Next Article in Journal
Effect of Hydrophobic and Hydrophilic Metal Oxide Nanoparticles on the Performance of Xanthan Gum Solutions for Heavy Oil Recovery
Next Article in Special Issue
Manufacture of Highly Transparent and Hazy Cellulose Nanofibril Films via Coating TEMPO-Oxidized Wood Fibers
Previous Article in Journal
Magnetic Nanofiber Mats for Data Storage and Transfer
Previous Article in Special Issue
Three-Dimensional Stable Alginate-Nanocellulose Gels for Biomedical Applications: Towards Tunable Mechanical Properties and Cell Growing
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Nanomaterials
Volume 9
Issue 1
10.3390/nano9010093
nanomaterials-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Article

Hydrothermal Synthesis of Cellulose-Derived Carbon Nanospheres from Corn Straw as Anode Materials for Lithium ion Batteries

by
Kaifeng Yu
1,
Jingjing Wang
1,
Kexian Song
1,
Xiaofeng Wang
2,
Ce Liang
1,* and
Yanli Dou
1,*
1
Key Laboratory of automobile Materials, Ministry of Education, and College of Materials Science and Engineering, Jilin University, Changchun 130025, China
2
State Key Laboratory of Inorganic Synthesis and Preparative Chemistry, College of Chemistry, Jilin University, Changchun 130025, China
*
Authors to whom correspondence should be addressed.
Nanomaterials 2019, 9(1), 93; https://doi.org/10.3390/nano9010093
Submission received: 10 December 2018 / Revised: 7 January 2019 / Accepted: 8 January 2019 / Published: 12 January 2019
(This article belongs to the Special Issue Cellulose Nanomaterials)
Browse Figures
Versions Notes

Abstract

:
As a most attractive renewable resource, biomass has the advantages of low pollution, wide distribution and abundant resources, promoting its applications in lithium ion batteries (LIBs). Herein, cellulose-derived carbon nanospheres (CCS) were successfully synthesized by hydrothermal carbonization (HTC) from corn straw for use as an anode in LIBs. The uniform distribution and cross-linked structure of carbon nanospheres were obtained by carefully controlling reaction time, which could not only decrease the transport pathway of lithium ions, but also reduce the structural damage caused by the intercalation of lithium ions. Especially, obtained after hydrothermal carbonization for 36 h, those typical characteristics make it deliver excellent cycling stability as well as the notable specific capacity of 577 mA h g−1 after 100 cycles at 0.2C. Hence, this efficient and environment-friendly method for the fabrication of CCS from corn straw could realize the secondary utilization of biomass waste, as well as serve as a new choice for LIBs anode materials.

1. Introduction

With the shortage of fossil fuels and the emergence of environmental problems, there is a booming demand for clean energy to meet current and future energy needs [1,2,3,4,5]. There are many kinds of biomass resources, among which cellulose, hemicellulose and lignin are the main forms. Biomass is an economical and promising carbon material for the anode of lithium ion batteries (LIBs), which has attracted the attention of many experts and scholars [2,3,5]. At present, it is crucial to realize the comprehensive utilization of biomass for the development of the LIBs system [5,6,7,8,9]. In recent years, with the rapid development of new energy technology, it is a trend to prepare carbonaceous LIBs anode materials using biomass as raw materials [9,10,11,12,13]. As a kind of farmland waste, corn straw is a kind of non-pollution renewable resource. Using corn straw-derived carbon material as an electrode not only realizes the re-using of agricultural waste, but also provides a novel environment-friendly way to obtain negative carbon material for LIBs.
In order to enhance the energy density, cycle performance and rate performance of LIBs, many efforts have been made on the structure of anode carbon materials, such as carbon nanotube, carbon nanowire, carbon nanosphere, carbon nanorod and carbon nanocapsule [14,15]. Carbon nanosphere is an important structure of negative carbon materials, which is considered as a promising precursor of carbon electrode materials owing to the higher bulk density and higher volume specific capacity than natural graphite and other flake materials. Moreover, the spherical structure exhibits excellent thermal and chemical stability of insertion and extraction of lithium ions [16,17,18,19,20].
At present, hydrothermal carbonization is the main method to prepare carbon nanospheres, as well as an effective way to realize the thermochemical conversion of biomass. HTC has the advantages of a simple operation process, mild synthesis conditions and renewable raw materials, providing a broad prospect for the large-scale production of carbon nanospheres [21,22,23,24]. Zhao et al. prepared well-dispersed micrometer-sized carbon nanospheres from cellulose by citric acid catalysed HTC (200–240 °C), and the diameter of carbon nanospheres became wider with the increase of citric acid concentration, reaction temperature and reaction time [25]. Hao et al. reported a new technique for preparing porous carbon nanospheres by the HTC of waste sugar solution followed through KOH activation. The specific capacity of the carbon nanospheres delivered good cycle life (296.1 F g−1 at a current density of 40 mA g−1) and superior rate capability (1.5 A g−1 after 5000 cycles) [26]. Inada et al. prepared carbon nanospheres by HTC from glucose at 800 °C; the obtained carbon nanospheres possessed a highly specific surface area, low resistance and high capacitance (higher than commercial activated carbon electrode) [27]. Remarkably, the work published by Xie and coworkers reported the preparation of homogeneous nanospheres (120, 360 nm) by introducing a small amount of poly (4-styrenesulfonic acid-co-maleic acid) sodium salt (PSSMA) into the hydrothermal system. Nanospheres with an adjustable size in the range of 1.4 to 5.2 μm were prepared in the presence of PSSMA and hydrochloric acid and showed good performance in catalytic hydrogenation [28].
Up to the present, although great progress has been made in the preparation of carbon nanospheres, the application of carbon nanospheres in LIBs is still a great challenge. Complex preparation processes and low yield have become significant drawback for LIBs anodes, which hinder the commercial development of carbon nanospheres [6,13,29]. To address these issues, it is highly desirable to develop an economical and efficient method to prepare carbon nanospheres, which will circumvent these limitations, especially for large batteries. We propose, herein, an environmental and simple route to obtain cellulose-derived carbon nanospheres by using corn straw as raw material. Through controlling the reaction time, the cellulose-derived carbon nanospheres after HTC for 36 h display an excellent electrical conductivity and rate performance, opening up a new opportunity for LIBs anodes.

