Crystallization of TiO2-MoS2 Hybrid Material under Hydrothermal Treatment and Its Electrochemical Performance

Hydrothermal crystallization was used to synthesize an advanced hybrid system containing titania and molybdenum disulfide (with a TiO2:MoS2 molar ratio of 1:1). The way in which the conditions of hydrothermal treatment (180 and 200 °C) and thermal treatment (500 °C) affect the physicochemical properties of the products was determined. A physicochemical analysis of the fabricated materials included the determination of the microstructure and morphology (scanning and transmission electron microscopy—SEM and TEM), crystalline structure (X-ray diffraction method—XRD), chemical surface composition (energy dispersive X-ray spectroscopy—EDS) and parameters of the porous structure (low-temperature N2 sorption), as well as the chemical surface concentration (X-ray photoelectron spectroscop—XPS). It is well known that lithium-ion batteries (LIBs) represent a renewable energy source and a type of energy storage device. The increased demand for energy means that new materials with higher energy and power densities continue to be the subject of investigation. The objective of this research was to obtain a new electrode (anode) component characterized by high work efficiency and good electrochemical properties. The synthesized TiO2-MoS2 material exhibited much better electrochemical stability than pure MoS2 (commercial), but with a specific capacity ca. 630 mAh/g at a current density of 100 mA/g.


Introduction
There are currently many scientific studies associated with the search for new materials and construction solutions enabling the further advancement of lithium-ion battery (LIB) technology. These batteries are considered to be one of the leading energy storage methods, and currently constitute a rapidly developing area of research [1][2][3]. The determination of optimal correlations between the electrode materials (cathode and anode) is of great importance in the construction of lithium-ion cells. These dependencies significantly influence the parameters of the cells, such as voltage, capacity, with the volume of active material. The graphene@TiO 2 @MoS 2 hybrid material was characterized by a tvery high capacity of 980 mAh/g at a current density of 0.1 A/g, and a capacity retention of 89% after 200 cycles.
The energy crisis and environmental degradation have stimulated the rapid development of lithium-ion batteries and photocatalysts. TiO 2 -MoS 2 hybrid materials have great potential and are still widely tested both in rechargeable lithium-ion batteries and in photocatalysis, due to their excellent properties. In addition to the high chemical stability of both MoS 2 and TiO 2 , TiO 2 -MoS 2 hybrids also have other advantages. These include the combination of the strong optical absorption of TiO 2 with the high catalytic activity of MoS 2 , which is promising for photocatalysis, and the excellent structural stability of TiO 2 together with the high theoretical specific capacity and unique layered structure of MoS 2 , because of which these composites are exciting prospective anode materials. The objective of the present research was to obtain a TiO 2 -MoS 2 hybrid material, which would exhibit enhanced electrochemical performance as an anode material. To achieve this, we attempted to apply a hydrothermal method (with the use of different temperatures) for the synthesis of TiO 2 -MoS 2 hybrid materials. The prepared hybrid systems were further treated at 500 • C to increase their crystallinity. Most importantly, we demonstrated that the calcination process can significantly improve the electrochemical performance of TiO 2 -MoS 2 electrodes.

Fabrication of TiO 2 -MoS 2 Hybrid Systems
TiO 2 -MoS 2 hybrid systems (with a TiO 2 :MoS 2 molar ratio of 1:1) were synthesized via a hydrothermal method. First, in a plastic vessel, an appropriate amount of inorganic precursor of Mo (sodium molybdate dehydrate) was dissolved in 50 cm 3 of deionized water to form a transparent solution. Dissolution was carried out at room temperature in a closed vessel, using an IKAMAG R05 magnetic stirrer (IKA Werke GmbH, Staufen, Germany) at 500 rpm for 10 min. Then, an appropriate amount of the organic precursor of TiO 2 (titanium(IV) isopropoxide) was added dropwise to the solution and stirred for 10 min to obtain a suspension. After that time, the organic precursor of S, thiourea (in an appropriate quantity), was added to the reaction mixture and stirred for 60 min to disperse it. The obtained solution was transferred to a Teflon-lined stainless steel autoclave, and hydrothermally treated at 180 or 200 • C for 24 h. The hydrothermal reactor was cooled at room temperature, and the obtained hybrids were filtered and washed three times with deionized water. The precipitates were then dried at 60 • C for 6 h. At the final stage, the samples were ground and sieved through an 80-µm sieve. Selected samples of the obtained hybrids were calcined at 500 • C (with heating rate 5 • C/min) for 4 h under inert gas (N 2 ) using a Nabertherm P320 Controller (Lilienthal, Germany). The materials hydrothermally treated at 180 and 200 • C were labelled as TM_180 and TM_200, and those additionally calcined at 500 • C as TM_180_500 and TM_200_500.

Characterization of Synthesized Hybrid Materials
The physicochemical characterization of the fabricated materials included the determination of microstructure and morphology (SEM and TEM), crystalline structure (XRD), chemical surface Materials 2020, 13, 2706 4 of 21 composition (EDS), and the parameters of the porous structure (low-temperature N 2 sorption). Additionally, to confirm the chemical surface concentration and the presence of the characteristic surface groups of the synthesized materials, X-ray photoelectron spectroscopy (XPS) and Fourier-transform infrared spectroscopy (FTIR) were used [35,36].

Electrochemical Performance
The TiO 2 -MoS 2 hybrid material was used as a working electrode, lithium foil (Whatmann, 0.4-0.6 mm thick) as a counter, reference electrode, and separator, and 1 M of LiPF 6 in EC/DMC-1:1 by volume (dissolved in a mixture of ethylene carbonate and dimethyl carbonate) as an electrolyte. The working electrodes were prepared by a slurry tape casting procedure. Typically, the mass of the electrode was as follows: Li: ca. 4.5 mg (0.785 cm 2 ), TiO 2 -MoS 2 -3.5-4.0 mg. The slurry consisted of 70% wt. active hybrid materials, 15% wt. Acetylene Black and 15% wt. poly(vinylidene fluoride) (PVdF) dissolved in N-methyl-2-pyrrolidinone (NMP). The weight of the whole paste was 0.4 g. The slurry was tape-cast on the copper foil, and then the coated electrodes were dried at 120 • C for 24 h. Electrochemical tests were carried out in a Swagelok ® system. Galvanostatic charge/discharge tests were conducted on the battery measurement system at various current densities in the range 50-1000 mA/g with a cut-off voltage range of 0.01-3.0 V vs. Li/Li + at room temperature. The impedance of cells (0.01 Hz and 100 kHz) and cyclic voltammetry (scan rate of 0.1 mV/s over a potential range of 0.01-3.0 V (vs. Li + /Li)) were determined using the GTM750 Potentiostat/Galvanostat/ZRA (Gamry Instruments, Warminster, USA).

