Fabrication of Carbon Nanoﬁbers Decorated with Various Kinds of Metal Oxides for Battery Applications

: Carbon nanoﬁbers decorated with various metal oxide nanoparticles were fabricated by combining an electrospinning technique of bicomponent polymer mixture and a sol-gel reaction and subsequent carbonization process. Electrospun polymer nanoﬁbers consisting of polyacrylonitrile (PAN) and poly(vinyl pyrrolidone) (PVP) with controllable diameters were fabricated with PAN/PVP core/shell types via phase-separation due to the immiscibility between two polymers. The electrospun nanoﬁbers served as supporting materials with binding sites of PVP to incorpo-rate titanium oxide precursor. Subsequently, the carbonization of the ﬁbers led to the formation of carbon nanoﬁbers@TiO 2 for energy application, in which rutile TiO 2 nanoparticles were decorated on the surface of carbon nanoﬁber. Especially, this TiO 2 decorated carbon nanoﬁber electrode exhibited excellent electrochemical property in lithium-ion batteries ( ≈ 600 mA h g − 1 at C/5 rate for 100 cycles). Furthermore, the carbon nanoﬁbers were also successfully modiﬁed with other metal oxides, including NiO, SnO 2 , and ZrO 2 nanoparticles, in a similar manner.

Surface modification of carbon nanofibers with metal oxides has been considered as an efficient route for these purposes by combining the advantages of both components [21,22]. Metal oxides have received significant attention due to their high thermal and chemical stability, availability of green chemistry synthetic route, and diverse technical applications [23][24][25]. For example, TiO 2 is one of the most appropriate candidates for photocatalytic processes owing to its powerful oxidation capability, superior charge transport, and corrosion resistance [26][27][28][29]. Desirable photocatalytic properties, including enhanced absorption in the visible region, electron conductivity, and stability, were obtained by
Preparation of carbon nanofibers decorated with various metal oxides: Before electrospinning, blends of PAN and PVP were prepared by dissolving PAN and PVP (concentrations of 10, 15, and 20 wt%) in DMF at a mass ratio of 1:1 at 80 • C under magnetic stirring for 24 h to obtain a homogeneous solution. The resulting polymer solutions were transferred into a plastic syringe equipped for the electrospinning process. A variable high voltage power supply (Gamma High Voltage Research, ES40P-20W) was used to provide desired voltage (15-20 kV) depending on the concentration of the PAN/PVP solution for electrospinning. The needle tip was connected to the positive terminal of the high voltage power supply, and grounded aluminum (Al) foil was used as a target collector. The feeding rate of the polymer solution and distance between tip and collector were 1.2 mL/h and 15 cm, respectively. Electrospun polymer nanofibers were collected on the Al foil and dried in a vacuum to remove residual solvent. Then, the PAN/PVP nanofiber sheets were detached from the Al foil and immersed into alkoxide solutions diluted in hexane (0.1-0.5 mL/mL) for 1 h. Alkoxides-loaded PAN/PVP sheets were washed with excess hexane and dried in a vacuum oven for 24 h. The PAN/PVP nanofiber sheets with alkoxides were placed into a tube furnace for heat treatment. The samples were heated at a rate of 1 • C/min to 280 • C in the air to make TiO 2 nanoparticles, held for 1 h to stabilize the Energies 2021, 14, 1353 3 of 10 electrospun fibers, and carbonized at 800 • C for 1 h under a flowing nitrogen/hydrogen (95%/5%) mixture gas. The gas flow rate was adjusted to keep the net flow rate at 5 sccm.
Electrochemical test of Carbon nanofiber@TiO 2 electrode: A freestanding carbon nanofiber@TiO 2 electrode was made from PAN/PVP nanofiber sheets by electrospinning and heat treatment. The mass loading of the electrode was 1 mg cm −2 . Electrochemical properties of the half cell were evaluated using coin-type half-cells (2016R) that were composed of active materials (the freestanding carbon nanofiber@TiO 2 composite electrodes) as the working electrode and lithium metal as a counter electrode, which were prepared under an argon-filled glove box. The electrolyte was 1.3 M LiPF6 with ethylene carbonate/diethyl carbonate (PANAX Starlyte, Korea, 3/7 (v/v)) including 10 wt% fluoroethylene carbonate additive. The half-cells were tested galvanostatically between 0.01 and 3.0 V (versus Li/Li+) at C/20 and C/5 rates using WBCS 3000 battery systems.