2. Materials and Methods

2.1. Materials Synthesis

Corn straw was collected from a farmland in Jilin Province, China. Corn straw was washed with deionized water and dried in oven at 60 °C for 24 h. The dried corn straw was pulverized into powder by a pulverizing machine. Thirty grams of corn straw power was added to 4% H2SO4 at 1:10 solid-liquid ratio at 90 °C water bath. The xylose acid solution and filtrate residue were obtained by separating the solution from the filter residue after the reaction. Filter residue I was washed to neutral and dried with deionized water. Then Lignin was removed from filter residue I and 50 g L−1 NaOH at 99 °C water bath at 1:15 solid-liquid ratio. Lignin lye solution and filter residue Ⅱ were obtained by separating the reaction solution from the filter residue. The filter residue Ⅱ was washed to neutral and dry with deionized water. After filtering, the solid was transferred to a stainless steel autoclave with water treated at 200 °C. The reaction time was carried out for 24, 36, 48 and 60 h, respectively. The powder was carbonized in a tubular furnace at 600 °C under argon atmosphere at a heating rate of 5 °C min−1. The obtained samples were washed with deionized water and ethanol to remove tar and other organics, and then were dried in an oven at 60 °C. The samples were labeled as CCS-24, CCS-36, CCS-48, CCS-60, respectively.

2.2. Material Characterizations

X-ray diffraction patterns of samples were measured with X-ray diractometer (Siemens D5000, Munich, Germany) with nickel-filtered Cu K radiation (λ = 0.15406 nm) at 4° min−1. Raman spectra was tested on a Renishaw inVia instrument (wavenumber range: 200–2000 cm−1, λ = 514 nm). Thermogravimetric analysis (TGA) of corn straw was accomplished on Q500 thermogravimetric analyzer (TA Instruments, New Castle, PA, USA) at a scanning rate of 5 °C min−1 from 20 °C to 800 °C under N2 atmosphere. The specific surface area and pore diameter were carried out using nitrogen adsorption–desorption measurements (Micromeritics, ASAP2420, Micromeritics Instrument, Norcross, GA, USA). The morphology of samples was characterized by scanning electron microscopy (SEM, JEOL-JSM-6700F, JEOL Ltd, Tokyo, Japan) and transmission electron microscopy (TEM, JEM-2100F, JEOL Ltd, Tokyo, Japan). The superficial area and pore size distribution of the carbons were observed through Micromeritics ASAP2420.

2.3. Electrochemical Measurement

The slurry was prepared by mixing CCS, acetylene black and PVDF with a mass ratio of 8:1:1 in a mixing bottle. After grinding evenly, N-methyl-2-pyrrolidone was added into the mixture and then magnetically stirred for 6 h. The agitated paste was smeared on the copper foil, followed by drying in a vacuum oven at 120 °C for 12 h. The dried anode plate was punched on the sheet press to form a circular plate with a diameter of 10 mm; the circular electrode plates were weighed and numbered. The electrode loading mass was 0.13 mg cm−2. Coin-type (CR2025) cells were assembled in a glove box filled with argon. The opposite electrode and reference electrode used a lithium metal sheet, and polypropylene microporous membrane was used as the diaphragm. EC and DMC were used as the electrolyte solvent with a volume ratio of 1:1; LiPF6 was used as electrolyte solute at 1 mol L−1. The electrochemical performance was tested after 12 h of battery assembly. Cyclic voltammograms and impedance curve were performed on an electrochemical workstation (CHI660C) within a voltage window of 0–3.0 V at a scan rate of 0.1 mV s−1. The charge–discharge performance was tested between 0.02 V and 3.0 V at a 0.2C (1C = 372 mA g−1) on a LAND (CT2001A) battery system.