Microstructure and Morphology
For the visualization of the morphology and microstructure of the TiO 2 -MoS 2 hybrid materials, scanning and transmission electron microscopy were applied. The SEM images of samples TM_180 and TM_180_500 indicate the presence of irregular and spherical shaped particles of TiO 2 , which show a high tendency to agglomerate, as well as flower-shaped MoS 2 particles (Figure 1a,b). The SEM image of sample TM_200 (TiO 2 -MoS 2 hybrid system hydrothermally treated at 200 • C; Figure 1c) shows the presence of numerous flower-shaped MoS 2 particles, which probably covered the irregular particles of TiO 2 . The SEM image for a sample hydrothermally treated at 200 • C and additionally calcined at 500 • C (TM_200_500; Figure 1d) indicates irregular shaped particles and nanoplates merging into larger clusters. Numerous macropores are also visible. The physicochemical characterization of the fabricated materials included the determination of microstructure and morphology (SEM and TEM), crystalline structure (XRD), chemical surface composition (EDS), and the parameters of the porous structure (low-temperature N2 sorption). Additionally, to confirm the chemical surface concentration and the presence of the characteristic surface groups of the synthesized materials, X-ray photoelectron spectroscopy (XPS) and Fourier-transform infrared spectroscopy (FTIR) were used [35,36].

Electrochemical Performance
The TiO2-MoS2 hybrid material was used as a working electrode, lithium foil (Whatmann, 0.4-0.6 mm thick) as a counter, reference electrode, and separator, and 1 M of LiPF6 in EC/DMC-1:1 by volume (dissolved in a mixture of ethylene carbonate and dimethyl carbonate) as an electrolyte. The working electrodes were prepared by a slurry tape casting procedure. Typically, the mass of the electrode was as follows: Li: ca. 4.5 mg (0.785 cm 2 ), TiO2-MoS2-3.5-4.0 mg. The slurry consisted of 70% wt. active hybrid materials, 15% wt. Acetylene Black and 15% wt. poly(vinylidene fluoride) (PVdF) dissolved in N-methyl-2-pyrrolidinone (NMP). The weight of the whole paste was 0.4 g. The slurry was tape-cast on the copper foil, and then the coated electrodes were dried at 120 °C for 24 h. Electrochemical tests were carried out in a Swagelok ® system. Galvanostatic charge/discharge tests were conducted on the battery measurement system at various current densities in the range 50-1000 mA/g with a cut-off voltage range of 0.01-3.0 V vs. Li/Li + at room temperature. The impedance of cells (0.01 Hz and 100 kHz) and cyclic voltammetry (scan rate of 0.1 mV/s over a potential range of 0.01-3.0 V (vs. Li + /Li)) were determined using the GTM750 Potentiostat/Galvanostat/ZRA (Gamry Instruments, Warminster, USA).

Microstructure and Morphology
For the visualization of the morphology and microstructure of the TiO2-MoS2 hybrid materials, scanning and transmission electron microscopy were applied. The SEM images of samples TM_180 and TM_180_500 indicate the presence of irregular and spherical shaped particles of TiO2, which show a high tendency to agglomerate, as well as flower-shaped MoS2 particles (Figure 1a,b). The SEM image of sample TM_200 (TiO2-MoS2 hybrid system hydrothermally treated at 200 °C; Figure  1c) shows the presence of numerous flower-shaped MoS2 particles, which probably covered the irregular particles of TiO2. The SEM image for a sample hydrothermally treated at 200 °C and additionally calcined at 500 °C (TM_200_500; Figure 1d) indicates irregular shaped particles and nanoplates merging into larger clusters. Numerous macropores are also visible.  The TEM images for TiO2-MoS2 samples hydrothermally treated at 180 and 200 °C (Figure 2a,b) indicate the presence of spherical particles characteristic of titanium dioxide, as well as sheets, which can be attributed to the presence of molybdenum disulfide.

Crystalline Structure
The determination of the crystalline structure of the synthesized TiO2-MoS2 hybrid materials was a key goal of the physicochemical analysis. The XRD results are shown in Figure 3.
The XRD pattern of sample TM_180 (TiO2-MoS2 hybrid system hydrothermally treated at 180 °C; Figure 3a) [37]. The interpretation of the XRD pattern of a TiO2-MoS2 hybrid system hydrothermally treated at 200 °C ( Figure 3b) demonstrates that increasing the temperature of the thermal treatment leads to a product with slightly better crystallinity. Powder diffraction patterns for TiO2-MoS2 hybrid systems hydrothermally treated at 180 and 200 °C and additionally calcined at 500 °C ( Figure. 3a, b; black curves) indicate that the calcination process leads to products in which the reflections from MoS2 are higher. It was confirmed that the higher temperature of thermal treatment led to final products with more intensive reflections characteristic of the MoS2 structure. Xu et al. [9] also observed that, after annealing, the reflection characteristic of MoS2 at 2θ = 14.33° is sharper, which suggests the better crystallinity of TiO2@MoS2 composites after annealing. For the analyzed samples, on the XRD patterns (Figure 3a [38]. Prabhakar Vattikuti et al. [38] also reported the formation of the orthorhombic phase γ-MoO3 space group P63/mmc no. 194, which is probably related to the oxidization of some of the MoS2 in the

Crystalline Structure
The determination of the crystalline structure of the synthesized TiO 2 -MoS 2 hybrid materials was a key goal of the physicochemical analysis. The XRD results are shown in Figure 3. hydrothermal process. Moreover, Li et al. [32] demonstrated that the hydrothermal route is an effective method enabling the successful coating of MoS2 sheets in a TiO2@MoS2 nanocomposite. They noted that, after thermal treatment of the nanocomposite at 800 °C, most of the reflections became more intense and sharper, while the intensities of the diffraction peaks of TiO2 decreased. Moreover, for fabricated hybrid materials, the phase composition (% wt.) and the lattice parameter of each phase were determined from the Rietveld method using the Fullprof software [39]. The results are presented in Table 1.   The XRD pattern of sample TM_180 (TiO 2 -MoS 2 hybrid system hydrothermally treated at 180 • C; Figure 3a) [37]. The interpretation of the XRD pattern of a TiO 2 -MoS 2 hybrid system hydrothermally treated at 200 • C (Figure 3b) demonstrates that increasing the temperature of the thermal treatment leads to a product with slightly better crystallinity. Powder diffraction patterns for TiO 2 -MoS 2 hybrid systems hydrothermally treated at 180 and 200 • C and additionally calcined at 500 • C (Figure 3a,b; black curves) indicate that the calcination process leads to products in which the reflections from MoS 2 are higher. It was confirmed that the higher temperature of thermal treatment led to final products with more intensive reflections characteristic of the MoS 2 structure. Xu et al. [9] also observed that, after annealing, the reflection characteristic of MoS 2 at 2θ = 14.33 • is sharper, which suggests the better crystallinity of TiO 2 @MoS 2 composites after annealing. For the analyzed samples, on the XRD patterns (Figure 3a [38]. Prabhakar Vattikuti et al. [38] also reported the formation of the orthorhombic phase γ-MoO 3 space group P6 3 /mmc no. 194, which is probably related to the oxidization of some of the MoS 2 in the hydrothermal process. Moreover, Li et al. [32] demonstrated that the hydrothermal route is an effective method enabling the successful coating of MoS 2 sheets in a TiO 2 @MoS 2 nanocomposite. They noted that, after thermal treatment of the nanocomposite at 800 • C, most of the reflections became more intense and sharper, while the intensities of the diffraction peaks of TiO 2 decreased. Moreover, for fabricated hybrid materials, the phase composition (% wt.) and the lattice parameter of each phase were determined from the Rietveld method using the Fullprof software [39]. The results are presented in Table 1.