Characterization: Surface morphologies of polymer fibers, alkoxide-loaded sample, and metal oxide-decorated carbon nanofibers were investigated by a scanning electron microscope (SEM Leo/Zeiss 1530). For the Transmission electron microscopy (TEM) characterization, the products were transferred onto a copper grid after dispersion by sonication in ethanol, and a JEM-1400 was used to obtain TEM images at an accelerating voltage of 100 kV. The crystalline phases of the samples were identified using X-ray diffraction (XRD) analysis (PANalytical X'Pert PRO Alpha-1 with Cu K-α1 source). Raman spectra were obtained using a Renishaw RM 1000 spectromicroscopy system (≈2 µm spot size). He-Ne laser emission at wavelengths of 633 nm was used for excitation in this study. The thermogravimetric analysis (TA Instruments SDT-Q600) was used to determine the weight of the metal oxides loaded to carbon nanofibers with a heating rate of 10 • C/min under air condition.

Results
Schematic illustration shows the overall procedure composed of three steps for fabricating carbon nanofibers decorated with metal oxides (Figure 1). The electrospun nanofibers of PAN/PVP mixtures were collected on the Al foil in the first step. The PAN and PVP were phase-separated upon electrospinning process due to the incompatibility between PAN and PVP. Subsequently, numerous alkoxides, as a precursor of metal oxide, were coated on the surface of electrospun PAN/PVP bicomponent fiber sheets. In the final step, carbon nanofibers decorated with many kinds of metal oxides were generated by carbonization of the polymer fibers and calcination of alkoxides to metal oxides. °C/min to 280 °C in the air to make TiO2 nanoparticles, held for 1 h to stabilize the electrospun fibers, and carbonized at 800 °C for 1 h under a flowing nitrogen/hydrogen (95%/5%) mixture gas. The gas flow rate was adjusted to keep the net flow rate at 5 sccm. Electrochemical test of Carbon nanofiber@TiO2 electrode: A freestanding carbon nan-ofiber@TiO2 electrode was made from PAN/PVP nanofiber sheets by electrospinning and heat treatment. The mass loading of the electrode was 1 mg cm −2 . Electrochemical properties of the half cell were evaluated using coin-type half-cells (2016R) that were composed of active materials (the freestanding carbon nanofiber@TiO2 composite electrodes) as the working electrode and lithium metal as a counter electrode, which were prepared under an argon-filled glove box. The electrolyte was 1.3 M LiPF6 with ethylene carbonate/diethyl carbonate (PANAX Starlyte, Korea, 3/7 (v/v)) including 10 wt% fluoroethylene carbonate additive. The half-cells were tested galvanostatically between 0.01 and 3.0 V (versus Li/Li+) at C/20 and C/5 rates using WBCS 3000 battery systems.
Characterization: Surface morphologies of polymer fibers, alkoxide-loaded sample, and metal oxide-decorated carbon nanofibers were investigated by a scanning electron microscope (SEM Leo/Zeiss 1530). For the Transmission electron microscopy (TEM) characterization, the products were transferred onto a copper grid after dispersion by sonication in ethanol, and a JEM-1400 was used to obtain TEM images at an accelerating voltage of 100 kV. The crystalline phases of the samples were identified using X-ray diffraction (XRD) analysis (PANalytical X'Pert PRO Alpha-1 with Cu K-α1 source). Raman spectra were obtained using a Renishaw RM 1000 spectromicroscopy system (≈2 µm spot size). He-Ne laser emission at wavelengths of 633 nm was used for excitation in this study. The thermogravimetric analysis (TA Instruments SDT-Q600) was used to determine the weight of the metal oxides loaded to carbon nanofibers with a heating rate of 10 °C/min under air condition.

