Nonporous TiO 2 @C Microsphere with a Highly Integrated Structure for High Volumetric Lithium Storage and Enhance Initial Coulombic Efficiency

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The results revealed that the composite exhibited a highly integrated structure of TiO 2 with oxygen vacancies and carbon, along with an exceptionally small specific surface area of 11.52 m²/g. Due to its unique microstructure, the composite demonstrated remarkable lithium storage properties, including a high ICE of 75%, a notable capacity of 426.8 mAh/g after 200 cycles at 0.2 A/g, superior rate performance of 210.1 mAh/g at 5 A/g, and an outstanding cycle life, with a capacity decay rate of only 0.003% per cycle over 2000 cycles. Furthermore, electrochemical kinetic studies further validated the advantages of this microstructure. Lithium-ion batteries TiO2 Coulombic efficiency Oxygen vacancies Figures Figure 1 Figure 2 Figure 3 Figure 4 Figure 5 Figure 6 Figure 7 1. Introduction In the context of the rapid development of the global economy, the energy crisis and environmental pollution remain two significant challenges that humanity must address. The advent of rechargeable lithium-ion batteries (LIBs) appears to offer an effective solution to these issues, given their numerous advantages, including high energy density, environmental sustainability, and portability [ 1 – 5 ]. Currently, the anode of LIBs is predominantly composed of commercial graphite due to its low lithium insertion potential, abundant availability, and cost-effectiveness. However, the low lithium embedding potential of graphite can lead to the formation of lithium dendrites, which pose safety risks [ 6 – 8 ]. Consequently, it is essential to identify a safer anode material to replace graphite. Among the various anode materials for LIB, TiO 2 exhibits a high lithium embedding potential, which effectively mitigates the formation of lithium dendrites, thereby significantly enhancing the safety of LIBs [ 9 – 11 ]. Furthermore, it is favored by researchers due to its environmental friendliness, abundant availability, minimal volume expansion, and excellent cycling stability [ 12 ]. However, TiO 2 also presents certain limitations, including low specific capacity, poor electrical conductivity, and slow lithium insertion kinetics, which are inherent to its characteristics [ 13 – 15 ]. In recent years, researchers have proposed numerous strategies to address these shortcomings, including the use of nanostructures [ 16 – 18 ], the incorporation of carbon [ 19 – 21 ], and the development of specialized morphologies [ 22 , 23 ] or porous structures [ 24 ]. While these measures can significantly enhance the lithium storage capacity of TiO 2 , they also introduce certain drawbacks, such as reduced volumetric energy density and initial coulombic efficiency (ICE), which are crucial factors for the commercial viability of TiO 2 . The primary contributors to these negative effects include the large specific surface area (SSA) of TiO 2 , which diminishes its volumetric mass and exacerbates electrolyte side reactions. Previous research has demonstrated that reducing the SSA of the active material can improve its bulk mass and decrease the occurrence of electrolyte side reactions, thereby enhancing its ICE [ 25 ]. However, a low SSA in the active material can impair lithium storage performance, particularly the rate performance, due to suboptimal electrochemical kinetics. Consequently, achieving a balance between these two opposing factors to attain optimal overall performance remains a significant challenge. In this study, we employed a surface-confined in-situ inter-growth mechanism to produce TiO 2 embedded in a carbon microsphere (denoted as TiO 2 @C), which exhibits a highly complex structure comprising both TiO 2 and carbon, alongside an extremely small specific surface area (SSA) of only 11.52 m²/g. This intricate structure effectively promotes the transfer of electric charge, while the presence of oxygen vacancies enhances lithium storage sites. Additionally, the small SSA significantly mitigates the occurrence of electrolyte side effects. As a result, TiO 2 @C demonstrates an impressive initial coulombic efficiency (ICE) of 75%, a stable capacity of 426.8 mAh/g after 200 cycles at a current density of 0.2 A/g, a remarkable rate capability of 210.1 mAh/g at 5 A/g, and an outstanding cycle life, with a capacity decay rate of only 0.003% per cycle over 2000 cycles. 2. Experimental 2.1 Synthesis of materials The preparation of TiO 2 @C microspheres is achieved through a surface-confined in-situ inter-growth mechanism. The process begins with the injection of 280 µL of methanal, 200 mg of 3-aminophenol, and 1 mL of NH 3 ·H 2 O into 80 mL of ethyl alcohol, followed by stirring for 0.5 h. Subsequently, 3.4 mL of titanium tetrabutoxide (TBOT) is swiftly added to the solution and stirred for 2 h. After stirring, the resulting yellowish precursor is collected through repeated vacuum filtration and washed with ethanol, then dried at 80°C for 12 h. Finally, the precursor undergoes heat treatment in a tube furnace under an argon atmosphere, where it is heated to 500°C and held for 2 h to form the TiO 2 @C composite. For comparison, the preparation method for pure TiO 2 follows a similar procedure, with the only difference being the use of air instead of argon, while all other experimental conditions remain constant. 2.2 Material characterization The crystal structure of the sample was determined through the use of the X-ray diffraction (XRD) technique with a Rigaku D/Max−2500 instrument. A scanning electron microscope (SEM, HITACHI SU8010) was employed to observe the morphology of the samples, while transmission electron microscopy (TEM, JEM−2100F) was utilized to characterize the internal structure. The nanoscale structure of the sample underwent further investigation via a high-resolution transmission electron microscope (HRTEM, JEM−2100F). Accurate calculations of the specific surface area and pore structure of the sample were performed using the Brunauer-Emmett-Teller (BET) method with a Micrometrics ASAP2460. X-ray photoelectron spectroscopy (XPS, Thermo ESCALAB 250XI) was applied to analyze the chemical states of the elements C, Ti and O on the sample's surface. The composite's carbon content was assessed through thermal analysis (PE STA−8000). Moreover, Raman spectroscopy (DXR3 Flex) was employed to characterize the structural properties of the samples. 2.3 Electrochemical Measurements The assembly of the CR2025 battery was conducted inside a glove box filled with argon gas. To prepare the working electrode slurry, a mixture was formed by blending 80 wt% active material, 10 wt% acetylene black, and 10 wt% carboxymethyl cellulose (CMC) in deionized water, which was stirred at room temperature for 12 h. This resulting slurry was then spread onto copper foil and left to dry overnight in a vacuum oven set to 80°C. In assembling the CR2025 coin cells, lithium foil was utilized as the anode, while celgard polypropylene was employed as the separator. The selected electrolyte consisted of a 1 M solution of LiPF6, dissolved in a 1:1 volume ratio of ethylene carbonate (EC) and dimethyl carbonate (DMC). Charge-discharge cycling using a galvanostatic method and the galvanostatic intermittent titration technique (GITT) were performed within a voltage range of 0.01 to 3 V. Cyclic voltammetry (CV) analyses were implemented with a CHI 660d electrochemical workstation, at a scan rate of 0.1 mV/s across a voltage range of 0.01 to 3 V. Additionally, electrochemical impedance spectroscopy (EIS) was conducted using the same CHI 660d workstation, spanning a frequency range from 0.01 to 100,000 Hz. 3. Results and discussion The XRD spectra of the samples are presented in Fig. 1 a, where all spectral peaks of both samples align perfectly with those of standard anatase TiO 2 . Due to the low carbon ratio in TiO 2 @C, or its presence in an amorphous form, the characteristic peaks of carbon were not detected in the TiO 2 @C sample. In comparison to pure TiO 2 , TiO 2 @C exhibited lower crystallinity and broader diffraction peaks, which indicate a smaller grain size attributed to the effective suppression of carbon. Furthermore, the structural characteristics of the samples were analyzed using raman spectroscopy, as shown in Fig. 1 b. In both samples, five distinct peaks were observed near 145, 203, 395, 521, and 635 cm − 1 , corresponding to the typical raman vibration modes of TiO 2 [ 26 ]. Additionally, two faint Raman peaks at 1599 and 1348 cm − 1 in the TiO 2 @C composite material were identified as the G and D peaks of carbon [ 27 ]. Figure S1 presents the TG-DSC curve of TiO 2 @C. The TG curve demonstrates a weight loss up to 300°C, which is primarily attributed to the vaporization of surface-adsorbed water. Following this, a rapid decrease in weight is observed between 300°C and 500°C, accompanied by a significant exothermic peak at 375°C, which is attributed to the combustion and elimination of carbon. The carbon