600°C. When silver nitrate is introduced, a higher sintering temperature is needed to obtain the target product.

Figure 2A shows the XRD pattern of PVP/Ce(NO₃)₃ composite fiber membranes and the membranes after calcination at 550°C in air and incubated for 0.5 h. The result indicates that the membranes after calcination have obvious diffraction peaks at 2θ = 28.4°, 33.0°, 47.4°, 56.1°, 59.0°, 69.2°, 76.4°, and 78.8°, corresponding to the (111), (200), (220), (311), (222), (400), (331), and (420) crystal faces of cubic fluorite crystal CeO₂, which is consistent with the standard card of cerium dioxide (JCPDS card no. 43 -1002). Because the fibers in membranes are covered and encapsulated by a large number of polymer PVPs, two amorphous bread peaks appear in the XRD pattern which are the diffraction peaks of the polymer. In addition, there were no other sharp diffraction peaks, and it was found that the composite fiber membrane synthesized by the electrospinning method was formed into a face-centered cubic cerium dioxide with standard card JCPDS card no. 21-1272 after calcination.

Figure 2B shows the XRD pattern of PVP/Ce (NO₃)₃/AgNO₃ composite fiber membranes with different silver content after calcination at 600°C for 1 h in muffle furnace, which contains the molar ratios of AgNO₃/Ce (NO₃)₃ of 1:50, 3:50, and 5:50 respectively. From the XRD curve, it can be seen that at 2θ = 28.4°, 33.0°, 47.4°, 56.1°, 59.0°, 69.2°, 76.4°, and 78.8°, the diffraction peaks correspond to (111), (200), (220), (311), (222), (400), (331), and (420) planes of the cubic fluorite crystal CeO₂. At diffraction angles of 2θ = 37.98°, 44.18°, 64.42°, and 77.26°, the diffraction signals correspond to the (111), (200), (220), and (311) planes of silver, which match the standard card of the nano-silver cubic crystal structure (JCPDS card no. 04-0783). All the diffraction peaks for the three samples are cerium dioxide and nano-silver. And with the increase of the relative content of silver, the peak of nano-silver shows more strongly, while the diffraction peak of cerium dioxide is weakened. All of these have proven that the prepared material is a thin cerium dioxide fiber film material loaded with nano-silver.

Figure 3 shows the real photographs and SEM images of the PVP/Ce(NO₃)₃ composite fiber membranes and the membranes after calcination at 550°C in air. Figure 3A shows the real photographs of cerium dioxide after calcination. Obviously, the membrane has a greater degree of contraction and is pale yellow, the weight is very light and fragile, but still retains the structure of lamellae. Figure 3B shows the SEM image at a magnification of 100 μm, which shows that the sample is relatively flat and compact and has a high porosity. Figure 3C shows the SEM image at a magnification of 20 μm. It can be seen that the sample consists of a large number of nanofibers, and the fibers are disordered, within layers, and with no accumulation of fibers. Figure 3D shows the high resolution FESEM picture, the scale is 1 μm, the fiber is straight, the thickness and the distribution are uniform, the fiber diameter is about 100 nm, and has a very high aspect ratio.

Figure 4 shows the real photographs and SEM images of the Ag/CeO₂ fiber membrane prepared at different molar ratios of Ce(NO₃)₃/AgNO₃ including 1:50, 3:50, and 5:50. Figure 4A shows the real photographs of the sample after calcination at 600°C. It can be seen that the sample still retains the morphology of the membranes, and the addition of silver ions significantly increases the color of the sample which presents as brownish yellow when compared to the CeO₂ fiber membrane. Figures 4B–D show the SEM images of the Ag/CeO₂ fiber membrane prepared at different molar ratios of Ce(NO₃)₃/AgNO₃ including 1:50, 3:50, and 5:50. It can be seen that the sample still retains the fiber morphology. The fiber thickness of the Ag/CeO₂ membranes loaded with nano-silver is relatively uneven and the fiber distribution is more cluttered compared with the pure cerium oxide fiber. There is a phenomenon of heap and fracture in the microstructure of the membranes. Because of the introduction of metallic silver ions in the spinning solution, the introduction of this inorganic salt changes the electrostatic parameters of the spinning solution, making the electrospinning process of the spinning fluid become more complex and changeable and making fibers of uneven thickness. With the increase of silver ions, the overall morphology of the fiber becomes more uneven, and agglomeration is becoming more and more serious.

Figure 5 shows the TEM and HRTEM images of the nano-cerium dioxide membrane material. From Figure 5A, it can be observed that the cerium dioxide is a fibrous structure and the diameter of the fiber is about 100 nm. The morphology is well preserved and has a large aspect ratio. Figure 5B shows the high–resolution transmission electron microscopy (HRTEM) image. It can be seen that the fiber is actually made of nano–sized cerium dioxide grains. The cerium dioxide grains forming the fibers have a grain size of 15 nm, and there is a large number of lattice lines of cerium dioxide crystals. By measuring the interplanar spacing, it can be seen that the exposed active surface is a (111) plane and d₍₁₁₁₎ = 0.313 nm.