Surface Chemical Composition
To investigate the surface elemental composition of the synthesized TiO 2 -MoS 2 hybrid systems, energy-dispersive X-ray spectrometry (EDS) was used ( Figure 4).
The results indicate that the TiO 2 -MoS 2 hybrid system hydrothermally treated at 200 • C and additionally calcined at 500 • C (TM_200_500; Figure 4d) had the highest content of molybdenum (56.51%) and the lowest content of titanium (16.17%) among all of the synthesized materials. Furthermore, the results of the EDS analysis for all samples show that the percentage content of titanium decreased, and that of molybdenum increased, when the temperature of the hydrothermal treatment increased from 180 to 200 • C. The EDS results confirmed the effectiveness of the proposed hydrothermal method in the synthesis of TiO 2 -MoS 2 hybrid materials. Moreover, it was demonstrated that the temperature of hydrothermal treatment has a small effect on the surface composition of the analyzed materials. It was shown that the hydrothermal method makes it possible to obtain hybrid materials with strictly defined properties.  The results indicate that the TiO2-MoS2 hybrid system hydrothermally treated at 200 °C and additionally calcined at 500 °C (TM_200_500; Figure 4d) had the highest content of molybdenum (56.51%) and the lowest content of titanium (16.17%) among all of the synthesized materials. Furthermore, the results of the EDS analysis for all samples show that the percentage content of titanium decreased, and that of molybdenum increased, when the temperature of the hydrothermal treatment increased from 180 to 200 °C. The EDS results confirmed the effectiveness of the proposed hydrothermal method in the synthesis of TiO2-MoS2 hybrid materials. Moreover, it was demonstrated that the temperature of hydrothermal treatment has a small effect on the surface composition of the analyzed materials. It was shown that the hydrothermal method makes it possible to obtain hybrid materials with strictly defined properties.

Textural Properties
Many studies have proven that the surface area of an electrode material affects the efficiency of the electrochemical process [40,41]. In view of this fact, to investigate the textural properties of the synthesized hybrid products, low-temperature N2 sorption was carried out ( Figure 5). The pore size distribution (Sp) and pore volume (Vp) were analyzed using the Barrett-Joyner-Halenda (BJH) method, and the surface area (ABET) was calculated using the Brunauer-Emmett-Teller (BET) method. The isotherm curves of the TiO2-MoS2 hybrid materials ( Figure 5) are in good agreement with type IV isotherms with H3 hysteresis behavior, which are characteristic of mesoporous products according to the International Union of Pure and Applied Chemistry (IUPAC) classification [40].
The values obtained for parameters of the porous structure showed that TiO2-MoS2 hybrid systems hydrothermally treated at 180 and 200 °C without calcination (samples TM_180 and TM_200; Figure 5a,b) had a lower BET surface area than the corresponding products which were additionally calcined at 500 °C. The BET surface area was 30 m 2 /g and 23 m 2 /g for samples TM_180 and TM_200, respectively. The lower value of the BET surface area for sample TM_200 confirms that the higher temperature of the hydrothermal treatment causes greater sintering of the particles of the material and the formation of agglomerates, which is accompanied by the collapse of the porous structure of the material. A high temperature of hydrothermal treatment accelerates the evaporation of water from the fabricated hybrid material, contributing to the loss of surface hydroxyl (-OH) groups, whose presence increases the surface area [42]. The mean pore diameter of these materials

Textural Properties
Many studies have proven that the surface area of an electrode material affects the efficiency of the electrochemical process [40,41]. In view of this fact, to investigate the textural properties of the synthesized hybrid products, low-temperature N 2 sorption was carried out ( Figure 5). The pore size distribution (S p ) and pore volume (V p ) were analyzed using the Barrett-Joyner-Halenda (BJH) method, and the surface area (A BET ) was calculated using the Brunauer-Emmett-Teller (BET) method. The isotherm curves of the TiO 2 -MoS 2 hybrid materials ( Figure 5) are in good agreement with type IV isotherms with H3 hysteresis behavior, which are characteristic of mesoporous products according to the International Union of Pure and Applied Chemistry (IUPAC) classification [40].
The values obtained for parameters of the porous structure showed that TiO 2 -MoS 2 hybrid systems hydrothermally treated at 180 and 200 • C without calcination (samples TM_180 and TM_200; Figure 5a,b) had a lower BET surface area than the corresponding products which were additionally calcined at 500 • C. The BET surface area was 30 m 2 /g and 23 m 2 /g for samples TM_180 and TM_200, respectively. The lower value of the BET surface area for sample TM_200 confirms that the higher temperature of the hydrothermal treatment causes greater sintering of the particles of the material and the formation of agglomerates, which is accompanied by the collapse of the porous structure of the material. A high temperature of hydrothermal treatment accelerates the evaporation of water from the fabricated hybrid material, contributing to the loss of surface hydroxyl (-OH) groups, whose presence increases the surface area [42]. The mean pore diameter of these materials was 7.7 nm (sample TM_180) and 11.4 nm (sample TM_200), and the total pore volume was equal to 0.064 cm 3 /g and 0.070 cm 3 /g for samples hydrothermally treated at 180 and 200 • C, respectively. After the calcination of the materials at 500 • C, the resultant BET surface areas were found to be 56 m 2 /g and 48 m 2 /g for samples TM_180_500 and TM_200_500, respectively. The total pore volume of sample TM_180_500 was 0.107 cm 3 /g, and the mean pore diameter 7.2 nm, while the mean pore diameter of sample TM_200_500 was 10.0 nm and the total pore volume 0.134 cm 3 /g.
An analysis of the parameters of the porous structure indicated that thermal treatment at 500 • C positively affected the value of the BET surface area of the fabricated hybrid materials. The higher BET surface area of TiO 2 -MoS 2 materials is probably related to the formation of the MoO 3 crystalline phase, which is confirmed by the XRD analysis. Moreover, N 2 adsorption/desorption isotherms for all synthesized materials ( Figure 5) exhibited a significant opening of the hysteresis loops, which indicates sample TM_180_500 was 0.107 cm 3 /g, and the mean pore diameter 7.2 nm, while the mean pore diameter of sample TM_200_500 was 10.0 nm and the total pore volume 0.134 cm 3 /g. An analysis of the parameters of the porous structure indicated that thermal treatment at 500 °C positively affected the value of the BET surface area of the fabricated hybrid materials. The higher BET surface area of TiO2-MoS2 materials is probably related to the formation of the MoO3 crystalline phase, which is confirmed by the XRD analysis. Moreover, N2 adsorption/desorption isotherms for all synthesized materials ( Figure 5) exhibited a significant opening of the hysteresis loops, which indicates a developed mesoporous structure. The presence of mesopores in the synthesized hybrid materials may be desirable for energy storage applications.