content, as determined from the TG-DSC curve, is calculated to be approximately 7.9%. The morphology of samples prepared through different processes was analyzed using SEM. Figure S2 illustrates the precursor, which displays an irregular shape characterized by several interconnected nanospheres (Figure S2a). Upon closer inspection, the precursor appears as a slightly rough spheroid with an approximate size of 500 nm (Figure S2b). Following heat treatment in various atmospheres, the overall morphology of the TiO 2 @C and TiO 2 samples remains largely unchanged compared to the precursor (Figs. 2 a, c). However, a subtle distinction in surface morphology is observed, with TiO 2 exhibiting a relatively rougher surface due to the combustion of carbon during the precursor's heat treatment in an air atmosphere (Figs. 2 b, d). This combustion effectively promotes the further growth of TiO 2 grains, providing visual evidence for the inhibitory role of carbon in TiO 2 grain growth. TEM was employed to investigate the internal structure of the TiO 2 @C composite material. As shown in Fig. 2 e, the TiO 2 @C nanospheres possess a compact solid internal structure, indicating that the TiO 2 @C composite has a low specific surface area (SSA). Figure 2 f presents HRTEM image of the TiO 2 @C, revealing clear lattice fringes corresponding to the anatase TiO 2 (101) crystal plane. Notably, amorphous carbon (shown as a white curved region) closely envelops the TiO 2 without discernible boundaries, suggesting a potential co-existence process during the formation of the TiO 2 @C precursor. This co-existence process facilitates the persistent polymerization of 3-aminophenol and methanal around TiO 2 , with the resulting polymer effectively preventing the aggregation of primary TiO 2 grains. The electron diffraction pattern depicted in Fig. 2 g indicates that TiO 2 within the TiO 2 @C sample exists in a polycrystalline state. Additionally, Fig. 2 h displays the elemental distribution mapping for TiO 2 @C, revealing a uniform distribution of C, Ti and O elements within the composite. Figure 3 illustrates the SSA and pore size of both samples. As shown in Fig. 3 a, there is no discernible hysteresis loop in the nitrogen adsorption/desorption curves for either sample at relative pressures (P/P 0 ) of 0.5 and 1.0, indicating that the SSA of TiO 2 @C and TiO 2 is quite small. The SSA values for TiO 2 @C and TiO 2 were determined to be 10.41 and 9.84 m² g⁻¹, respectively. Furthermore, Fig. 3 b indicates that the pore sizes of TiO 2 @C and TiO 2 are predominantly concentrated at 4.8 and 4.3 nm, respectively. The observed difference in pore sizes can be attributed to the inhibition of TiO 2 grain growth by carbon during the heat treatment of the TiO 2 @C composite in an argon atmosphere. Such small SSA not only contribute to an increase in the tap density of the anode electrode material, thereby enhancing its volumetric energy density, but also significantly reduce the contact area between the active material and electrolyte. This reduction leads to a decrease in side reactions and an improvement in the ICE of the TiO 2 @C electrode. Figure 4 a presents the XPS full spectrum of both samples, indicating the presence of C, Ti and O elements on the surface of TiO 2 @C. Figure 4 b illustrates the high-resolution XPS (HR-XPS) spectra of the Ti 2p for both TiO 2 @C and TiO 2 . The Ti 2p HR-XPS spectra of the TiO 2 sample reveal a pair of peaks located at 463.9 and 458.2 eV, corresponding to the binding energies of 2p 1/2 and 2p 3/2 of Ti 4+ [ 28 ]. In contrast, the Ti 2p HR-XPS spectra of the TiO 2 @C sample exhibit two pairs of peaks: a prominent pair at 464.8 and 458.9 eV, which correspond to 2p 1/2 and 2p 3/2 of Ti 4+ , and another pair at 463.8 and 458.2 eV, attributed to 2p 1/2 and 2p 3/2 of Ti 3+ [ 29 ]. Notably, the binding energy of Ti 4 + in the TiO 2 @C sample is higher, which can be ascribed to the presence of Ti 3+ . Figure 4 c displays the O 1s HR-XPS spectrum of the TiO 2 @C sample, where three peaks can be fitted at 531.9, 530.2 and 529.9 eV, corresponding to the oxygen vacancy (O-Ti 3+ ), O-C, and O-Ti 4 + bonds, respectively [ 30 ]. The formation of O-Ti 3 + in the TiO 2 @C may result from insufficient oxygen during heat treatment in an argon atmosphere. Previous studies have confirmed that the presence of O-Ti 3 + not only enhances the intrinsic conductivity of TiO 2 but also increases the active sites for lithium storage in TiO 2 @C composite materials [ 31 ]. Figure 4 d illustrates the HR-XPS of C 1s in TiO 2 @C, where the two fitted peaks at 284.8 and 283.4 eV correspond to the binding energies of C-C/C = C and C-O bonds, respectively [ 32 ]. Through the analysis of the aforementioned test results, this paper proposes a surface-confined in-situ inter-growth mechanism for the formation of TiO 2 @C, as illustrated in Fig. 5 . The experimental synthesis process described herein involves only three reactants: TBOT, methanal, and 3-aminophenol. Initially (Step I), due to the high concentration of NH 3 ·H 2 O, TBOT rapidly hydrolyzes to form primary TiO 2 grains, while NH 4 + accumulate on its surface. Concurrently, methanal and 3-aminophenol undergo rapid polymerization to generate 3-aminophenol-methanal (3-APM) oligomers in the presence of NH 4+ , which subsequently accumulate around the primary TiO 2 grains, resulting in the formation of high-density TiO 2 @3-APM microspheres. Subsequently (Step II), following thermal treatment under an argon atmosphere, TiO 2 @3-APM is transformed into TiO 2 @C with oxygen vacancies due to the absence of an oxygen source. In the preparation of nano-TiO 2 , NH 3 ·H 2 O solution is typically excluded because of its propensity to induce rapid hydrolysis of the titanium source, leading to significant particle aggregation of TiO 2 . In contrast, the synthesis method presented in this paper strategically leverages the rapid hydrolysis properties of the titanium source, facilitating the formation of a micro-environment on the TiO 2 surface that triggers the polymerization of 3-aminophenol with methanal. The advantages of this approach are as follows: The technical route is straightforward, time-efficient, and does not require precise control, thereby enhancing its feasibility for commercial preparation; The micro-environment created around the primary TiO 2 promotes a close association between TiO 2 and 3-APM oligomers, which is essential for the subsequent thermal treatment aimed at achieving a highly integrated carbon and TiO 2 structure. The electrochemical behavior of TiO 2 @C electrode was investigated using CV, with the result presented in in Fig. 6 a. During the initial discharge process, the CV curve reveals a broad reduction peak between 1.75 and 1 V, indicative of the initial Li + insertion into TiO 2 @C and the formation of the solid electrolyte interphase (SEI) [ 33 ]. Subsequently, during the charging process, the Li + extraction potential is observed to be approximately 2.2 V. In the subsequent cycles, the CV curves demonstrate a notable overlap, with the Li + insertion potential shifting towards a higher value. This observation suggests that the TiO 2 @C electrode has undergone a degree of activation, exhibiting excellent electrochemical reversibility and structural stability. The discharge/charge curves for both electrodes during the first three cycles at a current density of 0.2 A/g are presented in Fig. 6 b and Figure S3. The initial discharge specific capacities of the TiO 2 @C and TiO 2 electrodes are 584.4 and 368.2 mAh/g, respectively. Correspondingly, the initial charge specific capacities are 438.3 mAh/g for TiO 2 @C and 272.4 mAh/g for TiO 2 . The ICE for TiO 2 @C and TiO 2 electrodes are 75% and 74%, respectively, surpassing those reported in previous studies (Fig. 6 c) [ 16 , 20 , 23 , 34 – 36 ]. These results demonstrate that the experimental approach employed in this study effectively enhances the ICE of the electrode by minimizing their SSA. The discharge/charge curves of both the TiO 2 @C and TiO 2 electrodes over the subsequent two cycles exhibit a significant degree of overlap, indicating the high reversibility of these electrode materials during the Li + insertion and extraction processes. Furthermore, the reversible specific capacity of the TiO 2 @C electrode is approximately 1.6 times greater than that of the TiO 2 electrode. This enhancement can be attributed to the intimate connection between TiO 2 and carbon within the TiO 2 @C composite, which facilitates the full participation of the TiO 2 active material. Additionally, the presence of oxygen vacancies provides extra Li + storage active sites. Figures 6 (d, e) illustrate the cyclic and rate performance of both electrodes. As depicted in Fig. 6 d, both electrodes demonstrate remarkable cyclic stability, with only a slight decrease in reversible specific capacity during the initial cycles. The reversible specific capacities recorded during the second cycle for the TiO 2 @C and TiO 2 electrodes are 466.4 and 287.5 mAh/g, respectively. After 200 