Figure 6 shows the TEM and HRTEM images of the Ag/CeO₂ fiber membrane with an Ag/CeO₂ molar ratio of 3:50. Figure 6A shows the TEM image of the sample at a 200-nm scale. It can be seen from the figure that the fibrous Ag/CeO₂ has a diameter of about 100 nm. Figure 6B shows an enlarged TEM image at 20 nm, and it can be clearly seen that the fibers are deposited from a large number of crystal particles with a grain size of about 10 nm. Figure 6C shows the HRTEM image, at 10 nm, of the Ag/CeO₂ fiber membrane with the Ag/CeO₂ molar ratio of 3:50. A large number of lattice lines are shown in which the spacing of most of the lattice lines is 0.31 nm corresponding to the (111) plane of the cerium dioxide cubic crystal structure, and there is also a lattice line with a crystal plane spacing of 0.22 nm corresponding to the (111) crystal face of Ag nanoparticles. All of the above analyses prove that the material is cerium dioxide fiber material doped with nano-silver, which corresponds to the XRD result.

Figure 7 shows the UV-Vis absorption spectra and its corresponding forbidden band width calculation for the pure cerium oxide fiber membrane and the cerium oxide fiber membrane with different amounts of loaded silver. As can be seen from Figure 7A, the light absorption of the pure cerium dioxide fiber membrane in the wavelength range of 400–800 nm is weak, and gradually increases before 400 nm. While compared with the nano–silver-loaded material, the absorption of nano-silver-loaded material in the visible light area has significantly improved. This is because the nano–silver loaded in the CeO₂ semiconductor brings defects, resulting in changes in the band structure and reduction of the band gap width. And the nano-silver particles have the capability to absorb light, so the material on the absorption of visible light intensity is significantly enhanced.

The band gap energy (Eg) values of pure cerium dioxide nanofiber membranes and cerium dioxide nanofiber membranes doped with different amounts of nano-silver were obtained by absorbance spectra using the Tauc relation (Tang et al., 2020; Wang et al., 2020; Wang and Tian, 2020; Wang et al., 2021e; Gao et al., 2021). ( F ( R ) h ν ) n = A ( h ν − E g ) (1) Where ν is the frequency, A is the absorption coefficient, and n is equal to 2. The band gap of the samples are obtained by a simple intercept method. In Figure 7B, the band gap width of pure cerium oxide fibers is consistent with the literature (Gao et al., 2018) (3.15 eV). When the molar ratios of Ag/CeO₂ are 1:50, 3:50, and 5:50, the corresponding band gap values are 3.08, 3.01, and 2.96 eV, respectively. It can be seen that the band gap of the Ag/CeO₂ fiber membrane decreases gradually with the increase of the relative content of metallic silver. After modification of the CeO₂ fiber membrane by Ag nanoparticles, the band gap of the CeO₂ fiber membrane is reduced.

Figure 8 shows the hydrogen production of bulk cerium dioxide, cerium dioxide nanofibers, and three different silver-doped cerium dioxide nanofiber membranes. It can be seen from the figure that the hydrogen production of the sample is increasing with the progress of the reaction, but the efficiency of hydrogen production decreases with the consumption of the sacrificial agent and the decrease of the catalyst activity. The hydrogenation efficiency of bulk cerium dioxide and cerium dioxide nanofibers are very low because the cerium dioxide only absorbs ultraviolet light, which leads to low photocatalytic activity. The photocatalytic hydrogen production efficiency of the noble metal nano-silver-doped cerium dioxide fiber material has been greatly improved due to the nano-silver as it is in contact with the cerium dioxide crystal to form a heterojunction, and the band of the semiconductor is bent at the interface. Then, the electrons shift from a high Fermi level to a low Fermi level, forming a Schottky barrier in the materials. Comparing 3 M ratios of Ag/CeO₂, the photocatalytic hydrogen is the highest when the molar ratio of Ag/CeO₂ is 3:50, and the hydrogen production is about 402 µmol/g after 6 h of illumination. The photocatalytic activity of CeO₂ fiber increases with the addition of nano-silver, but the photocatalytic activity decreases when the doped noble metal nano-silver goes over a certain limit. This is because the excess of nano-silver particles will become the recombination center of the carrier, which will capture the hole on the surface of the CeO₂ fiber, leading to a decrease of photogenerated carrier density and a reduction in photocatalytic performance. While too much precious metal particles will cover the active center of CeO₂, which will also reduce the photocatalytic performance of the system. Moreover, it can be seen from the SEM image that CeO₂ has a tendency to accumulate into blocks as the amount of silver increases which can make the specific surface area reduce.

Based on band theory and experimental results, Figure 9 shows the photocatalytic mechanism of CeO₂ and Ag/CeO₂ photocatalysts. When visible light irradiates on the surface of CeO₂, because the band gap of CeO₂ is large, it can only respond to ultraviolet light, so the probability of valence band electron transition to the conduction band is small. At the same time, the photocatalytic hydrogen production efficiency is low because a small number of electrons in the conduction band are easily recombined with the holes in the valence band. When Ag is loaded on the surface of CeO₂, the electron transition from the valence band of CeO₂ to its conduction band is accelerated, so that the Ag/CeO₂ photocatalyst can respond to visible light. The electrons that transition to the CeO₂ conduction band will accelerate the transfer to Ag particles, preventing the electron from recombination with the holes of the CeO₂ conduction band. The transfer and separation of electrons and holes play an important role in the whole process of photocatalytic hydrogen production. Ag particles act as the carrier of charge carrier transfer during the whole process.