Results
Schematic illustration shows the overall procedure composed of three steps for fabricating carbon nanofibers decorated with metal oxides (Figure 1). The electrospun nanofibers of PAN/PVP mixtures were collected on the Al foil in the first step. The PAN and PVP were phase-separated upon electrospinning process due to the incompatibility between PAN and PVP. Subsequently, numerous alkoxides, as a precursor of metal oxide, were coated on the surface of electrospun PAN/PVP bicomponent fiber sheets. In the final step, carbon nanofibers decorated with many kinds of metal oxides were generated by carbonization of the polymer fibers and calcination of alkoxides to metal oxides. PAN and PVP were chosen to serve as carbon sources and binding moieties of metal oxide precursors in the phase-separated PAN/PVP blend systems, respectively. Figure 2a shows a typical SEM image of the electrospun PAN/PVP nanofibers. As observed in Figure  2a, the bicomponent nanofibers were successfully generated without formation of any PAN and PVP were chosen to serve as carbon sources and binding moieties of metal oxide precursors in the phase-separated PAN/PVP blend systems, respectively. Figure 2a shows a typical SEM image of the electrospun PAN/PVP nanofibers. As observed in Figure 2a, the bicomponent nanofibers were successfully generated without formation of any droplets (or beads). Electrospun PAN/PVP nanofibers have smooth surfaces with an average diameter of ≈297 nm. It is well-known that the bicomponent nanofibers of PAN and PVP form phase-separated structures in the blended system due to their immiscibility [45]. To confirm the structures of bicomponent polymer fibers, the electrospun fibers were hydrothermally treated in an autoclave at 90 • C, since PVP dissolves well in water while PAN is insoluble. Figure 2b shows the SEM image of polymer nanofibers produced after water treatment. The average diameter of water-extracted nanofibers is ≈246 nm, which is smaller than that of the as-electrospun fibers. It means that PVP parts were selectively dissolved out from bicomponent nanofibers.
Thermoplastic PAN fibers were converted to thermosetting plastics via laddering of their binding during the stabilization step in the oxidative atmosphere [46]. The asprepared carbon nanofibers have a smaller diameter than the polymer nanofibers due to the pyrolysis of organic species and carbon densification during the heating process. It was seen that the carbon nanofibers have very smooth surface morphologies (Figure 2c). droplets (or beads). Electrospun PAN/PVP nanofibers have smooth surfaces with an average diameter of ≈297 nm. It is well-known that the bicomponent nanofibers of PAN and PVP form phase-separated structures in the blended system due to their immiscibility [45]. To confirm the structures of bicomponent polymer fibers, the electrospun fibers were hydrothermally treated in an autoclave at 90 °C, since PVP dissolves well in water while PAN is insoluble. Figure 2b shows the SEM image of polymer nanofibers produced after water treatment. The average diameter of water-extracted nanofibers is ≈246 nm, which is smaller than that of the as-electrospun fibers. It means that PVP parts were selectively dissolved out from bicomponent nanofibers. Thermoplastic PAN fibers were converted to thermosetting plastics via laddering of their binding during the stabilization step in the oxidative atmosphere [46]. The as-prepared carbon nanofibers have a smaller diameter than the polymer nanofibers due to the pyrolysis of organic species and carbon densification during the heating process. It was seen that the carbon nanofibers have very smooth surface morphologies (Figure 2c). PVP can provide the binding sites of inorganic materials, while PAN serves as one of the best precursors of carbon. Because PVP portions were the outer shell of the bicomponent nanofibers, Ti precursors can be readily combined with the PVP portion through a coordinated covalent bond with the partial negative charge of oxygen in the PVP structure [41]. Thus, titanium butoxide, a widely used TiO2 precursor in sol-gel reactions, was incorporated into the as-prepared PAN/PVP nanofibers by immersing nanofiber sheets into the precursor solution. The bicomponent nanofibers decorated with Ti precursors were converted to carbon nanofibers@TiO2 (CNF@TiO2) after a one-step heat treatment. Figure 3a shows that TiO2 nanoparticles with a diameter of 10 nm were coated on the surface of the carbon nanofibers. For the clear view of the composition of the CNF@TiO2, the samples were characterized by TEM and energy dispersive X-ray spectroscopy (EDX) line profiles. TiO2 nanoparticles were positioned on the surface of the carbon nanofibers, not encapsulated in the carbon nanofibers, as shown Figure 3.