FTIR Analysis
Fourier transform infrared spectroscopy was used to identify changes in the chemical structure of the synthesized hybrid systems based on TiO2 and MoS2. The FTIR spectra of the TiO2-MoS2 materials are shown in Figure 6.
The FTIR analysis for the obtained hybrid systems showed the presence of an absorption band at wavenumber 680 cm −1 , corresponding to stretching vibrations of the Ti-O-Ti group [43,44]. Symmetric and asymmetric stretching vibrations of the Mo-O group at 818 cm −1 , 773 cm −1 and 675 cm −1 were also observed [45]. Moreover, the absorption band present at wavenumber 900 cm −1 indicates the presence of Mo-S bonds [43]. The bands at the wavenumbers 1100 cm −1 and 1400 cm −1 may correspond to stretching vibrations of the C-O group, while the signal at wavenumber 1500 cm −1 may indicate the presence of stretching vibrations of the N-H group [42]. The bands at 1636 cm −1 and 3365 cm −1 are attributed to hydroxyl groups (-OH) and water on MoS2 [46]. The band located at 1149 cm −1 corresponds to asymmetric S=O and S-O stretching vibrations [46].

FTIR Analysis
Fourier transform infrared spectroscopy was used to identify changes in the chemical structure of the synthesized hybrid systems based on TiO 2 and MoS 2 . The FTIR spectra of the TiO 2 -MoS 2 materials are shown in Figure 6.   [45]. Moreover, the absorption band present at wavenumber 900 cm −1 indicates the presence of Mo-S bonds [43]. The bands at the wavenumbers 1100 cm −1 and 1400 cm −1 may correspond to stretching vibrations of the C-O group, while the signal at wavenumber 1500 cm −1 may indicate the presence of stretching vibrations of the N-H group [42]. The bands at 1636 cm −1 and 3365 cm −1 are attributed to hydroxyl groups (-OH) and water on MoS 2 [46]. The band located at 1149 cm −1 corresponds to asymmetric S=O and S-O stretching vibrations [46].
The interpretation of the results indicates the presence of Ti-O-Ti, Mo-S, and -OH groups in the synthesized hybrid materials. It was shown that a change in the temperature of hydrothermal treatment (from 180 to 200 • C) does not affect the intensity of the characteristic bands. On the other hand, calcination caused a decrease in band intensity for the -OH group, although it did not change the intensity of the characteristic bands from TiO 2 .

XPS Analysis
Detailed high-resolution X-ray photoelectron spectra were acquired for the fresh sample TM_200 and for the corresponding sample after calcination, TM_200_500. They are presented in Figure 7. The XPS Ti 2p spectrum observed for both analyzed samples consists of a doublet of peaks originating from a spin-orbit splitting of Ti 2p orbitals (see Figure 7a). The most intense peak, the component Ti 2p 3/2 , has a maximum at a binding energy of 458.8 eV. The shift of the Ti 2p 1/2 component is 5.7 eV. Both the position and the shift are characteristic of TiO 2 [47,48]. The position and the envelope of the spectra recorded for samples before and after calcination are virtually identical, which indicates a lack of chemical transformation of titania during this process. region around 530 eV [48,52]. TiO2 and MoO3 are indistinguishable in this analysis. The XPS S 2p (Figure 7d) spectrum acquired for the TM_200 sample consists of two maxima. The more intense of these is located at a binding energy of approximately 162 eV and corresponds to the presence of MoS2 [49]. The other local maximum, centered at a binding energy of 169.6 eV, is usually attributed to the presence of hexavalent sulfur atoms, S 6+ , as in sulfates [51]. The presence of the latter is corroborated by a notable shoulder in the XPS O 1s spectrum at a binding energy of approximately 532 eV, which can also be attributed to SO4 2-ions [51]. After calcination, both components originating from S-O interactions disappear, indicating that the elevated temperature induced the decomposition of these bonds. The results described above indicate that the surface of the TiO2-MoS2 hybrid is a complex structure. The predominant compounds are titanium dioxide and molybdenum disulfide, as was also observed with the use of other analytical methods. However, the substantial oxidation of MoS2 to MoO3 is observed, and this is more prominent for the calcined sample. The surface of the fresh sample also contains SO4 2-ions, which are removed at an elevated temperature.