cycles, the reversible specific capacities are maintained at 426.8 and 275.9 mAh/g, respectively. The capacity retention rates for the TiO 2 @C and TiO 2 electrodes, relative to their second cycle capacities, are 91.5% and 95.6%, respectively. Notably, the TiO 2 electrode exhibits a superior capacity retention rate compared to the TiO 2 @C electrode, which may be attributed to the TiO 2 electrode undergoing stronger activation during repeated charge and discharge cycles, thereby enabling more TiO 2 active sites to participate in Li + . As the current density increases, the reversible specific capacities of both the TiO 2 @C and TiO 2 electrodes exhibit a gradual decline, as illustrated in Fig. 6 e. The average reversible specific capacities of the TiO 2 @C electrode at current densities of 0.1, 0.2, 0.5, 1.0, 2.0, and 5.0 A/g are 512.9, 468.2, 417.4, 350.9, 299.1, and 210.1 mAh/g, respectively, which surpass those reported in previous studies (Fig. 6 f) [ 20 , 37 – 42 ]. Upon returning the current density to 0.1 A/g, the average reversible specific capacity is recorded at 511.8 mAh/g, indicating remarkable cycling reversibility. In contrast, the reversible capacity of TiO 2 is only 124.3 mAh/g at a current density of 5.0 A/g, which is significantly lower than that of TiO 2 @C. This disparity suggests that the incorporation of carbon and the presence of oxygen vacancies considerably enhance the electrochemical kinetics of TiO 2 @C. The long-term cycling stability of the TiO 2 @C electrode, as demonstrated in Fig. 6 g, confirms that it possesses an extended cycling life and stable coulombic efficiency. After 2000 cycles, the reversible specific capacity decreases from an initial value of 216.8 mAh/g to 203.8 mAh/g, resulting in an impressive capacity retention rate of 94%. This translates to a capacity decay rate of only 0.003% per cycle, indicating that the TiO 2 @C composite maintains exceptional structural integrity. The electrochemical kinetics of TiO 2 @C and TiO 2 electrodes were investigated using EIS and GITT, with the results presented in Fig. 7 . The EIS data indicate that the TiO 2 @C electrode exhibits reduced charge transfer resistance (Rct), as shown in Fig. 7 a. Figure 7 b illustrates the GITT curves for both electrodes. The diffusion rates of Li + during the charge and discharge processes were calculated using the following equation: [ 30 ]. The diffusion rates of Li + , depicted in Figs. 7 c and 7 d, indicate that the TiO 2 @C electrode achieves a diffusion rate ranging from approximately 10 − 9 to 10 − 10 cm² s − 1 , which is significantly higher than that of the TiO 2 electrode. By integrating the findings from the EIS and GITT tests, it can be concluded that the optimal composite structure of TiO 2 with carbon, coupled with the presence of oxygen vacancies, collectively enhances the electrochemical kinetics of the TiO 2 @C electrode, thereby resulting in superior electrochemical performance. 4. Conclusions Nonporous TiO 2 @C microspheres with a highly integrated structure were synthesized using a surface-confined in-situ inter-growth strategy. When employed as an anode electrode for LIB, these microspheres exhibit a high volumetric energy density and improved ICE. The enhanced ICE is attributed to the extremely small SSA of the TiO 2 @C microspheres, which minimizes contact between the active material and the electrolyte, thereby reducing the occurrence of side reactions. Results from electrochemical kinetics studies strongly indicate that the synergistic interaction between the highly integrated structure and oxygen vacancies contributes to effective Li + storage. Furthermore, our synthesis method is not only efficient but also presents a novel approach for the development of other electrode materials. Declarations Data availability The authors declare that all data generated or analysed during this study are included in this published article. Acknowledgements This research is financially supported by the China Postdoctoral Science Foundation (Grant No. 2023M732858), the Shandong Provincial Natural Science Foundation (Grant No. ZR2022QE290) and the development plan for Weifang city (Grant No. 2023GX061). Supporting Information The Supporting Information is available free of charge at: Author contributions Jinpeng Yin, Guanqin Wang, Dongqing Kong, Chuang Li, Qiang Zhang, Dongbai Xie, Yangyang Yan, Ning Li, Qiang Li wrote the main manuscript text and prepared all figures. All authors reviewed the manuscript. References Wang, C., Yang, C. & Zheng, Z. Toward practical high‐energy and high‐power lithium battery anodes: present and future. Adv. Sci. 9, 2105213 (2022). Li, J. et al. Revolutionizing lithium storage capabilities in TiO 2 by expanding the redox range. ACS Nano 17, 21604-21613 (2023). Zhang, Y. et al. Polydopamine sacrificial layer mediated SiO x /C@ C yolk@ shell structure for durable lithium storage. Mater. Chem. Front. 4, 1656-1663 (2020). Lee, J. et al. Everlasting living and breathing gyroid 3D network in Si@ SiO x /C nanoarchitecture for lithium ion battery. ACS Nano 13, 9607-9619 (2019). Zhao, C. et al. 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Supplementary Files Supplementary.pdf Cite Share Download PDF Status: Published Journal Publication published 28 Dec, 2024 Read the published version in Scientific Reports → Version 1 posted Editorial decision: Revision requested 24 Sep, 2024 Reviews received at journal 20 Sep, 2024 Reviews received at journal 19 Sep, 2024 Reviews received at journal 09 Sep, 2024 Reviewers agreed at journal 28 Aug, 2024 Reviewers agreed at journal 28 Aug, 2024 Reviewers agreed at journal 28 Aug, 2024 Reviewers invited by journal 28 Aug, 2024 Editor assigned by journal 28 Aug, 2024 Editor invited by journal 27 Aug, 2024 Submission checks completed at journal 27 Aug, 2024 First submitted to journal 16 Aug, 2024 You are reading this latest preprint version Research Square lets you share your work early, gain feedback from the community, and start making changes to your manuscript prior to peer review in a journal. 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Also discoverable on Platform About Our Team In Review Editorial Policies Advisory Board Help Center Resources Author Services Accessibility API Access RSS feed Manage Cookie Preferences © Research Square 2026 | ISSN 2693-5015 (online) Privacy Policy Terms of Service Do Not Sell My Personal Information {"props":{"pageProps":{"initialData":{"identity":"rs-4923096","acceptedTermsAndConditions":true,"allowDirectSubmit":false,"archivedVersions":[],"articleType":"Article","associatedPublications":[],"authors":[{"id":358300806,"identity":"d6aa1aca-c174-4a45-bbee-b35ef8a36075","order_by":0,"name":"Jinpeng Yin","email":"data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAZAAAAAyAQMAAABI0h/eAAAABlBMVEX///8AAABVwtN+AAAACXBIWXMAAA7EAAAOxAGVKw4bAAAA/UlEQVRIiWNgGAWjYDACZgYGgwQI6wBDBUTMgFgtbAkMZxgYJAhrQQAeA+K0GBznPVDwcMcdOXP+Nd8kDrbV1TGwN2+TYKi5g1vLYb4Eg8Qzz4wtZ7zdBtRyWIKB51iZBMOxZ3i08BgYJLYdTtxw4+y22x/bDkgwSOSYSTA2HCaopX7DjTPPbgAdJsEg/4Y4LQkG53vYgFqYgbbw4NciCdHyzHDDDTbzHwfOHZZs40krtkg4hlsL3/kzZoY/2+7IG5w//NjgQFkdPz/74Y03PtTg1qJwgIENGA0HgBGSABFhAxEJODUwMMg3MDA/AGvhP4BH2SgYBaNgFIxoAACWZ1zLTPCfwgAAAABJRU5ErkJggg==","orcid":"","institution":"Weifang University of Science and Technology","correspondingAuthor":true,"prefix":"","firstName":"Jinpeng","middleName":"","lastName":"Yin","suffix":""},{"id":358300807,"identity":"0acf4c9e-425d-4de4-a7b8-20b8ffb96197","order_by":1,"name":"Guanqin Wang","email":"","orcid":"","institution":"Weifang University of Science and Technology","correspondingAuthor":false,"prefix":"","firstName":"Guanqin","middleName":"","lastName":"Wang","suffix":""},{"id":358300810,"identity":"1eafe50b-946c-4851-9267-e6d19071fbf8","order_by":2,"name":"Dongqing Kong","email":"","orcid":"","institution":"Weifang University of Science and Technology","correspondingAuthor":false,"prefix":"","firstName":"Dongqing","middleName":"","lastName":"Kong","suffix":""},{"id":358300814,"identity":"cde240c0-3c4d-4ce3-b7b2-9274bcaeaa66","order_by":3,"name":"Chuang Li","email":"","orcid":"","institution":"Weifang University of Science and Technology","correspondingAuthor":false,"prefix":"","firstName":"Chuang","middleName":"","lastName":"Li","suffix":""},{"id":358300816,"identity":"0af31659-171e-4afe-bce1-bf217052323f","order_by":4,"name":"Qiang Zhang","email":"","orcid":"","institution":"Weifang University of Science and Technology","correspondingAuthor":false,"prefix":"","firstName":"Qiang","middleName":"","lastName":"Zhang","suffix":""},{"id":358300822,"identity":"90de9da6-5c6a-44c4-993d-ad2da138602e","order_by":5,"name":"Dongbai Xie","email":"","orcid":"","institution":"Weifang University of Science and Technology","correspondingAuthor":false,"prefix":"","firstName":"Dongbai","middleName":"","lastName":"Xie","suffix":""},{"id":358300824,"identity":"e5035a26-2581-424a-9122-3c4826e19b63","order_by":6,"name":"Yangyang Yan","email":"","orcid":"","institution":"Weifang University of Science and