Generally, 1-D structures using solution mixtures of polymer and different species to introduce certain chemical or physical properties were produced by electrospinning. The additives were embedded into a polymer or carbon fiber matrix in the hybrid polymer or carbon nanofibers due to the nature of the electrospinning method. In this case, the matrix layer can prevent the contact between additives and other materials or atmospheres, resulting in a reduction in reactivity or performance. Meanwhile, carbon nanofibers decorated with TiO2 nanoparticles can exhibit their properties, since the TiO2 nanoparticles are exposed to the exterior environment. PVP can provide the binding sites of inorganic materials, while PAN serves as one of the best precursors of carbon. Because PVP portions were the outer shell of the bicomponent nanofibers, Ti precursors can be readily combined with the PVP portion through a coordinated covalent bond with the partial negative charge of oxygen in the PVP structure [41]. Thus, titanium butoxide, a widely used TiO 2 precursor in sol-gel reactions, was incorporated into the as-prepared PAN/PVP nanofibers by immersing nanofiber sheets into the precursor solution. The bicomponent nanofibers decorated with Ti precursors were converted to carbon nanofibers@TiO 2 (CNF@TiO 2 ) after a one-step heat treatment. Figure 3a shows that TiO 2 nanoparticles with a diameter of 10 nm were coated on the surface of the carbon nanofibers. For the clear view of the composition of the CNF@TiO 2 , the samples were characterized by TEM and energy dispersive X-ray spectroscopy (EDX) line profiles. TiO 2 nanoparticles were positioned on the surface of the carbon nanofibers, not encapsulated in the carbon nanofibers, as shown Figure 3.
Generally, 1-D structures using solution mixtures of polymer and different species to introduce certain chemical or physical properties were produced by electrospinning. The additives were embedded into a polymer or carbon fiber matrix in the hybrid polymer or carbon nanofibers due to the nature of the electrospinning method. In this case, the matrix layer can prevent the contact between additives and other materials or atmospheres, resulting in a reduction in reactivity or performance. Meanwhile, carbon nanofibers decorated with TiO 2 nanoparticles can exhibit their properties, since the TiO 2 nanoparticles are exposed to the exterior environment. Figure 4a displays XRD patterns of the electrospun PAN/PVP nanofibers immersed into the solution of Ti butoxides before and after the carbonization process to demonstrate the degree of transformation of Ti precursor to TiO 2 . There are no obvious diffraction peaks in the samples before the heat-treatment because the structure of TiO 2 as-synthesized from hydrolyzing the alkoxide is amorphous [47]. However, the XRD patterns of the CNF@TiO 2 produced after carbonization at 800 • C show the typical diffraction peaks for crystalline TiO 2 . The characteristic diffraction peaks of TiO 2 can be found at several positions, indicating the complete reduction to form crystalline TiO 2 during the one-step carbonization. It was found that the crystalline phases of the TiO 2 nanoparticles on the Figure 4a displays XRD patterns of the electrospun PAN/PVP nanofibers immersed into the solution of Ti butoxides before and after the carbonization process to demonstrate the degree of transformation of Ti precursor to TiO2. There are no obvious diffraction peaks in the samples before the heat-treatment because the structure of TiO2 as-synthesized from hydrolyzing the alkoxide is amorphous [47]. However, the XRD patterns of the CNF@TiO2 produced after carbonization at 800 °C show the typical diffraction peaks for crystalline TiO2. The characteristic diffraction peaks of TiO2 can be found at several positions, indicating the complete reduction to form crystalline TiO2 during the one-step carbonization. It was found that the crystalline phases of the TiO2 nanoparticles on the carbon nanofibers observed using XRD were composed primarily of rutile in structure with a minority phase of anatase (JCPDS file No.84-1285 and 74-1219).