Electrochemical Performance
It has been noted in recent years that, just as graphene is obtained from graphite, layers of individual atoms can be obtained from many other crystals. Such layers have been produced for, among others, transition metal chalcogenides such as sulfides, selenides and tellurides. Molybdenum disulfide (MoS2) layers have proved to be a particularly interesting material. This compound occurs in nature as molybdenite, a crystalline mineral often taking the form of characteristic hexagonal plates with a silvery color. Molybdenite, which resembles graphite and has often been confused with it, is found in rocks around the world. It has been used for many years in the production of lubricants and metal alloys. As with graphite, the properties of monatomic MoS2 Some variations of the peak envelopes are observed after the calcination of sample TM_200 (TM_200_500) in binding energy regions characteristic of molybdenum, oxygen and sulfur (see Figure 7b-d). The X-ray photoelectron spectrum of the Mo 3d region is complex and consists of several local maxima. At approximately 226 eV, a component originating from sulfur atoms (XPS S 2s peak) is observed [49]. The main maximum at 229.0 eV originates from the electrons of the Mo 3d 5/2 component [50]. This position is attributed to the presence of MoS 2 . Mo 3d orbitals have a spin-orbit splitting of about 3.2 eV. Therefore, a Mo 3d 3/2 component coming from molybdenum atoms bound with sulfur atoms should be located at a binding energy of approximately 230 eV. There is a prominent peak at this position. However, it is a superposition of two components: Mo 3d 3/2 from MoS 2 , and another Mo 3d 5/2 component originating from the electrons of Mo 6+ ions in MoO 3 [51]. This last component is confirmed by the presence of its spin-orbit component (a local maximum at approximately 335.6 eV). The observed Mo 3d spectrum envelopes indicate that the surface of the sample consists of MoS 2 as well as MoO 3 , before and after calcination. However, after calcination, the local maximum at 335.6 eV, characteristic of MoO 3 , is more prominent. In spite of the inert atmosphere in which the calcination at 500 • C was carried out, some oxidation of molybdenum compounds takes place during this process.
An analysis of the X-ray photoelectron spectrum for oxygen atoms (XPS O 1s; Figure 7c) confirms the presence of the transition metal oxides, since its maximum is located at a characteristic region around 530 eV [48,52]. TiO 2 and MoO 3 are indistinguishable in this analysis. The XPS S 2p (Figure 7d) spectrum acquired for the TM_200 sample consists of two maxima. The more intense of these is located at a binding energy of approximately 162 eV and corresponds to the presence of MoS 2 [49]. The other local maximum, centered at a binding energy of 169.6 eV, is usually attributed to the presence of hexavalent sulfur atoms, S 6+ , as in sulfates [51]. The presence of the latter is corroborated by a notable shoulder in the XPS O 1s spectrum at a binding energy of approximately 532 eV, which can also be attributed to SO 4 2ions [51]. After calcination, both components originating from S-O interactions disappear, indicating that the elevated temperature induced the decomposition of these bonds. The results described above indicate that the surface of the TiO 2 -MoS 2 hybrid is a complex structure. The predominant compounds are titanium dioxide and molybdenum disulfide, as was also observed with the use of other analytical methods. However, the substantial oxidation of MoS 2 to MoO 3 is observed, and this is more prominent for the calcined sample. The surface of the fresh sample also contains SO 4 2ions, which are removed at an elevated temperature.