Technology","correspondingAuthor":false,"prefix":"","firstName":"Yangyang","middleName":"","lastName":"Yan","suffix":""},{"id":358300825,"identity":"e6fc2de3-20c0-406e-a30b-6afa68d9ced0","order_by":7,"name":"Ning Li","email":"","orcid":"","institution":"Weifang University of Science and Technology","correspondingAuthor":false,"prefix":"","firstName":"Ning","middleName":"","lastName":"Li","suffix":""},{"id":358300826,"identity":"562f30f5-8fe9-4247-99f8-cea67f23995b","order_by":8,"name":"Qiang Li","email":"","orcid":"","institution":"Weifang University of Science and Technology","correspondingAuthor":false,"prefix":"","firstName":"Qiang","middleName":"","lastName":"Li","suffix":""}],"badges":[],"createdAt":"2024-08-16 07:10:17","currentVersionCode":1,"declarations":"","doi":"10.21203/rs.3.rs-4923096/v1","doiUrl":"https://doi.org/10.21203/rs.3.rs-4923096/v1","draftVersion":[],"editorialEvents":[{"content":"https://doi.org/10.1038/s41598-024-82179-z","type":"published","date":"2024-12-28T15:57:30+00:00"}],"editorialNote":"","failedWorkflow":false,"files":[{"id":65262419,"identity":"3bf6a764-b070-4e58-8dec-614ea8d9bd52","added_by":"auto","created_at":"2024-09-25 11:11:47","extension":"png","order_by":1,"title":"Figure 1","display":"","copyAsset":false,"role":"figure","size":513168,"visible":true,"origin":"","legend":"\u003cp\u003eXRD patterns (a) and Raman spectra (b) of TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e.\u003c/p\u003e","description":"","filename":"floatimage1.png","url":"https://assets-eu.researchsquare.com/files/rs-4923096/v1/8a87234be22d1aa2f4bec41e.png"},{"id":65261761,"identity":"ab196590-62f5-4384-b908-4b1b0c8bb48f","added_by":"auto","created_at":"2024-09-25 11:03:47","extension":"png","order_by":2,"title":"Figure 2","display":"","copyAsset":false,"role":"figure","size":395743,"visible":true,"origin":"","legend":"\u003cp\u003eSEM images of the TiO\u003csub\u003e2 \u003c/sub\u003e(a, b)\u003cstrong\u003e \u003c/strong\u003eand TiO\u003csub\u003e2\u003c/sub\u003e@C (c, d), TEM and HRTEM images of the TiO\u003csub\u003e2\u003c/sub\u003e@C (e, f), SAED pattern of TiO\u003csub\u003e2\u003c/sub\u003e@C (g), EDX mapping images of TiO\u003csub\u003e2\u003c/sub\u003e@C (h).\u003c/p\u003e","description":"","filename":"floatimage2.png","url":"https://assets-eu.researchsquare.com/files/rs-4923096/v1/a501daf17d3d7809ebd70ba3.png"},{"id":65261766,"identity":"4eaf07fe-edc8-48c9-93b3-8a3d9ff886bd","added_by":"auto","created_at":"2024-09-25 11:03:47","extension":"png","order_by":3,"title":"Figure 3","display":"","copyAsset":false,"role":"figure","size":156614,"visible":true,"origin":"","legend":"\u003cp\u003eN\u003csub\u003e2\u003c/sub\u003e adsorption/desorption isotherms (a) and pore size distribution (b) of TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e\u003c/p\u003e","description":"","filename":"floatimage3.png","url":"https://assets-eu.researchsquare.com/files/rs-4923096/v1/b4a9b412009ee7aef8aba378.png"},{"id":65261765,"identity":"a99fcefe-4081-461e-9565-bf8ef6488019","added_by":"auto","created_at":"2024-09-25 11:03:47","extension":"png","order_by":4,"title":"Figure 4","display":"","copyAsset":false,"role":"figure","size":347215,"visible":true,"origin":"","legend":"\u003cp\u003eThe whole XPS spectra (a) and Ti2p spectrum (b) of TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e, O1s spectrum (c) and C1s spectrum (d) in the TiO\u003csub\u003e2\u003c/sub\u003e@C.\u0026nbsp;\u003c/p\u003e","description":"","filename":"floatimage4.png","url":"https://assets-eu.researchsquare.com/files/rs-4923096/v1/ad35fecdf8765908cbced839.png"},{"id":65262416,"identity":"c21efb4a-95aa-4648-8ea5-68895cdbc50e","added_by":"auto","created_at":"2024-09-25 11:11:47","extension":"png","order_by":5,"title":"Figure 5","display":"","copyAsset":false,"role":"figure","size":161334,"visible":true,"origin":"","legend":"\u003cp\u003eSchematic of the formation process of TiO\u003csub\u003e2\u003c/sub\u003e@C.\u003c/p\u003e","description":"","filename":"floatimage5.png","url":"https://assets-eu.researchsquare.com/files/rs-4923096/v1/0b75dfa4a1a592a1771b6e22.png"},{"id":65262632,"identity":"c7f2cd2a-59e0-4354-91bb-1d4871f64fb0","added_by":"auto","created_at":"2024-09-25 11:19:47","extension":"png","order_by":6,"title":"Figure 6","display":"","copyAsset":false,"role":"figure","size":444486,"visible":true,"origin":"","legend":"\u003cp\u003e(a)\u003cstrong\u003e \u003c/strong\u003eCV curves of the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode at a scan rate of 0.1 mV s\u003csup\u003e-1 \u003c/sup\u003e(b) Discharge/charge curves of the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode at 0.2 A/g, (c) The initial coulombic efficiency comparison between the TiO\u003csub\u003e2\u003c/sub\u003e@C in this paper and other TiO\u003csub\u003e2\u003c/sub\u003e-based electrode (d) Cycling performance of TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes at 0.2 A/g, (e) Rate performance of TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes at different current densities,\u003cstrong\u003e \u003c/strong\u003e(f) Comparison of rate performance of TiO\u003csub\u003e2\u003c/sub\u003e@C in this paper with recently reported works on TiO\u003csub\u003e2\u003c/sub\u003e-based electrode for LIBs, (g) The long-term cycling performance of the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode at a current density of 5 A/g.\u003c/p\u003e","description":"","filename":"floatimage6.png","url":"https://assets-eu.researchsquare.com/files/rs-4923096/v1/0ade7e3e7bc42954bbcb354b.png"},{"id":65261762,"identity":"32320108-abcb-438e-91b9-801122283ef0","added_by":"auto","created_at":"2024-09-25 11:03:47","extension":"png","order_by":7,"title":"Figure 7","display":"","copyAsset":false,"role":"figure","size":359633,"visible":true,"origin":"","legend":"\u003cp\u003e(a) EIS curves of TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes after 10 cycles (b) GITT curves and (c, d) the calculated Li-ion diffusion coefficient of the of TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes.\u003c/p\u003e","description":"","filename":"floatimage7.png","url":"https://assets-eu.researchsquare.com/files/rs-4923096/v1/7f10f4f8292a6a70ebfe1f3e.png"},{"id":72641410,"identity":"f28fab48-1828-4a3b-87d0-a5c71ccb84ca","added_by":"auto","created_at":"2024-12-30 16:11:30","extension":"pdf","order_by":0,"title":"","display":"","copyAsset":false,"role":"manuscript-pdf","size":2927987,"visible":true,"origin":"","legend":"","description":"","filename":"manuscript.pdf","url":"https://assets-eu.researchsquare.com/files/rs-4923096/v1/eca7cc25-9c63-4c47-917b-9a1e171c3587.pdf"},{"id":65262631,"identity":"58fac29b-190f-4d44-8bd1-228d6ba44537","added_by":"auto","created_at":"2024-09-25 11:19:47","extension":"pdf","order_by":2,"title":"","display":"","copyAsset":false,"role":"supplement","size":549419,"visible":true,"origin":"","legend":"","description":"","filename":"Supplementary.pdf","url":"https://assets-eu.researchsquare.com/files/rs-4923096/v1/3fed0c6a35bae865566b959b.pdf"}],"financialInterests":"No competing interests reported.","formattedTitle":"Nonporous TiO 2 @C Microsphere with a Highly Integrated Structure for High Volumetric Lithium Storage and Enhance Initial Coulombic Efficiency","fulltext":[{"header":"1. Introduction","content":"\u003cp\u003eIn the context of the rapid development of the global economy, the energy crisis and environmental pollution remain two significant challenges that humanity must address. The advent of rechargeable lithium-ion batteries (LIBs) appears to offer an effective solution to these issues, given their numerous advantages, including high energy density, environmental sustainability, and portability [\u003cspan additionalcitationids=\"CR2 CR3 CR4\" citationid=\"CR1\" class=\"CitationRef\"\u003e1\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR5\" class=\"CitationRef\"\u003e5\u003c/span\u003e]. Currently, the anode of LIBs is predominantly composed of commercial graphite due to its low lithium insertion potential, abundant availability, and cost-effectiveness. However, the low lithium embedding potential of graphite can lead to the formation of lithium dendrites, which pose safety risks [\u003cspan additionalcitationids=\"CR7\" citationid=\"CR6\" class=\"CitationRef\"\u003e6\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR8\" class=\"CitationRef\"\u003e8\u003c/span\u003e]. Consequently, it is essential to identify a safer anode material to replace graphite.