The Raman spectra of the samples before and after the carbonization process are shown in Figure 4b. The production of carbon was confirmed after the carbonization step of PAN, while there are no typical peaks in the case of non-carbonized PAN. The fundamental vibrations of the carbon after carbonization were observed at 1600 cm −1 and 1370 cm −1 , corresponding to the graphite band (G-band) and the disorder band (D-band), respectively. The intensity ratio of D band to G band (ID/IG) of the sample were calculated to be about 1.15, indicating amorphous characteristics of carbon [48]. The characteristic bands of TiO2 detected at 436 and 612 cm −1 , which correspond to the rutile modes [42], indicate the conversion of Ti precursors to TiO2, which is consistent with the XRD result. It should be noted that this preparation route is suitable for generating high-quality CNF@TiO2.   Figure 5 shows the TiO2 coated carbon nanofibers with different diameters. The diameters of the electrospun nanofibers were influenced by the viscosity of the polymer solutions, which were controlled by varying the concentrations of the PAN/PVP. When the concentration of PAN/PVP solution was increased from 10 wt% to 15 and 20 wt%, the diameter of the carbon nanofibers was increased from 80 nm to 200 nm and 450 nm, respectively. Furthermore, the population of TiO2 on the carbon nanofibers was also controlled by manipulating the amount of Ti precursors. At higher concentrations of Ti butoxide solution (Figure 5c), larger amounts of Ti precursors were deposited and grown on the PVP. After carbonization, the oxide mass loading correspondingly increased, as shown in Figure 3. The Raman spectra of the samples before and after the carbonization process are shown in Figure 4b. The production of carbon was confirmed after the carbonization step of PAN, while there are no typical peaks in the case of non-carbonized PAN. The fundamental vibrations of the carbon after carbonization were observed at 1600 cm −1 and 1370 cm −1 , corresponding to the graphite band (G-band) and the disorder band (D-band), respectively. The intensity ratio of D band to G band (ID/IG) of the sample were calculated to be about 1.15, indicating amorphous characteristics of carbon [48]. The characteristic bands of TiO 2 detected at 436 and 612 cm −1 , which correspond to the rutile modes [42], indicate the conversion of Ti precursors to TiO 2 , which is consistent with the XRD result. It should be noted that this preparation route is suitable for generating high-quality CNF@TiO 2 . Figure 5 shows the TiO 2 coated carbon nanofibers with different diameters. The diameters of the electrospun nanofibers were influenced by the viscosity of the polymer solutions, which were controlled by varying the concentrations of the PAN/PVP. When Energies 2021, 14, 1353 6 of 10 the concentration of PAN/PVP solution was increased from 10 wt% to 15 and 20 wt%, the diameter of the carbon nanofibers was increased from 80 nm to 200 nm and 450 nm, respectively. Furthermore, the population of TiO 2 on the carbon nanofibers was also controlled by manipulating the amount of Ti precursors. At higher concentrations of Ti butoxide solution (Figure 5c), larger amounts of Ti precursors were deposited and grown on the PVP. After carbonization, the oxide mass loading correspondingly increased, as shown in Figure 3.  Figure 5 shows the TiO2 coated carbon nanofibers with different diameters. The diameters of the electrospun nanofibers were influenced by the viscosity of the polymer solutions, which were controlled by varying the concentrations of the PAN/PVP. When the concentration of PAN/PVP solution was increased from 10 wt% to 15 and 20 wt%, the diameter of the carbon nanofibers was increased from 80 nm to 200 nm and 450 nm, respectively. Furthermore, the population of TiO2 on the carbon nanofibers was also controlled by manipulating the amount of Ti precursors. At higher concentrations of Ti butoxide solution (Figure 5c), larger amounts of Ti precursors were deposited and grown on the PVP. After carbonization, the oxide mass loading correspondingly increased, as shown in Figure 3. The amount of TiO2 on the surface of the electrospun carbon nanofibers was quantified by TGA. Figure 6 shows the TGA curves of the samples with different diameters of carbon nanofibers and amounts