3. Results

3.1. Preparation of CCS

Up to now, Lamer’s “nucleation-diffusion control” model has been widely used to explain the formation of carbon nanospheres in the hydrothermal process, including nucleation and growth [30,31]. At first, the aromatic nuclei are formed in the solution. When the concentration reaches the saturation critical value, the nucleation is produced, and then the crystal nuclei will grow under the joint action of diffusion and adsorption [29,30,31,32]. During the preparation of CCS, the morphology of carbon materials changed greatly from corn straw to carbon nanospheres. Figure 1 shows the schematic illustration of the formation of CCS. The corn straw was hydrolyzed under the action of acid to remove hemicelluloses and then boiled with alkali to remove lignin to obtain cellulose. After acidizing hydrolysis and alkali boiling of corn straw, cellulose with a block structure was obtained. The subsequent hydrothermal carbonation stage is the key to the formation of carbon nanospheres. Firstly, at a high temperature and high pressure, cellulose molecules hydrolyze in aqueous solution to form glucose. Soluble 5-hydroxymethylfurfural (HMF) was formed by condensation of hydroxaldehyde between glucose molecules, which is considered to be an important unit of the next step of the reaction. HMF is condensed by dehydration between molecules to form soluble polymers, then the aromatization reaction took place in the dehydrogenation of polymers. The aromatization products formed aromatic clusters through intermolecular dehydration [22,29,30,31,32,33,34,35,36,37]. The resulting aromatic compounds are thought to be the core of carbon nanospheres. When the aromatic group in the solution reaches the critical value, explosive nucleation will occur and the resulting carbon nucleus grows in the aqueous solution isotropic through diffusion. According to the principle of similarity, hydrophilic groups (such as hydroxyl groups, carboxyl groups) and hydrophobic substances (such as aromatic rings and ethers) are covalently bonded to form carbon nanospheres [35,38,39,40].

3.2. Characterization of CCS

Figure 2 shows the X-ray diffraction pattern of CCS-24, CCS-36, CCS-48 and CCS-60 samples. Two peaks can be observed near 22° and 44°, corresponding to the crystal plane (002) and (100) of typical disordered carbon. The intense peak (002) is commonly associated to the carbon interlayer-stacking structure and (100) to the interlayer reflection of the hexagonal carbon structure [41]. With the increase of reaction time in the HTC stage, the peak strength did not change obviously, which indicates that the reaction time has no obvious influence on the formation of amorphous carbon. Figure 2b displays the Raman spectrum of CCS-24, CCS-36, CCS-48 and CCS-60 samples. Although reaction time had no obvious influence on amorphous carbon, it changed the disorder degree of samples. The two characteristic peaks at 1340 and 1590 cm−1 correspond to the D and G bands. The D band is caused by the defects and disorder in the carbon material, and the G band is caused by the stretching of the C–C bond in the graphite. The ID/IG ratio of the CCS-36 sample was 0.87, significantly lower than that of CCS-24 (ID/IG = 0.92), CCS-48 (ID/IG = 0.96) and CCS-60 (ID/IG = 0.90), indicating the reduced disorder degree of the materials due to uniform distribution of carbon nanospheres. Figure 2c shows a thermogravimetric curve of corn straw. The first weight loss at less than 300 °C can be related to the presence of unbounded/physisorbed water. When the temperature exceeds 300 °C, the loss of weight is due to thermal degradation. The residual weight at 800 °C is estimated to be 2.63 wt.%.
In order to characterize the structure of carbon materials, the specific surface area and pore size distribution of samples are also measured through N2. BJH adsorption–desorption. As depicted in Figure 3a, the isotherm of CCS samples belongs to the type Ⅳ adsorption isotherm. At lower relative pressure, the curve rises upward, indicating the existence of micropores. These micropores are produced during the carbonization and activation stage. When the relative pressure is about 0.3, capillary condensation occurs, and the desorption isotherm lags behind the adsorption isotherm. The phenomenon of adsorption hysteresis that occur in CCS samples demonstrate the existence of mesopores (2–50 nm). When the relative pressure is close to 1, the adsorption of the macropores increases and the adsorption curve rises quickly. The specific surface areas of CCS-24, CCS-36, CCS-48 and CCS-60 are 183, 402, 201 and 339 m2 g−1, respectively. CCS-36 exhibits a larger specific surface area due to a larger number of spheres and cross-linked structure, which is more favorable for the intercalation and removal of lithium ions. Furthermore, the BJH (Barrett-Joyner-Halenda) pore size distribution diagrams are shown in Figure 3b. The average pore sizes of CCS-24, CCS-36, CCS-48, CCS-60 are 4.0, 4.1, 6.1 and 5.3 nm, respectively. The pore size of the four samples is mainly between 2–10 nm, the existence of these mesopores can promote the infiltration of the materials in the electrolyte and facilitate the diffusion of lithium ions in the electrode materials. The total pore volumes of CCS-24, CCS-36, CCS-48, CCS-60 are 0.20, 0.27, 0.22 and 0.35 cm3 g−1, respectively. Comparing the specific surface area and total pore volume of CCS-48 and CCS-60, it is possible that with the increase of reaction time, some carbon nanospheres grow up and finally break down.
SEM and TEM are further used to characterize the morphology of materials. As presented in Figure 4a, the microstructure of CCS-24 sample is a large carbon block and a few spheres on the surface corresponding to the beginning of the carbon nanospheres formation after 24 h. Figure 4b shows a large number of carbon nanospheres with relatively uniform size and cross-linked structure, which is generated at 36 h. The cross-linked structure can shorten the distance between the lithium ion and electron, and thus improve the transmission efficiency. When the reaction time continued to increase, a large number of irregular-shaped carbon nanospheres generated together, as shown in Figure 4c,d. The occurrence of agglomeration will reduce the specific surface area of carbon materials, leading to the decrease of capacity. The TEM diagrams of CCS-24, CCS-36, CCS-48, CCS-60 are displayed in Figure 5. After comparison, it is observed that the hollow structure gradually formed, which is obvious with the increased reaction time. The hollow structure can reduce the structural damage caused by the intercalation of lithium ions and the collapse of the structure during the transmission process, thereby improving the cyclical stability of LIBs. In general, the formation of CCS occurs in the hydrothermal stage after 24 h, and the obtained carbon nanospheres possess a cross-linked structure. When the number of carbon nanospheres reached a certain level, the agglomeration appeared and became more and more serious over time.