\u003c/p\u003e \u003cp\u003eAmong the various anode materials for LIB, TiO\u003csub\u003e2\u003c/sub\u003e exhibits a high lithium embedding potential, which effectively mitigates the formation of lithium dendrites, thereby significantly enhancing the safety of LIBs [\u003cspan additionalcitationids=\"CR10\" citationid=\"CR9\" class=\"CitationRef\"\u003e9\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR11\" class=\"CitationRef\"\u003e11\u003c/span\u003e]. Furthermore, it is favored by researchers due to its environmental friendliness, abundant availability, minimal volume expansion, and excellent cycling stability [\u003cspan citationid=\"CR12\" class=\"CitationRef\"\u003e12\u003c/span\u003e]. However, TiO\u003csub\u003e2\u003c/sub\u003e also presents certain limitations, including low specific capacity, poor electrical conductivity, and slow lithium insertion kinetics, which are inherent to its characteristics [\u003cspan additionalcitationids=\"CR14\" citationid=\"CR13\" class=\"CitationRef\"\u003e13\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR15\" class=\"CitationRef\"\u003e15\u003c/span\u003e]. In recent years, researchers have proposed numerous strategies to address these shortcomings, including the use of nanostructures [\u003cspan additionalcitationids=\"CR17\" citationid=\"CR16\" class=\"CitationRef\"\u003e16\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR18\" class=\"CitationRef\"\u003e18\u003c/span\u003e], the incorporation of carbon [\u003cspan additionalcitationids=\"CR20\" citationid=\"CR19\" class=\"CitationRef\"\u003e19\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR21\" class=\"CitationRef\"\u003e21\u003c/span\u003e], and the development of specialized morphologies [\u003cspan citationid=\"CR22\" class=\"CitationRef\"\u003e22\u003c/span\u003e, \u003cspan citationid=\"CR23\" class=\"CitationRef\"\u003e23\u003c/span\u003e] or porous structures [\u003cspan citationid=\"CR24\" class=\"CitationRef\"\u003e24\u003c/span\u003e]. While these measures can significantly enhance the lithium storage capacity of TiO\u003csub\u003e2\u003c/sub\u003e, they also introduce certain drawbacks, such as reduced volumetric energy density and initial coulombic efficiency (ICE), which are crucial factors for the commercial viability of TiO\u003csub\u003e2\u003c/sub\u003e. The primary contributors to these negative effects include the large specific surface area (SSA) of TiO\u003csub\u003e2\u003c/sub\u003e, which diminishes its volumetric mass and exacerbates electrolyte side reactions. Previous research has demonstrated that reducing the SSA of the active material can improve its bulk mass and decrease the occurrence of electrolyte side reactions, thereby enhancing its ICE [\u003cspan citationid=\"CR25\" class=\"CitationRef\"\u003e25\u003c/span\u003e]. However, a low SSA in the active material can impair lithium storage performance, particularly the rate performance, due to suboptimal electrochemical kinetics. Consequently, achieving a balance between these two opposing factors to attain optimal overall performance remains a significant challenge.\u003c/p\u003e \u003cp\u003eIn this study, we employed a surface-confined in-situ inter-growth mechanism to produce TiO\u003csub\u003e2\u003c/sub\u003e embedded in a carbon microsphere (denoted as TiO\u003csub\u003e2\u003c/sub\u003e@C), which exhibits a highly complex structure comprising both TiO\u003csub\u003e2\u003c/sub\u003e and carbon, alongside an extremely small specific surface area (SSA) of only 11.52 m\u0026sup2;/g. This intricate structure effectively promotes the transfer of electric charge, while the presence of oxygen vacancies enhances lithium storage sites. Additionally, the small SSA significantly mitigates the occurrence of electrolyte side effects. As a result, TiO\u003csub\u003e2\u003c/sub\u003e@C demonstrates an impressive initial coulombic efficiency (ICE) of 75%, a stable capacity of 426.8 mAh/g after 200 cycles at a current density of 0.2 A/g, a remarkable rate capability of 210.1 mAh/g at 5 A/g, and an outstanding cycle life, with a capacity decay rate of only 0.003% per cycle over 2000 cycles.\u003c/p\u003e"},{"header":"2. Experimental","content":"\u003cdiv id=\"Sec3\" class=\"Section2\"\u003e \u003ch2\u003e2.1 Synthesis of materials\u003c/h2\u003e \u003cp\u003eThe preparation of TiO\u003csub\u003e2\u003c/sub\u003e@C microspheres is achieved through a surface-confined in-situ inter-growth mechanism. The process begins with the injection of 280 \u0026micro;L of methanal, 200 mg of 3-aminophenol, and 1 mL of NH\u003csub\u003e3\u003c/sub\u003e\u0026middot;H\u003csub\u003e2\u003c/sub\u003eO into 80 mL of ethyl alcohol, followed by stirring for 0.5 h. Subsequently, 3.4 mL of titanium tetrabutoxide (TBOT) is swiftly added to the solution and stirred for 2 h. After stirring, the resulting yellowish precursor is collected through repeated vacuum filtration and washed with ethanol, then dried at 80\u0026deg;C for 12 h. Finally, the precursor undergoes heat treatment in a tube furnace under an argon atmosphere, where it is heated to 500\u0026deg;C and held for 2 h to form the TiO\u003csub\u003e2\u003c/sub\u003e@C composite. For comparison, the preparation method for pure TiO\u003csub\u003e2\u003c/sub\u003e follows a similar procedure, with the only difference being the use of air instead of argon, while all other experimental conditions remain constant.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec4\" class=\"Section2\"\u003e \u003ch2\u003e2.2 Material characterization\u003c/h2\u003e \u003cp\u003eThe crystal structure of the sample was determined through the use of the X-ray diffraction (XRD) technique with a Rigaku D/Max\u0026minus;2500 instrument. A scanning electron microscope (SEM, HITACHI SU8010) was employed to observe the morphology of the samples, while transmission electron microscopy (TEM, JEM\u0026minus;2100F) was utilized to characterize the internal structure. The nanoscale structure of the sample underwent further investigation via a high-resolution transmission electron microscope (HRTEM, JEM\u0026minus;2100F). Accurate calculations of the specific surface area and pore structure of the sample were performed using the Brunauer-Emmett-Teller (BET) method with a Micrometrics ASAP2460. X-ray photoelectron spectroscopy (XPS, Thermo ESCALAB 250XI) was applied to analyze the chemical states of the elements C, Ti and O on the sample's surface. The composite's carbon content was assessed through thermal analysis (PE STA\u0026minus;8000). Moreover, Raman spectroscopy (DXR3 Flex) was employed to characterize the structural properties of the samples.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec5\" class=\"Section2\"\u003e \u003ch2\u003e2.3 Electrochemical Measurements\u003c/h2\u003e \u003cp\u003eThe assembly of the CR2025 battery was conducted inside a glove box filled with argon gas. To prepare the working electrode slurry, a mixture was formed by blending 80 wt% active material, 10 wt% acetylene black, and 10 wt% carboxymethyl cellulose (CMC) in deionized water, which was stirred at room temperature for 12 h. This resulting slurry was then spread onto copper foil and left to dry overnight in a vacuum oven set to 80\u0026deg;C. In assembling the CR2025 coin cells, lithium foil was utilized as the anode, while celgard polypropylene was employed as the separator. The selected electrolyte consisted of a 1 M solution of LiPF6, dissolved in a 1:1 volume ratio of ethylene carbonate (EC) and dimethyl carbonate (DMC). Charge-discharge cycling using a galvanostatic method and the galvanostatic intermittent titration technique (GITT) were performed within a voltage range of 0.01 to 3 V. Cyclic voltammetry (CV) analyses were implemented with a CHI 660d electrochemical workstation, at a scan rate of 0.1 mV/s across a voltage range of 0.01 to 3 V. Additionally, electrochemical impedance spectroscopy (EIS) was conducted using the same CHI 660d workstation, spanning a frequency range from 0.01 to 100,000 Hz.\u003c/p\u003e \u003c/div\u003e"},{"header":"3. Results and discussion","content":"\u003cp\u003eThe XRD spectra of the samples are presented in Fig.\u0026nbsp;\u003cspan\u003e1\u003c/span\u003ea, where all spectral peaks of both samples align perfectly with those of standard anatase TiO\u003csub\u003e2\u003c/sub\u003e. Due to the low carbon ratio in TiO\u003csub\u003e2\u003c/sub\u003e@C, or its presence in an amorphous form, the characteristic peaks of carbon were not detected in the TiO\u003csub\u003e2\u003c/sub\u003e@C sample. In comparison to pure TiO\u003csub\u003e2\u003c/sub\u003e, TiO\u003csub\u003e2\u003c/sub\u003e@C exhibited lower crystallinity and broader diffraction peaks, which indicate a smaller grain size attributed to the effective suppression of carbon. Furthermore, the structural characteristics of the samples were analyzed using raman spectroscopy, as shown in Fig.\u0026nbsp;\u003cspan\u003e1\u003c/span\u003eb. In both samples, five distinct peaks were observed near 145, 203, 395, 521, and 635 cm\u0026thinsp;\u003csup\u003e\u0026minus;\u0026thinsp;1\u003c/sup\u003e, corresponding to the typical raman vibration modes of TiO\u003csub\u003e2\u003c/sub\u003e [\u003cspan\u003e26\u003c/span\u003e]. Additionally, two faint Raman peaks at 1599 and 1348 cm\u0026thinsp;\u003csup\u003e\u0026minus;\u0026thinsp;1\u003c/sup\u003e in the TiO\u003csub\u003e2\u003c/sub\u003e@C composite material were identified as the G and D peaks of carbon [\u003cspan\u003e27\u003c/span\u003e]. Figure \u003cspan\u003eS1\u003c/span\u003e presents the TG-DSC curve of TiO\u003csub\u003e2\u003c/sub\u003e@C. The TG curve demonstrates a weight loss up to 300\u0026deg;C, which is primarily attributed to the vaporization of surface-adsorbed water. Following this, a rapid decrease in weight is observed between 300\u0026deg;C and 500\u0026deg;C, accompanied by a significant exothermic peak at 375\u0026deg;C, which is attributed to the combustion and elimination of carbon. The carbon content, as determined from the TG-DSC curve, is calculated to be approximately 7.9%.