Electrochemical Performance
It has been noted in recent years that, just as graphene is obtained from graphite, layers of individual atoms can be obtained from many other crystals. Such layers have been produced for, among others, transition metal chalcogenides such as sulfides, selenides and tellurides. Molybdenum disulfide (MoS 2 ) layers have proved to be a particularly interesting material. This compound occurs in nature as molybdenite, a crystalline mineral often taking the form of characteristic hexagonal plates with a silvery color. Molybdenite, which resembles graphite and has often been confused with it, is found in rocks around the world. It has been used for many years in the production of lubricants and metal alloys. As with graphite, the properties of monatomic MoS 2 layers have long gone unnoticed.
From the point of view of applications in electronics, layered molybdenum disulfide has a significant advantage over graphene: it exhibits what is called an energy gap. The existence of this gap means that electrons cannot absorb any energy, and, by applying an electric field, the material can be switched between a state in which it conducts a current and a state in which it behaves like an insulator.
Scientific research related to the search for new material and construction solutions, enabling the further progress of lithium-ion (LIB) technology, which is considered one of the leading energy storage methods, is currently a dynamically developing scientific and research trend. TiO 2 -MoS 2 has become very popular in various applications related to the environment and energy, as evidenced by numerous scientific publications on this type of material in recent years. Several recent review articles have focused on the synthesis and application of hybrid materials based on TiO 2 [53][54][55][56][57][58][59][60][61][62] and MoS 2 [63][64][65][66][67][68][69][70][71][72][73][74].
Wang et al. [27] described the synthesis of MoS 2 -based composites quite extensively-he included broad applications for electrochemical energy storage, including LIB, sodium ion batteries (SIB) and supercapacitors. Additionally, the application of a wide range of MoS 2 and TiO 2 based materials in electro-and photocatalysis, solar cells and supercapacitors, electronic devices, sensors, bioapplications, LIB and SIB was discussed. On the other hand, Tian et al. [75] analyzed TiO 2 -based heterostructures for a wide range of applications: dye-sensitive solar cells, sensors, LIB, biomedicine, for photocatalysis, catalysis and lithium-ion cells. Moreover, titania is commonly used in solar cells, gas sensors, photonic crystals and self-cleaning coatings. Its universality results from its chemical stability, environmental friendliness and low cost. Titanium dioxide's behavior in the abovementioned applications (especially for solar cells) depends on its crystallinity, crystalline phase, surface area and morphology [76].
It is worth noting that these materials are characterized with high chemical and thermal stability. An additional advantage is their biocompatibility and relatively large surface area (associated with well-developed porosity). Their stable electrochemical window and increased cyclic efficiency is of great significance when they are applied in battery fabrication. All these features mean that systems based on titanium dioxide can be the active components of anode materials in lithium-ion batteries.
It should be mentioned that hydrothermal and solvothermal methods are suitable for the preparation of MoS 2 nanocomponents using Mo and S ions. The TiO 2 matrix shows excellent chemical stability under these conditions. Therefore, hydrothermal and solvothermal methods are most often used for the synthesis of MoS 2 on the TiO 2 surface. Figure 8 illustrates the method in which two stages are marked: nucleation and growth.
Wang et al. [27] described the synthesis of MoS2-based composites quite extensively-he included broad applications for electrochemical energy storage, including LIB, sodium ion batteries (SIB) and supercapacitors. Additionally, the application of a wide range of MoS2 and TiO2 based materials in electro-and photocatalysis, solar cells and supercapacitors, electronic devices, sensors, bioapplications, LIB and SIB was discussed. On the other hand, Tian et al. [75] analyzed TiO2-based heterostructures for a wide range of applications: dye-sensitive solar cells, sensors, LIB, biomedicine, for photocatalysis, catalysis and lithium-ion cells. Moreover, titania is commonly used in solar cells, gas sensors, photonic crystals and self-cleaning coatings. Its universality results from its chemical stability, environmental friendliness and low cost. Titanium dioxide's behavior in the abovementioned applications (especially for solar cells) depends on its crystallinity, crystalline phase, surface area and morphology [76].
It is worth noting that these materials are characterized with high chemical and thermal stability. An additional advantage is their biocompatibility and relatively large surface area (associated with well-developed porosity). Their stable electrochemical window and increased cyclic efficiency is of great significance when they are applied in battery fabrication. All these features mean that systems based on titanium dioxide can be the active components of anode materials in lithium-ion batteries.
It should be mentioned that hydrothermal and solvothermal methods are suitable for the preparation of MoS2 nanocomponents using Mo and S ions. The TiO2 matrix shows excellent chemical stability under these conditions. Therefore, hydrothermal and solvothermal methods are most often used for the synthesis of MoS2 on the TiO2 surface. Figure 8 illustrates the method in which two stages are marked: nucleation and growth. The nucleation stage is very important. TiO2 introduced in the reaction solution acts as a substrate or matrix for MoS2 nucleation, which is called heterogeneous nucleation [77]. The surface structure (crystal lattice and surface) of the TiO2 matrix has been shown to have a strong effect on the heterogeneous MoS2 nucleation on this matrix. After successful nucleation, MoS2 is present on the TiO2 matrix. This has a significant impact on the size and density of MoS2 nanoparticles, they are The nucleation stage is very important. TiO 2 introduced in the reaction solution acts as a substrate or matrix for MoS 2 nucleation, which is called heterogeneous nucleation [77]. The surface structure (crystal lattice and surface) of the TiO 2 matrix has been shown to have a strong effect on the heterogeneous MoS 2 nucleation on this matrix. After successful nucleation, MoS 2 is present on the TiO 2 matrix. This has a significant impact on the size and density of MoS 2 nanoparticles, they are easily controlled by adjusting the reaction parameters: growth time, growth temperature, initial reagent concentration, pH value and additives.
Titanium dioxide samples with a single anatase phase using 0.5 M NaNO 3 :0.5 M KNO 3 (TiO 2 -I) and 0.88 M LiNO 3 :0.12 M LiCl (TiO 2 -II) salts were fabricated by Reddy et al. [78]. The cyclic voltammetry studies for prepared materials identified characteristic cathodic and anodic redox peaks at ∼1.7 and ∼2.0 V vs. Li/Li + , in the voltage range 1.0-2.8 V, respectively. The results of the galvanostatic cycling tests for the TiO 2 -I sample showed the first discharge/charge capacity values at 244 and 198 mAh/g for at a current of 33 mA/g. On the other hand, the TiO 2 -II product was characterized with less capacity fade during cycling and delivered first discharge/charge capacity values at 340 and 253 mAh/g.
Petnikota and co-authors [79] proposed the simple solid state 'Graphenothermal Reduction' method for the synthesis of exfoliated graphene oxide (EG)/MoO 2 composites (with 46% wt. of EG). The fabricated EG/MoO 2 composite was tested as an anode material. The tested anode material was characterized with reversible capacity values of about 878 and 431 mAh/g at current densities of 100 and 1000 mA/g after 100 cycles. Moreover, the exfoliated graphene oxide (EG)/MoO 2 composite exhibited stable cycling for up to 100 cycles at 1000 mA/g with a capacity retention of~100%. Electrochemical and structural studies indicated that lithium's intercalation into the MoO 2 structure was transformed into conversion reactions. This fact had an ideal effect on increasing the capacity of the tested materials at a lower current density. Moreover, due to differences in reaction kinetics and Li diffusion coefficients, the intercalation mechanism at a higher current is favorable for the entire cycle [80].
Zhou et al. [81], for the first time, synthesized a nano-TiO 2 composite coated with MoS 2 particles by the hydrothermal method. Using Na 2 MoO 4 *2H 2 O as the Mo source and C 2 H 5 N S as the S source, they were able to make a large number of MoS 2 -TiO 2 -based composites (200 • C for 24 h). Studies on the controlled synthesis of MoS 2 -coated TiO 2 composites with various morphologies are popular [31,[81][82][83][84][85][86]. MoS 2 -TiO 2 -based composites were synthesized by adjusting controlled factors. TiO 2 surface states directly affect nucleation and growth. The hydrothermal controlled synthesis of MoS 2 -TiO 2 -based composites is determined by the surface states of TiO 2 and the reaction parameters. All this also has a significant impact on the electrochemical properties of the resulting system. The proposed reaction mechanism is shown in Figure 9. and 1000 mA/g after 100 cycles. Moreover, the exfoliated graphene oxide (EG)/MoO2 composite exhibited stable cycling for up to 100 cycles at 1000 mA/g with a capacity retention of ~100%. Electrochemical and structural studies indicated that lithium's intercalation into the MoO2 structure was transformed into conversion reactions. This fact had an ideal effect on increasing the capacity of the tested materials at a lower current density. Moreover, due to differences in reaction kinetics and Li diffusion coefficients, the intercalation mechanism at a higher current is favorable for the entire cycle [80].