3.3. Electrochemical Properties of CCS

The electrochemical cycling performance of CCS-24, CCS-36, CCS-48 and CCS-60 at 0.2C are compared in Figure 6a. After 100 cycles, the specific discharge capacities of samples are stable at 489, 577, 450 and 386 mA h g−1, respectively. After 100 cycles, the specific charge–discharge capacity increased from 24 h to 36 h. The specific charge–discharge capacity of CCS-36 remained at the highest level due to the favorable distribution and uniform size of carbon nanospheres, showing excellent battery-specific capacity and stable cycling performance. The specific charge and discharge capacity of CCS-48 and CCS-60 decreased gradually. Although the specific surface area and total pore volume of CCS-60 are larger than that of CCS-48, the pore size of CCS-60 is smaller than that of CCS-48, indicating that the size of the pore may have a greater effect on the capacity with a considerable increase in time. The charge–discharge curves of CCS samples do not coincide completely at the beginning of the first 10 cycles, while after 10 cycles, the charge–discharge curves basically coincide. This is due to the fact that lithium ions are used to form a solid electrolyte interfacial film (SEI) in the early charge–discharge stage, which causes the insertion and extraction of lithium ions in an unbalanced state. When a stable SEI film is formed, the insertion and extraction of lithium ions reach equilibrium state. To further evaluate the electrochemical performance of samples, the rate performance is also tested under various current densities (Figure 6b). After charge and discharge at the rate of 0.2, 0.5, 1, 2 and 5C, the specific capacities of the batteries almost returns to the initial one for the 0.2C rate. The unique spherical and cross-linked structures have shortened the transport distance between lithium ions and electrons and reduced the structural damage caused by the intercalation of lithium ions, leading to an excellent rate performance of anode materials.
Figure 7 displays the cyclic voltammogram curve of CCS-24, CCS-36, CCS-48, CCS-60 samples. The curves of the 2nd and 3rd laps basically coincide, which reflects the stability of electrochemical properties of CCS samples. During the first cycle of the CCS-36 sample, three reduction peaks appear near 0.2, 0.5 and 1.6 V. The peak near 0.2 V is formed due to lithium ion being embedded into the electrode material. The reduction peak near 0.5 V appears to be attributed to the catalytic reduction of electrolyte components on the surface of the active electrode to form SEI film. The reduction peak that appears near 1.6 V is considered to be caused by the reaction of lithium ion with the oxygen-containing functional group on the surface. In addition, there are two oxidation peaks near 0.25 V and 1.0 V. The flat oxidation peak at 0.25 V is corresponding to the extraction of lithium ions from the electrode. The hump at 1.0 V is formed by the adsorption and desorption of lithium ion in the mesopores of the material.
Figure 8 shows the charge–discharge curves of CCS-24, CCS-36, CCS-48, CCS-60 samples at 0.2C. The charge–discharge curve shows a weak discharge plateau near 0 V without another obvious charge–discharge plateau, which is a typical characteristic of the charge–discharge curve of carbon materials. In the first cycle, the specific discharge capacities of samples are 956, 1228, 1144 and 1285 mA h g−1, respectively. The coulombic efficiency of CCS-24, CCS-36, CCS-48 and CCS-60 are 48.1%, 51.0%, 53.1% and 45.4%, respectively. The coulombic efficiency of CCS samples is not particularly high, which is mainly determined by the characteristic of amorphous carbon. After the 100th cycle, the charge–discharge curves of the 2nd, 10th, 50th and 100th laps are basically coincidence, indicating that the unique spherical structure promotes the formation of stable SEI films to improve electrochemical stability. The impedance curve of samples CCS-24, CCS-36, CCS-48 and CCS-60 are shown in Figure 9. The semicircle diameter of CCS-36 is smaller than that of other samples, indicating that the charge transfer resistance is the smallest. This is due to the fact that the cross-linked structure and uniform distribution facilitate the transport of charge between the electrolyte and the interface of the material.
Table 1 shows biomass-derived carbons used as anodes in LIBs. From the comparison of different kinds of biomass as the electrode, it is clear that the structure of carbon materials and raw materials will lead to great differences in specific capacity. Table 2 presents the properties of different carbon nanospheres types. The structure and particle size of the carbon nanospheres have a great influence on the specific capacity. Although the experimental results of carbon materials prepared from corn straw have not been greatly improved due to the influence of the structure of raw materials, we still need to improve the experimental scheme and explore better preparation methods.