\u003c/p\u003e\n\u003cp\u003eThe morphology of samples prepared through different processes was analyzed using SEM. Figure S2 illustrates the precursor, which displays an irregular shape characterized by several interconnected nanospheres (Figure S2a). Upon closer inspection, the precursor appears as a slightly rough spheroid with an approximate size of 500 nm (Figure S2b). Following heat treatment in various atmospheres, the overall morphology of the TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e samples remains largely unchanged compared to the precursor (Figs.\u0026nbsp;\u003cspan\u003e2\u003c/span\u003ea, c). However, a subtle distinction in surface morphology is observed, with TiO\u003csub\u003e2\u003c/sub\u003e exhibiting a relatively rougher surface due to the combustion of carbon during the precursor\u0026apos;s heat treatment in an air atmosphere (Figs.\u0026nbsp;\u003cspan\u003e2\u003c/span\u003eb, d). This combustion effectively promotes the further growth of TiO\u003csub\u003e2\u003c/sub\u003e grains, providing visual evidence for the inhibitory role of carbon in TiO\u003csub\u003e2\u003c/sub\u003e grain growth. TEM was employed to investigate the internal structure of the TiO\u003csub\u003e2\u003c/sub\u003e@C composite material. As shown in Fig.\u0026nbsp;\u003cspan\u003e2\u003c/span\u003ee, the TiO\u003csub\u003e2\u003c/sub\u003e@C nanospheres possess a compact solid internal structure, indicating that the TiO\u003csub\u003e2\u003c/sub\u003e@C composite has a low specific surface area (SSA). Figure\u0026nbsp;\u003cspan\u003e2\u003c/span\u003ef presents HRTEM image of the TiO\u003csub\u003e2\u003c/sub\u003e@C,\u003c/p\u003e\n\u003cp\u003erevealing clear lattice fringes corresponding to the anatase TiO\u003csub\u003e2\u003c/sub\u003e (101) crystal plane. Notably, amorphous carbon (shown as a white curved region) closely envelops the TiO\u003csub\u003e2\u003c/sub\u003e without discernible boundaries, suggesting a potential co-existence process during the formation of the TiO\u003csub\u003e2\u003c/sub\u003e@C precursor. This co-existence process facilitates the persistent polymerization of 3-aminophenol and methanal around TiO\u003csub\u003e2\u003c/sub\u003e, with the resulting polymer effectively preventing the aggregation of primary TiO\u003csub\u003e2\u003c/sub\u003e grains. The electron diffraction pattern depicted in Fig.\u0026nbsp;\u003cspan\u003e2\u003c/span\u003eg indicates that TiO\u003csub\u003e2\u003c/sub\u003e within the TiO\u003csub\u003e2\u003c/sub\u003e@C sample exists in a polycrystalline state. Additionally, Fig.\u0026nbsp;\u003cspan\u003e2\u003c/span\u003eh displays the elemental distribution mapping for TiO\u003csub\u003e2\u003c/sub\u003e@C, revealing a uniform distribution of C, Ti and O elements within the composite.\u003c/p\u003e\n\u003cp\u003eFigure \u003cspan\u003e3\u003c/span\u003e illustrates the SSA and pore size of both samples. As shown in Fig.\u0026nbsp;\u003cspan\u003e3\u003c/span\u003ea, there is no discernible hysteresis loop in the nitrogen adsorption/desorption curves for either sample at relative pressures (P/P\u003csub\u003e0\u003c/sub\u003e) of 0.5 and 1.0, indicating that the SSA of TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e is quite small. The SSA values for TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e were determined to be 10.41 and 9.84 m\u0026sup2; g⁻\u0026sup1;, respectively. Furthermore, Fig.\u0026nbsp;\u003cspan\u003e3\u003c/span\u003eb indicates that the pore sizes of TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e are predominantly concentrated at 4.8 and 4.3 nm, respectively. The observed difference in pore sizes can be attributed to the inhibition of TiO\u003csub\u003e2\u003c/sub\u003e grain growth by carbon during the heat treatment of the TiO\u003csub\u003e2\u003c/sub\u003e@C composite in an argon atmosphere. Such small SSA not only contribute to an increase in the tap density of the anode electrode material, thereby enhancing its volumetric energy density, but also significantly reduce the contact area between the active material and electrolyte. This reduction leads to a decrease in side reactions and an improvement in the ICE of the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode.\u003c/p\u003e\n\u003cp\u003eFigure \u003cspan\u003e4\u003c/span\u003ea presents the XPS full spectrum of both samples, indicating the presence of C, Ti and O elements on the surface of TiO\u003csub\u003e2\u003c/sub\u003e@C. Figure \u003cspan\u003e4\u003c/span\u003eb illustrates the high-resolution XPS (HR-XPS) spectra of the Ti 2p for both TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e. The Ti 2p HR-XPS spectra of the TiO\u003csub\u003e2\u003c/sub\u003e sample reveal a pair of peaks located at 463.9 and 458.2 eV, corresponding to the binding energies of 2p\u003csub\u003e1/2\u003c/sub\u003e and 2p\u003csub\u003e3/2\u003c/sub\u003e of Ti\u003csup\u003e4+\u003c/sup\u003e [\u003cspan\u003e28\u003c/span\u003e]. In contrast, the Ti 2p HR-XPS spectra of the TiO\u003csub\u003e2\u003c/sub\u003e@C sample exhibit two pairs of peaks: a prominent pair at 464.8 and 458.9 eV, which correspond to 2p\u003csub\u003e1/2\u003c/sub\u003e and 2p\u003csub\u003e3/2\u003c/sub\u003e of Ti\u003csup\u003e4+\u003c/sup\u003e, and another pair at 463.8 and 458.2 eV, attributed to 2p\u003csub\u003e1/2\u003c/sub\u003e and 2p\u003csub\u003e3/2\u003c/sub\u003e of Ti\u003csup\u003e3+\u003c/sup\u003e [\u003cspan\u003e29\u003c/span\u003e]. Notably, the binding energy of Ti\u003csup\u003e4\u0026thinsp;+\u003c/sup\u003e\u0026thinsp;in the TiO\u003csub\u003e2\u003c/sub\u003e@C sample is higher, which can be ascribed to the presence of Ti\u003csup\u003e3+\u003c/sup\u003e. Figure \u003cspan\u003e4\u003c/span\u003ec displays the O 1s HR-XPS spectrum of the TiO\u003csub\u003e2\u003c/sub\u003e@C sample, where three peaks can be fitted at 531.9, 530.2 and 529.9 eV, corresponding to the oxygen vacancy (O-Ti\u003csup\u003e3+\u003c/sup\u003e), O-C, and O-Ti\u003csup\u003e4\u0026thinsp;+\u003c/sup\u003e\u0026thinsp;bonds, respectively [\u003cspan\u003e30\u003c/span\u003e]. The formation of O-Ti\u003csup\u003e3\u0026thinsp;+\u003c/sup\u003e\u0026thinsp;in the TiO\u003csub\u003e2\u003c/sub\u003e@C may result from insufficient oxygen during heat treatment in an argon atmosphere. Previous studies have confirmed that the presence of O-Ti\u003csup\u003e3\u0026thinsp;+\u003c/sup\u003e\u0026thinsp;not only enhances the intrinsic conductivity of TiO\u003csub\u003e2\u003c/sub\u003e but also increases the active sites for lithium storage in TiO\u003csub\u003e2\u003c/sub\u003e@C composite materials [\u003cspan\u003e31\u003c/span\u003e]. Figure \u003cspan\u003e4\u003c/span\u003ed illustrates the HR-XPS of C 1s in TiO\u003csub\u003e2\u003c/sub\u003e@C, where the two fitted peaks at 284.8 and 283.4 eV correspond to the binding energies of C-C/C\u0026thinsp;=\u0026thinsp;C and C-O bonds, respectively [\u003cspan\u003e32\u003c/span\u003e].\u003c/p\u003e\n\u003cp\u003eThrough the analysis of the aforementioned test results, this paper proposes a surface-confined in-situ inter-growth mechanism for the formation of TiO\u003csub\u003e2\u003c/sub\u003e@C, as illustrated in Fig.\u0026nbsp;\u003cspan\u003e5\u003c/span\u003e. The experimental synthesis process described herein involves only three reactants: TBOT, methanal, and 3-aminophenol. Initially (Step I), due to the high concentration of NH\u003csub\u003e3\u003c/sub\u003e\u0026middot;H\u003csub\u003e2\u003c/sub\u003eO, TBOT rapidly hydrolyzes to form primary TiO\u003csub\u003e2\u003c/sub\u003e grains, while NH\u003csup\u003e4\u0026thinsp;+\u003c/sup\u003e\u0026thinsp;accumulate on its surface. Concurrently, methanal and 3-aminophenol undergo rapid polymerization to generate 3-aminophenol-methanal (3-APM) oligomers in the presence of NH\u003csup\u003e4+\u003c/sup\u003e, which subsequently accumulate around the primary TiO\u003csub\u003e2\u003c/sub\u003e grains, resulting in the formation of high-density TiO\u003csub\u003e2\u003c/sub\u003e@3-APM microspheres. Subsequently (Step II), following thermal treatment under an argon atmosphere, TiO\u003csub\u003e2\u003c/sub\u003e@3-APM is transformed into TiO\u003csub\u003e2\u003c/sub\u003e@C with oxygen vacancies due to the absence of an oxygen source.