Zhou et al. [81], for the first time, synthesized a nano-TiO2 composite coated with MoS2 particles by the hydrothermal method. Using Na2MoO4*2H2O as the Mo source and C2H5NS as the S source, they were able to make a large number of MoS2-TiO2-based composites (200 °C for 24 h). Studies on the controlled synthesis of MoS2-coated TiO2 composites with various morphologies are popular [31,[81][82][83][84][85][86]. MoS2-TiO2-based composites were synthesized by adjusting controlled factors. TiO2 surface states directly affect nucleation and growth. The hydrothermal controlled synthesis of MoS2-TiO2-based composites is determined by the surface states of TiO2 and the reaction parameters. All this also has a significant impact on the electrochemical properties of the resulting system. The proposed reaction mechanism is shown in Figure 9.
(1) Li-ion and electrons travel in reverse directions by diffusion in the solid and in parallel, disconnecting from the anode material; (2) the Li-ion shifts to the electrode/electrolyte boundary and passes through the electrolyte; (3) an electron driven by a higher potential from the cathode side flows through the anode particles and goes to the current collector instead of entering the electrolyte, then migrates through the external circuit to power the device; (4) the electron and lithium ion are simultaneously introduced into the cathode materials by semiconductor diffusion. (1) Li-ion and electrons travel in reverse directions by diffusion in the solid and in parallel, disconnecting from the anode material; (2) the Li-ion shifts to the electrode/electrolyte boundary and passes through the electrolyte; (3) an electron driven by a higher potential from the cathode side flows through the anode particles and goes to the current collector instead of entering the electrolyte, then migrates through the external circuit to power the device; (4) the electron and lithium ion are simultaneously introduced into the cathode materials by semiconductor diffusion.
Transition metal sulfides do not exhibit such high electronic conductivity. Thus, a high rate of electron transfer from the current collector to an electroactive material was possible thanks to the synthesis of transition metal III-IV group carbon/nitrogen (M n+1 AX n /MAX) phase materials. The various solid-state compounds applied to the fabrication of those types of materials are very often characterized with much higher electrochemical conductivity than that which is conventionally used carbonaceous materials. The abovementioned materials are very often used as surface modification agents. In the work by Ivanishcheva et al. [87], the authors proposed the using of titanium carbosilicide (Ti 3 SiC 2 ) to improve the performance of lithium transition metal phosphate cathode materials, such as Li 3 V 2 (PO 4 ) 3 /C or LiFePO 4 /C. It should be mentioned that MAX compounds do not participate in lithium ion transport, but intensify the motion of electrons within active material and thus Li-ion intercalation. Moreover, this compound is very attractive because of its function as protective layer between the electrode-electrolyte interface, which allows for a higher stability after cycling. However, the discharge capacity values for Ti 3 SiC 2 samples were still not high and equal to 95 mAh/g, 88 mAh/g after 100 cycles at current 1C for Li 3 V 2 (PO 4 ) 3 /C and LiFePO 4 /C cathode materials, respectively.
Moreover, it should be mentioned that the poor conductivity of some materials can be improved by using carbonaceous materials properly located in the intermolecular spaces such as carbon shells [88]. Ren with co-authors [88], proposed the sol-gel method assisted by hydrothermal treatment to fabricate the core-shell Li 3 V 2 (PO 4 ) 3 @C composite as a cathode material for LIBs. Electrochemical tests indicated that carbon shells incorporated onto Li 3 V 2 (PO 4 ) 3 material improved the diffusion process of lithium ions and electrical conductivity. The discharge capacity of the fabricated Li 3 V 2 (PO 4 ) 3 @C material was 125.9 mAh/g at a current density of 28 mA/g after 50 cycles. This value was two times higher than pure Li 3 V 2 (PO 4 ) 3 -68.1 mAh/g after 30 cycles at the same current density. Moreover, the retention rate of the cathode material modified by the carbon shell reached almost 98.5%. This fact is caused by the naturally high adsorptive properties and BET surface area of carbon-based materials, because they play a considerable role in their electrochemical applications.
Sample TM_200_500 (TiO 2 -MoS 2 hybrid systems hydrothermally treated at 200 • C and additionally calcined at 500 • C) was selected for electrochemical tests, because it is characterized by the best developed crystalline structure. Figure 10a displays the rate performance at various densities. At a current density of 500 mA/g, the capacity of the TiO 2 -MoS 2 hybrid is 580 mAh/g. When the current density returns to 50 mA/g, the TiO 2 -MoS 2 material still delivers a capacity of 685 mAh/g. discharge capacities in the second cycle are 622 mAh/g and 608 mAh/g, respectively, which gives a Coulombic efficiency of 98%. The loss of capacity is associated with irreversible reactions that occur during the discharge/charge processes [72,89]. High currents in both the loading and unloading process (in cycles) are used to improve the Coulombic efficiency. However, it should be remembered that high currents do not always lead to good energy efficiency. In addition, heterogeneous precipitation in the form of low solubility (sulfur in the charge cycle and sulfide/disulfide in the discharge cycle) leads to an insufficient use of active substances. Moreover, it should be noted that an insufficient current in the charging/discharging process can lead to failure or insufficient cell capacity throughout the entire process. The observed sudden decrease in the capacity of the high-voltage plateau is associated with the high reactivity of higher-order polysulfides with lithium electrodes.   Figure 10b illustrates that the reversible capacity for TiO 2 -MoS 2 material was 390 mAh/g after 100 cycles at a current density of 100 mA/g. After the second cycle, the TiO 2 -MoS 2 hybrid material showed a Coulombic efficiency of around 98%. The scanning electron microscopy images for the electrode before and after the charging/discharging process are presented in Figure 11. In the presented SEM images, many spherical particles are observed on the surface of an electrode before the charging/discharging process. Meanwhile, the MoS 2 nanostructures are difficult to determine. They are most likely related to the presence of Acetylene Black and a binder in the electrode structure. It has been observed that the initial capacity of the TiO 2 -MoS 2 hybrid is lower than that of pure MoS 2 (this is due to the presence of TiO 2 in the electrode structure). However, it should be noted that the cycle stability is superior to that of pure MoS 2 . Very often, we see a rapid decrease in the capacity of Li-S batteries. This phenomenon is explained by the high mobility of the polysulfide form in liquid electrolytes. Damage to the electrode structure by the subsequent precipitation of Li2S on the surfaces of both electrodes is associated with a loss of capacity on the low-voltage plateau [90][91][92][93][94]. Li2S is formed on the cathode by electrochemical reduction and, on the anode, Li2S is formed as a result of the chemical reduction in polysulfides that diffuse from the cathode. In addition, it is easy to observe the passivation layer in the form of a solid Li2S layer on the cathode surface. The Li2S passivation layer still remains on the carbon-cathode matrix, especially when the cell is fully charged [90]. Not only is this layer responsible for the electrode polarization, it is also responsible for the loss of capacity and high cell resistance [92,93]. In addition, the cell can be damaged by developing microcracks or cracks as a result of stress created during cyclic operation of the cell. The formation of a passivation layer on the anode side can secure the cyclical operation of lithium metal; however, the cell capacity decreases, and its resistance increases. A similar passivation layer of Li2S is formed on the anode surface as a result of the surface reaction of polysulfides with metallic lithium [92,93].
In the case of Li-S batteries with liquid electrolytes, the transfer of polysulfide in systems containing sulfur should be mentioned. This phenomenon is associated with several aspects, namely low Coulombic efficiency, high self-discharge, significant sulfur migration and rapid reduction in battery capacity. The uncontrolled process of precipitation in appropriate structures like Li2S2 or Li2S is associated with the mobility of sulfur forms, which, in turn, is caused by the transfer of polysulfide. All these properties have an influence on the charging/discharging profiles of Li-S cells. However, it should be noted that sulfur migration leads to the self-discharge of the system [93].
Electrochemical impedance spectroscopy is a very important measurement technique that provides information based on the study of electrochemical properties. The impedance frequency spectrum contains important information on the electrochemical properties of the studied system (diffusion, charge transfer, electrolyte resistance).