of TiO2. The major weight loss region was associated with the combustion of the carbon nanofibers, where the carbon began degrading at 450 °C and was completely burned out. The weight percentage of remaining TiO2 on the carbon nanofibers prepared using PAN/PVP (20 wt%) was calculated to ≈5 wt%. An increase of metal oxide amount is necessary to evaluate the energy density, particularly for energy-related applications such as lithium-ion batteries and supercapacitors. From this point of view, samples with a higher mass loading of TiO2 were obtained by decreasing the amount of carbon sources. As a result, the mass of TiO2 was increased up to 65 wt% in the samples with the smallest diameter and the highest loading concentration of TiO2 precursor solution, as shown in Figure 6. Therefore, carbon nanofibers decorated with a high mass loading of TiO2 by our approach may be candidate materials to exhibit high performance in energy application. The amount of TiO 2 on the surface of the electrospun carbon nanofibers was quantified by TGA. Figure 6 shows the TGA curves of the samples with different diameters of carbon nanofibers and amounts of TiO 2 . The major weight loss region was associated with the combustion of the carbon nanofibers, where the carbon began degrading at 450 • C and was completely burned out. The weight percentage of remaining TiO 2 on the carbon nanofibers prepared using PAN/PVP (20 wt%) was calculated to ≈5 wt%. An increase of metal oxide amount is necessary to evaluate the energy density, particularly for energyrelated applications such as lithium-ion batteries and supercapacitors. From this point of view, samples with a higher mass loading of TiO 2 were obtained by decreasing the amount of carbon sources. As a result, the mass of TiO 2 was increased up to 65 wt% in the samples with the smallest diameter and the highest loading concentration of TiO 2 precursor solution, as shown in Figure 6. Therefore, carbon nanofibers decorated with a high mass loading of TiO 2 by our approach may be candidate materials to exhibit high performance in energy application. Several TiO2 decorated carbon nanofiber composites were tested as anode materials in lithium-ion batteries. Figure 7a shows the freestanding electrode with different amounts of TiO2, which was flexible and did not have any physical damage under bend-  Several TiO 2 decorated carbon nanofiber composites were tested as anode materials in lithium-ion batteries. Figure 7a shows the freestanding electrode with different amounts of TiO 2 , which was flexible and did not have any physical damage under bending conditions. However, another electrode with large amounts of TiO 2 (65 wt%) shows many cracks and breakdown of the electrode as it was brittle due to low carbon content in its nanofibers. In the first cycle voltage and differential capacity (dQ/dV) profiles of the discharging (lithiation) and charging (delithiation) of the CNF@TiO 2 composite electrodes with different amounts of TiO 2 at a rate of C/20 in the range of 0.01-3.0 V, the first discharge capacities of CNF@TiO 2 (20 wt% TiO 2 and 30 wt% TiO 2 ) were 1755 and 1605 mA h g −1 , respectively (Supplementary Material, Figure S1). To further demonstrate the stability of the electrode during the electrochemical analysis, cyclic voltammetry (CV) and SEM analysis were conducted (Supplementary Material, Figure S2). The results indicated that the proposed electrode was stable. Increasing TiO 2 contents in the composite electrodes led to decreasing gravimetric capacity due to little specific capacity of TiO 2 compared to CNFs. However, the cycling performances of all of the CNF@TiO 2 composite anodes exhibit a highly stable property (Figure 7b,c). The 20 wt% TiO 2 and 30 wt% TiO 2 anodes showed discharge capacity of 724 and 547 mA h g −1 at a C/5 rate after 100 cycles, respectively. Excellent cycling performances of the two CNF@TiO 2 electrodes may be explained as follows: (i) a suitable amount of TiO 2 particles can act as active material without binder material, such as polyvinylidene fluoride (PVDF) during the lithiation/delithiation process. (ii) One-dimensional structures act as electron channels which can significantly increase the electrical conductivity. (iii) The freestanding electrode without a binder exhibits a low resistance value. (iv) Good mechanical