\u003c/p\u003e\n\u003cp\u003eIn the preparation of nano-TiO\u003csub\u003e2\u003c/sub\u003e, NH\u003csub\u003e3\u003c/sub\u003e\u0026middot;H\u003csub\u003e2\u003c/sub\u003eO solution is typically excluded because of its propensity to induce rapid hydrolysis of the titanium source, leading to significant particle aggregation of TiO\u003csub\u003e2\u003c/sub\u003e. In contrast, the synthesis method presented in this paper strategically leverages the rapid hydrolysis properties of the titanium source, facilitating the formation of a micro-environment on the TiO\u003csub\u003e2\u003c/sub\u003e surface that triggers the polymerization of 3-aminophenol with methanal. The advantages of this approach are as follows: The technical route is straightforward, time-efficient, and does not require precise control, thereby enhancing its feasibility for commercial preparation; The micro-environment created around the primary TiO\u003csub\u003e2\u003c/sub\u003e promotes a close association between TiO\u003csub\u003e2\u003c/sub\u003e and 3-APM oligomers, which is essential for the subsequent thermal treatment aimed at achieving a highly integrated carbon and TiO\u003csub\u003e2\u003c/sub\u003e structure.\u003c/p\u003e\n\u003cp\u003eThe electrochemical behavior of TiO\u003csub\u003e2\u003c/sub\u003e@C electrode was investigated using CV, with the result presented in in Fig.\u0026nbsp;\u003cspan\u003e6\u003c/span\u003ea. During the initial discharge process, the CV curve reveals a broad reduction peak between 1.75 and 1 V, indicative of the initial Li\u0026thinsp;\u003csup\u003e+\u003c/sup\u003e\u0026thinsp;insertion into TiO\u003csub\u003e2\u003c/sub\u003e@C and the formation of the solid electrolyte interphase (SEI) [\u003cspan\u003e33\u003c/span\u003e]. Subsequently, during the charging process, the Li\u0026thinsp;\u003csup\u003e+\u003c/sup\u003e\u0026thinsp;extraction potential is observed to be approximately 2.2 V. In the subsequent cycles, the CV curves demonstrate a notable overlap, with the Li\u0026thinsp;\u003csup\u003e+\u003c/sup\u003e\u0026thinsp;insertion potential shifting towards a higher value. This observation suggests that the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode has undergone a degree of activation, exhibiting excellent electrochemical reversibility and structural stability. The discharge/charge curves for both electrodes during the first three cycles at a current density of 0.2 A/g are presented in Fig.\u0026nbsp;\u003cspan\u003e6\u003c/span\u003eb and Figure S3. The initial discharge specific capacities of the TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes are 584.4 and 368.2 mAh/g, respectively. Correspondingly, the initial charge specific capacities are 438.3 mAh/g for TiO\u003csub\u003e2\u003c/sub\u003e@C and 272.4 mAh/g for TiO\u003csub\u003e2\u003c/sub\u003e. The ICE for TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes are 75% and 74%, respectively, surpassing those reported in previous studies (Fig.\u0026nbsp;\u003cspan\u003e6\u003c/span\u003ec) [\u003cspan\u003e16\u003c/span\u003e, \u003cspan\u003e20\u003c/span\u003e, \u003cspan\u003e23\u003c/span\u003e, \u003cspan\u003e34\u003c/span\u003e\u0026ndash;\u003cspan\u003e36\u003c/span\u003e]. These results demonstrate that the experimental approach employed in this study effectively enhances the ICE of the electrode by minimizing their SSA. The discharge/charge curves of both the TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes over the subsequent two cycles exhibit a significant degree of overlap, indicating the high reversibility of these electrode materials during the Li\u0026thinsp;\u003csup\u003e+\u003c/sup\u003e\u0026thinsp;insertion and extraction processes. Furthermore, the reversible specific capacity of the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode is approximately 1.6 times greater than that of the TiO\u003csub\u003e2\u003c/sub\u003e electrode. This enhancement can be attributed to the intimate connection between TiO\u003csub\u003e2\u003c/sub\u003e and carbon within the TiO\u003csub\u003e2\u003c/sub\u003e@C composite, which facilitates the full participation of the TiO\u003csub\u003e2\u003c/sub\u003e active material. Additionally, the presence of oxygen vacancies provides extra Li\u0026thinsp;\u003csup\u003e+\u003c/sup\u003e\u0026thinsp;storage active sites. Figures\u0026nbsp;\u003cspan\u003e6\u003c/span\u003e (d, e) illustrate the cyclic and rate performance of both electrodes. As depicted in Fig.\u0026nbsp;\u003cspan\u003e6\u003c/span\u003ed, both electrodes demonstrate remarkable cyclic stability, with only a slight decrease in reversible specific capacity during the initial cycles. The reversible specific capacities recorded during the second cycle for the TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes are 466.4 and 287.5 mAh/g, respectively. After 200 cycles, the reversible specific capacities are maintained at 426.8 and 275.9 mAh/g, respectively. The capacity retention rates for the TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes, relative to their second cycle capacities, are 91.5% and 95.6%, respectively. Notably, the TiO\u003csub\u003e2\u003c/sub\u003e electrode exhibits a superior capacity retention rate compared to the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode, which may be attributed to the TiO\u003csub\u003e2\u003c/sub\u003e electrode undergoing stronger activation during repeated charge and discharge cycles, thereby enabling more TiO\u003csub\u003e2\u003c/sub\u003e active sites to participate in Li\u003csup\u003e+\u003c/sup\u003e. As the current density increases, the reversible specific capacities of both the TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes exhibit a gradual decline, as illustrated in Fig.\u0026nbsp;\u003cspan\u003e6\u003c/span\u003ee. The average reversible specific capacities of the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode at current densities of 0.1, 0.2, 0.5, 1.0, 2.0, and 5.0 A/g are 512.9, 468.2, 417.4, 350.9, 299.1, and 210.1 mAh/g, respectively, which surpass those reported in previous studies (Fig.\u0026nbsp;\u003cspan\u003e6\u003c/span\u003ef) [\u003cspan\u003e20\u003c/span\u003e, \u003cspan\u003e37\u003c/span\u003e\u0026ndash;\u003cspan\u003e42\u003c/span\u003e]. Upon returning the current density to 0.1 A/g, the average reversible specific capacity is recorded at 511.8 mAh/g, indicating remarkable cycling reversibility. In contrast, the reversible capacity of TiO\u003csub\u003e2\u003c/sub\u003e is only 124.3 mAh/g at a current density of 5.0 A/g, which is significantly lower than that of TiO\u003csub\u003e2\u003c/sub\u003e@C. This disparity suggests that the incorporation of carbon and the presence of oxygen vacancies considerably enhance the electrochemical kinetics of TiO\u003csub\u003e2\u003c/sub\u003e@C. The long-term cycling stability of the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode, as demonstrated in Fig.\u0026nbsp;\u003cspan\u003e6\u003c/span\u003eg, confirms that it possesses an extended cycling life and stable coulombic efficiency. After 2000 cycles, the reversible specific capacity decreases from an initial value of 216.8 mAh/g to 203.8 mAh/g, resulting in an impressive capacity retention rate of 94%. This translates to a capacity decay rate of only 0.003% per cycle, indicating that the TiO\u003csub\u003e2\u003c/sub\u003e@C composite maintains exceptional structural integrity.\u003c/p\u003e\n\u003cp\u003eThe electrochemical kinetics of TiO\u003csub\u003e2\u003c/sub\u003e@C and TiO\u003csub\u003e2\u003c/sub\u003e electrodes were investigated using EIS and GITT, with the results presented in Fig.\u0026nbsp;\u003cspan\u003e7\u003c/span\u003e. The EIS data indicate that the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode exhibits reduced charge transfer resistance (Rct), as shown in Fig.\u0026nbsp;\u003cspan\u003e7\u003c/span\u003ea. Figure\u0026nbsp;\u003cspan\u003e7\u003c/span\u003eb illustrates the GITT curves for both electrodes. The diffusion rates of Li\u0026thinsp;\u003csup\u003e+\u003c/sup\u003e\u0026thinsp;during the charge and discharge processes were calculated using the following equation:\u003cimg src=\"https://myfiles.space/user_files/122228_c8a1650c59388082/122228_custom_files/img1727261786.png\"\u003e [\u003cspan\u003e30\u003c/span\u003e]. The diffusion rates of Li\u003csup\u003e+\u003c/sup\u003e, depicted in Figs.\u0026nbsp;\u003cspan\u003e7\u003c/span\u003ec and \u003cspan\u003e7\u003c/span\u003ed, indicate that the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode achieves a diffusion rate ranging from approximately 10\u0026thinsp;\u003csup\u003e\u0026minus;\u0026thinsp;9\u003c/sup\u003e to 10\u0026thinsp;\u003csup\u003e\u0026minus;\u0026thinsp;10\u003c/sup\u003e cm\u0026sup2; s\u0026thinsp;\u003csup\u003e\u0026minus;\u0026thinsp;1\u003c/sup\u003e, which is significantly higher than that of the TiO\u003csub\u003e2\u003c/sub\u003e electrode. By integrating the findings from the EIS and GITT tests, it can be concluded that the optimal composite structure of TiO\u003csub\u003e2\u003c/sub\u003e with carbon, coupled with the presence of oxygen vacancies, collectively enhances the electrochemical kinetics of the TiO\u003csub\u003e2\u003c/sub\u003e@C electrode, thereby resulting in superior electrochemical performance.