Slight differences were observed when adjusting the replacement circuit. It is worth noting that there are other systems that also fulfill their properties in analyzing impedance spectra. Ivanishchev with co-authors [95][96][97][98][99] give such examples when the electrode surface was calculated. In the abovementioned works, the authors examine cathode behavior in this way, e.g., Li3V2(PO4)3 [100]. The circuit they propose involves the transfer in the surface layer of the relative resin of the intercalation material and its mass. To model such a mechanism, two Warburg diffusion impedances connected in series are used, the effect of which is manifested in high and low frequencies [100]. Both these parameters allow for the determination of the diffusion coefficient of lithium ions in the Figure 11. SEM electrodes before (a) and after (b) the charging/discharging process. Figure 10c shows the voltage profiles of the TiO 2 -MoS 2 hybrid material during the first, second and 40th cycles at a current density of 100 mA/g at room temperature. According to the previous literature, it was confirmed that, during the first discharge cycle, two voltage plateaus can be observed-about 1.0 V and 0.50 V, respectively. The first voltage plateau is attributed to the Li insertion reaction (it most likely corresponds to the formation of Li x MoS 2 ). The second one-at 0.50 V-is associated with the reduction process. MoS 2 is reduced to Mo particles embedded in the LiS 2 matrix. It was observed that, for the first cycle, the discharge and charging capacities are 680 mAh/g and 610 mAh/g, respectively, which corresponds to a Coulombic efficiency of 89%. The charge and discharge capacities in the second cycle are 622 mAh/g and 608 mAh/g, respectively, which gives a Coulombic efficiency of 98%. The loss of capacity is associated with irreversible reactions that occur during the discharge/charge processes [72,89].
High currents in both the loading and unloading process (in cycles) are used to improve the Coulombic efficiency. However, it should be remembered that high currents do not always lead to good energy efficiency. In addition, heterogeneous precipitation in the form of low solubility (sulfur in the charge cycle and sulfide/disulfide in the discharge cycle) leads to an insufficient use of active substances. Moreover, it should be noted that an insufficient current in the charging/discharging process can lead to failure or insufficient cell capacity throughout the entire process. The observed sudden decrease in the capacity of the high-voltage plateau is associated with the high reactivity of higher-order polysulfides with lithium electrodes.
Very often, we see a rapid decrease in the capacity of Li-S batteries. This phenomenon is explained by the high mobility of the polysulfide form in liquid electrolytes. Damage to the electrode structure by the subsequent precipitation of Li 2 S on the surfaces of both electrodes is associated with a loss of capacity on the low-voltage plateau [90][91][92][93][94]. Li 2 S is formed on the cathode by electrochemical reduction and, on the anode, Li 2 S is formed as a result of the chemical reduction in polysulfides that diffuse from the cathode. In addition, it is easy to observe the passivation layer in the form of a solid Li 2 S layer on the cathode surface. The Li 2 S passivation layer still remains on the carbon-cathode matrix, especially when the cell is fully charged [90]. Not only is this layer responsible for the electrode polarization, it is also responsible for the loss of capacity and high cell resistance [92,93]. In addition, the cell can be damaged by developing microcracks or cracks as a result of stress created during cyclic operation of the cell. The formation of a passivation layer on the anode side can secure the cyclical operation of lithium metal; however, the cell capacity decreases, and its resistance increases. A similar passivation layer of Li 2 S is formed on the anode surface as a result of the surface reaction of polysulfides with metallic lithium [92,93].
In the case of Li-S batteries with liquid electrolytes, the transfer of polysulfide in systems containing sulfur should be mentioned. This phenomenon is associated with several aspects, namely low Coulombic efficiency, high self-discharge, significant sulfur migration and rapid reduction in battery capacity. The uncontrolled process of precipitation in appropriate structures like Li 2 S 2 or Li 2 S is associated with the mobility of sulfur forms, which, in turn, is caused by the transfer of polysulfide. All these properties have an influence on the charging/discharging profiles of Li-S cells. However, it should be noted that sulfur migration leads to the self-discharge of the system [93].
Electrochemical impedance spectroscopy is a very important measurement technique that provides information based on the study of electrochemical properties. The impedance frequency spectrum contains important information on the electrochemical properties of the studied system (diffusion, charge transfer, electrolyte resistance).
Slight differences were observed when adjusting the replacement circuit. It is worth noting that there are other systems that also fulfill their properties in analyzing impedance spectra. Ivanishchev with co-authors [95][96][97][98][99] give such examples when the electrode surface was calculated. In the abovementioned works, the authors examine cathode behavior in this way, e.g., Li 3 V 2 (PO 4 ) 3 [100]. The circuit they propose involves the transfer in the surface layer of the relative resin of the intercalation material and its mass. To model such a mechanism, two Warburg diffusion impedances connected in series are used, the effect of which is manifested in high and low frequencies [100]. Both these parameters allow for the determination of the diffusion coefficient of lithium ions in the intercalation material (this is used especially when there is a spectrum analysis after the charging/discharging process). Figure 12 shows the Electrochemical Impedance Spectroscopy (EIS) and equivalent circuit model of the tested system. R e represents the contribution of the resistance of the electrolyte, the electrode and the passivation layer between them. R ct and Constant Phase Element (CPE) are associated with charge transfer resistance, and Z w with Warburg impedance. For the TiO 2 -MoS 2 hybrid, the values of R e and R ct are 0.0151 kΩ and 0.132 kΩ, much lower than for MoS 2 (0.0023 kΩ and 0.182 kΩ). In addition, taking into account the electrode surface, the calculated and experimental Nyquist plots were illustrated. It should be noted that the results almost overlap, which indicates a good replacement circuit selection. Nyquist plots were illustrated. It should be noted that the results almost overlap, which indicates a good replacement circuit selection. Reddy et al. [101] gave an interesting interpretation of the impedance spectra. The authors, in their interpretation, matched all discharging and charging voltages to equivalent electrical circuits, slightly modified from the circuit. The following parameters were taken into account: total resistance of electrolytes and cell components (Re); resistance due to surface coating and transfer charge (Rsf+ct); Reddy et al. [101] gave an interesting interpretation of the impedance spectra. The authors, in their interpretation, matched all discharging and charging voltages to equivalent electrical circuits, slightly modified from the circuit. The following parameters were taken into account: total resistance of electrolytes and cell components (R e ); resistance due to surface coating and transfer charge (R sf+ct ); capacity due to surface layer and double layer (CPE sf + dl); bulk capacity (CPE b ); bulk resistance (R b ); Warburg impedance (W s ); intercalation capacity (C int ). It has been shown that, in most cases, the anode material showed similarity plot with only one circle in the high to medium frequency range. The authors used an identical substitute circuit for another anode material (nano-(V 1/2 Sb 1/2 Sn)O 4 ). Electrochemical impedance spectroscopy was also used to study the kinetics of the anode electrode [102].
This result further confirms that the introduction of TiO 2 can significantly improve the conductivity of the TiO 2 -MoS 2 hybrid electrode and significantly accelerate electron transport during the electrochemical lithium insertion and extraction reaction, which results in a significant improvement in electrochemical efficiency.

Conclusions
TiO 2 -MoS 2 hybrid materials were successfully synthesized utilizing a hydrothermal approach and were additionally subjected to a calcination process. Our results show that the temperature of the hydrothermal technique, as well as the use of calcination, significantly affected the morphology and crystalline and textural structure of the final hybrid products. The scanning and transmission electron microscopy images demonstrated that TiO 2 particles are uniformly distributed on MoS 2 sheets. Moreover, it was proven that additional calcination treatment leads to TiO 2 -MoS 2 hybrid materials with higher crystallinity.
The addition of TiO 2 significantly facilitates the transport of electrons and ions and controls the change in the volume of MoS 2 during the discharge process. The resulting good capacity may be due to the large surface area of the interface with the electrolyte and the shortened Li-ion insertion distance. The results suggest that the TiO 2 -MoS 2 hybrid is a promising candidate for an anode material in lithium-ion batteries.