4. Conclusions

In summary, CCS is successfully synthesized through HTC from corn straw by carefully controlling the reaction time. Owing to the uniform distribution and cross-linked structure, CCS-36 has delivered excellent rate performance (577 mA h g−1 at 0.2C). When the current was restored to 0.2C again, the specific charge and discharge capacity quickly recovered to the initial value. Cellulose-derived carbon nanospheres provide more active sites for the intercalation of lithium ions by increasing the specific surface area, and thus, could further improve the specific capacity of LIBs. Meanwhile, the cross-linked structure not only shortens the distance between lithium ion and the electron, but also reduces the structural damage caused by the intercalation of lithium ions. In conclusion, we developed an environmental and efficient route to obtain cellulose-derived carbon nanospheres from corn straw, which not only realizes the secondary utilization of biomass waste, but also opens up a new opportunity for LIBs anodes.

Author Contributions

Methodology, K.Y. and Y.D.; formal analysis, J.W.; investigation, J.W., K.S. and X.W.; writing—original draft preparation, J.W.; writing—review and editing, C.L.

Funding

This research was funded by National Science Foundation of China (51275203), the Key Scientific and Technological Project of Jilin Province (20140204052GX, 20180201074GX), the China Postdoctoral Science Foundation (2017M611321), the Project of Education Department of Jilin Province (JJKH20180130KJ) and Open Project of State Key Laboratory of Inorganic Synthesis and Preparative Chemistry, College of Chemistry, Jilin University (2019-8).

Acknowledgments

The authors wish to express their gratitude for the support from National Natural Science Foundation of China, China Postdoctoral Science Foundation and support from Jilin Provincial Science and Technology Department, Jilin Provincial Education Department.