properties of carbon nanofibers retains the structural integrity of electrodes during cycling. Further, the rate capability of the CNF@TiO 2 composite electrode (30 wt%) was evaluated at various C-rates, as shown in Figure S3. Notably, discharge capacity of the as-prepared electrode (≈290 mA h g −1 at 3C) was much higher than that of the bare TiO 2 electrode at the same conditions (45 mA h g −1 at 3C). The approach described in this study is a straightforward method for producing TiO2 on CNF. We extended this concept to decorate other metal oxides on the surface of CNF. Figure 8 shows the SEM images and the corresponding XRD patterns of CNF decorated with various metal oxides. Metal alkoxides were used as precursors for metal oxides due to their well-known protocol of sol-gel reaction. Zr butoxide solution was used for the preparation of ZrO2 in the same manner as Ti butoxide solution was for TiO2. As shown in Figure 8a  The approach described in this study is a straightforward method for producing TiO 2 on CNF. We extended this concept to decorate other metal oxides on the surface of CNF. Figure 8 shows the SEM images and the corresponding XRD patterns of CNF decorated with various metal oxides. Metal alkoxides were used as precursors for metal oxides due to their well-known protocol of sol-gel reaction. Zr butoxide solution was used for the preparation of ZrO 2 in the same manner as Ti butoxide solution was for TiO 2 . As shown in Figure 8a to their well-known protocol of sol-gel reaction. Zr butoxide solution was used for the preparation of ZrO2 in the same manner as Ti butoxide solution was for TiO2. As shown in Figure 8a,b, the deposition of ZrO2 nanoparticles (JCPDS file No.37-1484 and 42-1164) on the carbon nanofibers was accomplished, and their complete transformation was confirmed by indexing their representative XRD diffraction peaks. Besides, SnO2 (JCPDS file No.  and NiO (JCPDS file No. 47-1049) decorated carbon nanofibers were successfully produced by utilizing the corresponding alkoxides (Figure 8c-f).

Conclusions
In conclusion, we have described a facile route for the fabrication of carbon nanofibers decorated with various kinds of metal oxide nanoparticles through the combination of electrospinning and sol-gel method. PAN/PVP core/shell nanofibers with the controllable diameters formed by phase-separation of two immiscible polymers, serve effectively as the supporting structures for coating with metal oxides. TiO2, ZrO2, SnO2, and NiO nanoparticles were successfully converted from the corresponding metal alkoxides on the surface of CNF after heat treatment. Additionally, the density of the metal oxide nanoparticles exposed to the external environment was controlled simply by adjusting their concentrations of precursor solution and could be large in quantity. Furthermore, the freestanding CNF@TiO2 electrode consisting of a nanofiber structured sheet with a good mechanical property exhibited excellent electrochemical properties, including a highly stable

Conclusions
In conclusion, we have described a facile route for the fabrication of carbon nanofibers decorated with various kinds of metal oxide nanoparticles through the combination of electrospinning and sol-gel method. PAN/PVP core/shell nanofibers with the controllable diameters formed by phase-separation of two immiscible polymers, serve effectively as the supporting structures for coating with metal oxides. TiO 2 , ZrO 2 , SnO 2 , and NiO nanoparticles were successfully converted from the corresponding metal alkoxides on the surface of CNF after heat treatment. Additionally, the density of the metal oxide nanoparticles exposed to the external environment was controlled simply by adjusting their concentrations of precursor solution and could be large in quantity. Furthermore, the freestanding CNF@TiO 2 electrode consisting of a nanofiber structured sheet with a good mechanical property exhibited excellent electrochemical properties, including a highly stable cycling performance (a high reversible capacity of ≈600 mA h g −1 at C/5 rate after 100 cycles) in the lithium-ion battery system. This study provides an effective route to modify the surface of CNF with metal oxides, and they are potentially applicable for use in energy-related devices, such as batteries, supercapacitors, and dye-sensitized solar cells.