\u003c/p\u003e"},{"header":"4. Conclusions","content":"\u003cp\u003eNonporous TiO\u003csub\u003e2\u003c/sub\u003e@C microspheres with a highly integrated structure were synthesized using a surface-confined in-situ inter-growth strategy. When employed as an anode electrode for LIB, these microspheres exhibit a high volumetric energy density and improved ICE. The enhanced ICE is attributed to the extremely small SSA of the TiO\u003csub\u003e2\u003c/sub\u003e@C microspheres, which minimizes contact between the active material and the electrolyte, thereby reducing the occurrence of side reactions. Results from electrochemical kinetics studies strongly indicate that the synergistic interaction between the highly integrated structure and oxygen vacancies contributes to effective Li\u0026thinsp;\u003csup\u003e+\u003c/sup\u003e\u0026thinsp;storage. Furthermore, our synthesis method is not only efficient but also presents a novel approach for the development of other electrode materials.\u003c/p\u003e\n"},{"header":"Declarations","content":"\u003cp\u003e\u003cstrong\u003eData availability\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThe authors declare that all data generated or analysed during this study are included in this published article.\u003c/p\u003e\u003cp\u003e\u003cstrong\u003eAcknowledgements\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThis research is financially supported by the China Postdoctoral Science Foundation (Grant No. 2023M732858), the Shandong Provincial Natural Science Foundation (Grant No. ZR2022QE290) and the development plan for Weifang city (Grant No. 2023GX061).\u0026nbsp;\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eSupporting Information\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThe Supporting Information is available free of charge at:\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eAuthor contributions\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eJinpeng Yin, Guanqin Wang, Dongqing Kong, Chuang Li, Qiang Zhang, Dongbai Xie, Yangyang Yan, Ning Li, Qiang Li wrote the main manuscript text and prepared all figures. All authors reviewed the manuscript.\u003c/p\u003e\n"},{"header":"References","content":"\u003col\u003e\n\u003cli\u003eWang, C., Yang, C. \u0026amp; Zheng, Z. Toward practical high‐energy and high‐power lithium battery anodes: present and future. \u003cem\u003eAdv. Sci.\u003c/em\u003e\u003cstrong\u003e9,\u003c/strong\u003e 2105213 (2022).\u003c/li\u003e\n\u003cli\u003eLi, J. \u003cem\u003eet al.\u003c/em\u003e Revolutionizing lithium storage capabilities in TiO\u003csub\u003e2\u003c/sub\u003e by expanding the redox range. \u003cem\u003eACS Nano\u003c/em\u003e\u003cstrong\u003e17,\u003c/strong\u003e 21604-21613 (2023).\u003c/li\u003e\n\u003cli\u003eZhang, Y. \u003cem\u003eet al.\u003c/em\u003e Polydopamine sacrificial layer mediated SiO\u003csub\u003ex\u003c/sub\u003e/C@ C yolk@ shell structure for durable lithium storage. \u003cem\u003eMater. Chem. 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Facile synthesis of uniform N-doped carbon-coated TiO\u003csub\u003e2\u003c/sub\u003e hollow spheres with enhanced lithium storage performance. \u003cem\u003eNanoscale \u003c/em\u003e\u003cstrong\u003e13, \u003c/strong\u003e2368-2372 (2021).\u003c/li\u003e\n\u003cli\u003eRen, Y. \u003cem\u003eet al.\u003c/em\u003e Flower-like TiO\u003csub\u003e2\u003c/sub\u003e hollow microspheres with mixed-phases for high-pseudocapacitive lithium storage. \u003cem\u003eJ. Alloys Compd. \u003c/em\u003e\u003cstrong\u003e902,\u003c/strong\u003e 163730 (2022).\u003c/li\u003e\n\u003c/ol\u003e"}],"fulltextSource":"","fullText":"","funders":[],"hasAdminPriorityOnWorkflow":false,"hasManuscriptDocX":true,"hasOptedInToPreprint":true,"hasPassedJournalQc":"","hasAnyPriority":false,"hideJournal":false,"highlight":"","institution":"","isAcceptedByJournal":true,"isAuthorSuppliedPdf":false,"isDeskRejected":"","isHiddenFromSearch":false,"isInQc":false,"isInWorkflow":false,"isPdf":false,"isPdfUpToDate":true,"isWithdrawnOrRetracted":false,"journal":{"display":true,"email":"[email protected]","identity":"scientific-reports","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":false,"externalIdentity":"scirep","sideBox":"Learn more about [Scientific Reports](http://www.nature.com/srep/)","snPcode":"","submissionUrl":"","title":"Scientific Reports","twitterHandle":"","acdcEnabled":true,"dfaEnabled":true,"editorialSystem":"stoa","reportingPortfolio":"Scientific Reports","inReviewEnabled":true,"inReviewRevisionsEnabled":true},"keywords":"Lithium-ion batteries, TiO2, Coulombic efficiency, Oxygen vacancies","lastPublishedDoi":"10.21203/rs.3.rs-4923096/v1","lastPublishedDoiUrl":"https://doi.org/10.21203/rs.3.rs-4923096/v1","license":{"name":"CC BY 4.0","url":"https://creativecommons.org/licenses/by/4.0/"},"manuscriptAbstract":"\u003cp\u003eTo enhance the volumetric energy density and initial coulombic efficiency (ICE) of titanium oxide (TiO\u003csub\u003e2\u003c/sub\u003e) as anode electrode material for lithium-ion batteries (LIB), this study employed a surface-confined in-situ inter-growth mechanism to prepare a TiO\u003csub\u003e2\u003c/sub\u003e embedded carbon microsphere composite. The results revealed that the composite exhibited a highly integrated structure of TiO\u003csub\u003e2\u003c/sub\u003e with oxygen vacancies and carbon, along with an exceptionally small specific surface area of 11.52 m\u0026sup2;/g. Due to its unique microstructure, the composite demonstrated remarkable lithium storage properties, including a high ICE of 75%, a notable capacity of 426.8 mAh/g after 200 cycles at 0.2 A/g, superior rate performance of 210.1 mAh/g at 5 A/g, and an outstanding cycle life, with a capacity decay rate of only 0.003% per cycle over 2000 cycles. Furthermore, electrochemical kinetic studies further validated the advantages of this microstructure.\u003c/p\u003e","manuscriptTitle":"Nonporous TiO 2 @C Microsphere with a Highly Integrated Structure for High Volumetric Lithium Storage and Enhance Initial Coulombic Efficiency","msid":"","msnumber":"","nonDraftVersions":[{"code":1,"date":"2024-09-25 11:03:42","doi":"10.21203/rs.3.rs-4923096/v1","editorialEvents":[{"type":"communityComments","content":0},{"type":"decision","content":"Revision requested","date":"2024-09-24T07:11:03+00:00","index":"","fulltext":""},{"type":"editorInvitedReview","content":"","date":"2024-09-20T11:10:59+00:00","index":"hide","fulltext":""},{"type":"editorInvitedReview","content":"","date":"2024-09-19T09:23:35+00:00","index":"hide","fulltext":""},{"type":"editorInvitedReview","content":"","date":"2024-09-09T06:58:25+00:00","index":"hide","fulltext":""},{"type":"reviewerAgreed","content":"146764312845335757904684394233264156478","date":"2024-08-28T11:52:20+00:00","index":"hide","fulltext":""},{"type":"reviewerAgreed","content":"62413876890918071770041290039787369228","date":"2024-08-28T08:50:34+00:00","index":"hide","fulltext":""},{"type":"reviewerAgreed","content":"192493219495790071034430729389315838053","date":"2024-08-28T05:45:51+00:00","index":"hide","fulltext":""},{"type":"reviewersInvited","content":"","date":"2024-08-28T05:34:00+00:00","index":"","fulltext":""},{"type":"editorAssigned","content":"","date":"2024-08-28T05:29:47+00:00","index":"","fulltext":""},{"type":"editorInvited","content":"","date":"2024-08-28T03:25:39+00:00","index":"","fulltext":""},{"type":"checksComplete","content":"","date":"2024-08-27T04:45:23+00:00","index":"","fulltext":""},{"type":"submitted","content":"Scientific Reports","date":"2024-08-16T07:09:00+00:00","index":"","fulltext":""}],"status":"published","journal":{"display":true,"email":"[email protected]","identity":"scientific-reports","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":false,"externalIdentity":"scirep","sideBox":"Learn more about [Scientific Reports](http://www.nature.com/srep/)","snPcode":"","submissionUrl":"","title":"Scientific Reports","twitterHandle":"","acdcEnabled":true,"dfaEnabled":true,"editorialSystem":"stoa","reportingPortfolio":"Scientific Reports","inReviewEnabled":true,"inReviewRevisionsEnabled":true}}],"origin":"","ownerIdentity":"b5771abb-7bdc-4276-a29c-d1829bf340f6","owner":[],"postedDate":"September 25th, 2024","published":true,"recentEditorialEvents":[],"rejectedJournal":[],"revision":"","amendment":"","status":"published-in-journal","subjectAreas":[],"tags":[],"updatedAt":"2024-12-30T16:09:19+00:00","versionOfRecord":{"articleIdentity":"rs-4923096","link":"https://doi.org/10.1038/s41598-024-82179-z","journal":{"identity":"scientific-reports","isVorOnly":false,"title":"Scientific Reports"},"publishedOn":"2024-12-28 15:57:30","publishedOnDateReadable":"December 28th, 2024"},"versionCreatedAt":"2024-09-25 11:03:42","video":"","vorDoi":"10.1038/s41598-024-82179-z","vorDoiUrl":"https://doi.org/10.1038/s41598-024-82179-z","workflowStages":[]},"version":"v1","identity":"rs-4923096","journalConfig":"researchsquare"},"__N_SSP":true},"page":"/article/[identity]/[[...version]]","query":{"redirect":"/article/rs-4923096","identity":"rs-4923096","version":["v1"]},"buildId":"qtupq5eGEP_6zYnWcrvyt","isFallback":false,"isExperimentalCompile":false,"dynamicIds":[84888],"gssp":true,"scriptLoader":[]}