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Chen, F.; Yang, J.; Bai, T.; Long, B.; Zhou, X. Biomass waste-derived honeycomb-like nitrogen and oxygen dual-doped porous carbon for high performance lithium-sulfur batteries. Electrochim. Acta 2016, 192, 99–109. [Google Scholar] [CrossRef]
  2. Lee, J.; Kim, J.; Hyeon, T. Recent progress in the synthesis of porous carbon materials. Adv. Mater. 2006, 18, 2073–2094. [Google Scholar] [CrossRef]
  3. Gao, Y.; Chen, H.; Wang, J.; Shi, T.; Yang, H.; Wang, X. Characterization of products from hydrothermal liquefaction and carbonation of biomass model compounds and real biomass. J. Fuel Technol. 2011, 39, 893–900. [Google Scholar] [CrossRef]
  4. Xia, Y.; Mokaya, R. Ordered mesoporous carbon hollow spheres nanocast using mesoporous silica via chemical vapor deposition. Adv. Mater. 2004, 16, 886–891. [Google Scholar] [CrossRef]
  5. Harris, P.J.F. New perspectives on the structure of graphitic carbons. Crit. Rev. Solid State Mater. Sci. 2005, 30, 235–253. [Google Scholar] [CrossRef]
  6. Le Van, K.; Luong, T.T.T. Activated carbon derived from rice husk by NaOH activation and its application in supercapacitor. Prog. Nat. Sci. Mater. Int. 2014, 24, 191. [Google Scholar] [CrossRef]
  7. Zhang, Y.; Yang, S.; Wu, J.Q.; Yuan, T.Q.; Sun, R.C. Preparation and characterization of lignocellulosic oil sorbent by hydrothermal treatment of populus fiber. Materials 2014, 7, 6733–6747. [Google Scholar] [CrossRef]
  8. Kumar, S.; Kothari, U.; Kong, L.; Lee, Y.Y.; Gupta, R.B. Hydrothermal pretreatment of switchgrass and corn stover for production of ethanol and carbon microspheres. Biomass Bioenergy 2011, 35, 956–968. [Google Scholar] [CrossRef]
  9. Huang, X.; Kim, S.; Heo, M.S.; Kim, J.E.; Suh, H.; Kim, I. Easy synthesis of hierarchical carbon spheres with superior capacitive performance in supercapacitors. Langmui 2013, 29, 12266–12274. [Google Scholar] [CrossRef]
  10. Liu, F.; Chen, Y.; Gao, J. Preparation and characterization of biobased graphene from kraft lignin. Bio Resour. 2017, 12, 6545–6557. [Google Scholar] [CrossRef]
  11. Kim, D.; Yoshikawa, K.; Park, K.Y. Characteristics of biochar obtained by hydrothermal carbonization of cellulose for renewable energy. Energies 2015, 8, 14040–14048. [Google Scholar] [CrossRef]
  12. Liu, H.J.; Cui, W.J.; Jin, L.H.; Wang, C.X.; Xia, Y.Y. Preparation of three-dimensional ordered mesoporous carbon sphere arrays by a two-step templating route and their application for supercapacitors. J. Mater. Chem. 2009, 19, 3661–3667. [Google Scholar] [CrossRef]
  13. Ferrero, G.A.; Fuertes, A.B.; Sevilla, M. N-doped microporous carbon microspheres for high volumetric performance supercapacitors. Electrochim. Acta 2015, 168, 320–329. [Google Scholar] [CrossRef] [Green Version]
  14. Gu, W.; Yushin, G. Review of nanostructured carbon materials for electrochemical capacitor applications: Advantages and limitations of activated carbon, carbide-derived carbon, zeolite-templated carbon, carbon aerogels, carbon nanotubes, onion-like carbon, and grapheme. WIREs Energy Environ. 2014, 3, 424–473. [Google Scholar] [CrossRef]
  15. Li, Y.; Li, C.; Qi, H.; Yu, K.F.; Li, X. Formation mechanism and characterization of porous biomass carbon for excellent performance lithium-ion batteries. RSC Adv. 2018, 8, 12666–12671. [Google Scholar] [CrossRef] [Green Version]
  16. Sevilla, M.; Fuertes, A.B. The production of carbon materials by hydrothermal carbonization of cellulose. Carbon 2009, 47, 2281–2289. [Google Scholar] [CrossRef] [Green Version]
  17. Sevilla, M.; Fuertes, A.B.; Mokaya, R. High density hydrogen storage in superactivated carbons from hydrothermally carbonized renewable organic materials. Energy Environ. Sci. 2011, 4, 1400–1410. [Google Scholar] [CrossRef]
  18. Sevilla, M.; Fuertes, A.B. Graphitic carbon nanostructures from cellulose. Chem. Phys. Lett. 2010, 490, 63–68. [Google Scholar] [CrossRef] [Green Version]
  19. Sevilla, M.; Maciá-Agulló, J.A.; Fuertes, A.B. Hydrothermal carbonization of biomass as a route for the sequestration of CO2: Chemical and structural properties of the carbonized products. Biomass Bioenergy 2011, 35, 3152–3159. [Google Scholar] [CrossRef]
  20. Falco, C.; Sieben, J.M.; Brun, N.; Sevilla, M.; van der Mauelen, T.; Morallón, E.; Cazorla-Amorós, D.; Titirici, M. Hydrothermal carbons from hemicellulose-derived aqueous hydrolysis products as electrode materials for supercapacitors. ChemSusChem 2013, 6, 374–382. [Google Scholar] [CrossRef]
  21. Zheng, G.; Lee, S.W.; Liang, Z.; Lee, H.-W.; Yan, K.; Yao, H.; Wang, H.; Li, W.; Chu, S.; Cui, Y. Interconnected hollow carbon nanospheres for stable lithium metal anodes. Nat. Nanotechnol. 2014, 9, 618–623. [Google Scholar] [CrossRef] [PubMed]
  22. Caballero, A.; Hernan, L.; Morales, J. Limitations of disordered carbons obtained from biomass as anodes for real lithium-ion batteries. Chemsuschem. 2011, 4, 658–1633. [Google Scholar] [CrossRef] [PubMed]
  23. Libra, J.A.; Ro, K.S.; Kammann, C.; Funke, A.; Berge, N.D.; Neubauer, Y.; Titirici, M.-M.; Fuhner, C.; Bens, O.; Kern, J.; et al. Hydrothermal carbonization of biomass residuals: A comparative review of the chemistry, processes and applications of wet and dry pyrolysis. Biofuels 2011, 2, 71–106. [Google Scholar] [CrossRef]
  24. Wang, J.; Feng, S.; Song, Y.; Li, W.; Gao, W.; Elzatahry, A.A.; Aldhayan, D.; Xia, Y.; Zhao, D. Synthesis of hierarchically porous carbon spheres with yolk-shell structure for high performance supercapacitors. Catal. Today 2015, 243, 199–208. [Google Scholar] [CrossRef]
  25. Zhao, Y.; Li, W.; Zhao, X.; Wang, D.P.; Liu, S.X. Carbon spheres obtained via citric acid catalysed hydrothermal carbonisation of cellulose. Mater. Res. 2013, 17, 546–551. [Google Scholar] [CrossRef]
  26. Hao, Z.Q.; Cao, J.P.; Wu, Y.; Zhao, X.Y.; Zhuang, Q.Q.; Wang, X.Y.; Wei, X.Y. Preparation of porous carbon sphere from waste sugar solution for electric double-layer capacitor. J. Power Sources 2017, 361, 249–258. [Google Scholar] [CrossRef]
  27. Inada, M.; Enomoto, N.; Hojo, J.; Hayashi, K. Structural analysis and capacitive properties of carbon spheres prepared by hydrothermal carbonization. Adv. Powder Technol. 2017, 28, 884–889. [Google Scholar] [CrossRef]
  28. Xie, L.; Li, X.F.; Deng, J.; Gong, Y.T.; Wang, H.T.; Mao, S.J.; Wang, Y. Sustainable and scalable synthesis of monodisperse carbon nanospheres and their derived superstructures. Green Chem. 2018, 20, 4596. [Google Scholar] [CrossRef]
  29. Chowdhury, Z.Z.; Hamid, S.B.A.; Rahman, M.M.; Rafique, R.F. Catalytic activation and application of micro-spherical carbon derived from hydrothermal carbonization of lignocellulosic biomass: Statistical analysis using box-behnken design. RSC Adv. 2016, 6, 102680–102694. [Google Scholar] [CrossRef]
  30. Sun, X.; Li, Y. Colloidal carbon spheres and their core/shell structures with noble-metal nanoparticles. Angew. Chem. 2004, 43, 597–601. [Google Scholar] [CrossRef]
  31. Li, Q.; Jiang, R.; Dou, Y.; Wu, Z.; Huang, T.; Feng, D.; Yang, J.; Yu, A.; Zhao, D. Synthesis of mesoporous carbon spheres with a hierarchical pore structure for the electrochemical double-layer capacitor. Carbon 2011, 49, 1248–1257. [Google Scholar] [CrossRef]
  32. Wang, Z.L.; Kang, Z.C. Graphitic structure and surface chemical activity of nanosize carbon spheres. Carbon 1997, 35, 419–426. [Google Scholar] [CrossRef] [Green Version]
  33. Lou, X.W.; Li, C.M.; Archer, L.A. Designed synthesis of coaxial SnO2@carbon hollow nanospheres for highly reversible lithium storage. Adv. Mater. 2009, 21, 2536–2539. [Google Scholar] [CrossRef]
  34. Pang, J.; Zhang, W.; Zhang, H.; Zhang, J.; Zhang, H.; Cao, G. Sustainable nitrogen-containing hierarchical porous carbon spheres derived from sodium lignosulfonate for high-performance supercapacitors. Carbon 2018, 132, 280–293. [Google Scholar] [CrossRef]
  35. Liu, S.; Zhao, Y.; Zhang, B.; Xia, H.; Zhou, J.; Xie, W. Nano-micro carbon spheres anchored on porous carbon derived from dual-biomass as high rate performance supercapacitor electrodes. J. Power Sources 2018, 381, 116–126. [Google Scholar] [CrossRef]
  36. Li, S.; Liang, F.; Wang, J.; Zhang, H.; Zhang, S. Preparation of mono-dispersed carbonaceous spheres via hydrothermal process. Adv. Powder Technol. 2017, 28, 2648–2657. [Google Scholar] [CrossRef]
  37. Liu, L.; Yang, L.; Wang, P.; Wang, C.Y.; Cheng, J.; Zhang, G. Porous nitrogen-doped carbon derived from peanut shell as anode material for lithium ion battery. Int. J. Electrochem. Sci. 2017, 12, 9844–9854. [Google Scholar] [CrossRef]
  38. Titirici, M.M.; Thomas, A.; Yu, S.H.; Müller, J.; Antonietti, M. A direct synthesis of mesoporous carbons with bi-continuous pore morphology from crude plant material by hydrothermal carbonization. Chem. Mater. 2007, 19, 4205–4212. [Google Scholar] [CrossRef]
  39. Titirici, M.M.; Antonietti, M.; Baccile, N. Hydrothermal carbon from biomass: A comparison of the local structure from poly-to monosaccharides and pentoses/hexoses. Green Chem. 2008, 10, 1204–1212. [Google Scholar] [CrossRef]
  40. Bian, X.; Zhu, J.; Liao, L.; Scanlon, M.D.; Ge, P.; Ji, C.; Girault, H.H.; Liu, B. Nanocomposite of MoS2 on ordered mesoporous carbon nanospheres: A highly active catalyst for electrochemical hydrogen evolution. Electrochem. Commun. 2012, 22, 128–132. [Google Scholar] [CrossRef]
  41. Luna-Lama, F.; Puente-Santiago, A.R.; Caballero, A.; Balu, A.M.; Romero, A.A. Non-porous carbonaceous materials derived from coffee waste grounds as highly sustainable anodes for lithium-ion batteries. J. Clean. Prod. 2019, 207, e417. [Google Scholar] [CrossRef]
  42. Yu, X.L.; Zhang, K.Y.; Tian, N.; Qin, A.M.; Liao, L.; Du, R.; Wei, C. Biomass carbon derived from sisal fiber as anode material for lithium-ion batteries. Mater. Lett. 2015, 142, 193–196. [Google Scholar] [CrossRef]
  43. Wu, L.M.; Buchholz, D.; Vaalma, C.; Giffin, G.A.; Passerini, S. Apple-biowaste-derived hard carbon as a powerful anode material for Na-ion batteries. Chem. Electr. Chem. 2016, 3, 292–298. [Google Scholar] [CrossRef]
  44. Arrebola, J.C.; Caballero, A.; Hernan, L.; Morales, J.; Marin, M.O.; Serrano, V.G. Improving the performance of biomass-derived carbons in li-ion batteries by controlling the lithium insertion process. J. Electrochem. Soc. 2010, 157, A791–A797. [Google Scholar] [CrossRef]
  45. Stephan, A.M.; Kumar, T.P.; Ramesh, R.; Thomas, S.; Jeong, S.K.; Nahm, K.S. Pyrolitic carbon from biomass precursors as anode materials for lithium batteries. Mater. Sci. Eng. A 2006, 430, 132–137. [Google Scholar] [CrossRef]
  46. Yu, K.F.; Li, J.; Qi, H.; Liang, C. Cellulose-derived hollow carbonaceous nanospheres from rice husks as anode for lithium-ion batteries with enhanced reversible capacity and cyclic performance. Chem. Select. 2017, 2, 3627–3632. [Google Scholar] [CrossRef]
  47. Liu, S.G.; Mao, C.P.; Wang, L.; Jia, M.; Sun, Q.Q.; Liu, Y.; Xu, M.W.; Lu, Z.S. Bio-inspired synthesis of carbon hollow microspheres from a spergillus flavus conidia for lithium-ion batteries. RSC Adv. 2015, 5, 59655. [Google Scholar] [CrossRef]
  48. Zang, J.; Ye, J.C.; Fang, X.L.; Zhang, X.W.; Zheng, M.S.; Dong, Q.F. Hollow-in-hollow carbon spheres for lithium-ion batteries with superior capacity and cyclic performance. Electrochim. Acta 2015, 186, 436–441. [Google Scholar] [CrossRef]
  49. Xu, S.T.; Zhang, Z.F.; Wu, T.Y.; Xue, Y. Nanoporous carbon microspheres as anode material for enhanced capacity of lithium ion batteries. Ionics 2018, 24, 99–109. [Google Scholar] [CrossRef]
Nanomaterials 09 00093 g001 550
Figure 1. Schematic illustration of the CCS preparation.
Figure 1. Schematic illustration of the CCS preparation.
Nanomaterials 09 00093 g001
Nanomaterials 09 00093 g002 550
Figure 2. (a) XRD patterns and (b) Raman spectrum of CCS-24, CCS-36, CCS-48 and CCS-60 samples; (c) TG curve of corn straw.
Figure 2. (a) XRD patterns and (b) Raman spectrum of CCS-24, CCS-36, CCS-48 and CCS-60 samples; (c) TG curve of corn straw.
Nanomaterials 09 00093 g002
Nanomaterials 09 00093 g003 550
Figure 3. (a) Nitrogen adsorption–desorption isotherms and (b) pore sizes distribution of CCS-24, CCS-36, CCS-48 and CCS-60 samples.
Figure 3. (a) Nitrogen adsorption–desorption isotherms and (b) pore sizes distribution of CCS-24, CCS-36, CCS-48 and CCS-60 samples.
Nanomaterials 09 00093 g003
Nanomaterials 09 00093 g004 550
Figure 4. SEM images of (a) CCS-24, (b) CCS-36, (c) CCS-48, and (d) CCS-60 samples.
Figure 4. SEM images of (a) CCS-24, (b) CCS-36, (c) CCS-48, and (d) CCS-60 samples.
Nanomaterials 09 00093 g004
Nanomaterials 09 00093 g005 550
Figure 5. TEM images of (a) CCS-24, (b) CCS-36, (c) CCS-48, and (d) CCS-60 samples.
Figure 5. TEM images of (a) CCS-24, (b) CCS-36, (c) CCS-48, and (d) CCS-60 samples.
Nanomaterials 09 00093 g005
Nanomaterials 09 00093 g006 550
Figure 6. (a) Cycling performance of CCS samples at 0.2C and (b) rate performance of CCS samples.
Figure 6. (a) Cycling performance of CCS samples at 0.2C and (b) rate performance of CCS samples.
Nanomaterials 09 00093 g006
Nanomaterials 09 00093 g007 550
Figure 7. Cyclic Voltammograms of (a) CCS-24, (b) CCS-36, (c) CCS-48 and (d) CCS-60 samples.
Figure 7. Cyclic Voltammograms of (a) CCS-24, (b) CCS-36, (c) CCS-48 and (d) CCS-60 samples.
Nanomaterials 09 00093 g007
Nanomaterials 09 00093 g008 550
Figure 8. Charge-discharge curves of (a) CCS-24, (b) CCS-36, (c) CCS-48, and (d) CCS-60 samples.
Figure 8. Charge-discharge curves of (a) CCS-24, (b) CCS-36, (c) CCS-48, and (d) CCS-60 samples.
Nanomaterials 09 00093 g008
Nanomaterials 09 00093 g009 550
Figure 9. The impedance curves of CCS-24, CCS-36, CCS-48 and CCS-60 samples.
Figure 9. The impedance curves of CCS-24, CCS-36, CCS-48 and CCS-60 samples.
Nanomaterials 09 00093 g009
Table
Table 1. Biomass-derived carbons used as anodes in LIBs.
Table 1. Biomass-derived carbons used as anodes in LIBs.
MaterialC RateSpecific Capacity/ mA h g−1Reference
Porous carbon from peanut shell0.1180[37]
Carbon particle from coffee waste0.27285[41]
Honeycomb carbon from sisal fiber0.1530[42]
Carbon particle from apple waste0.1245[43]
Carbon from cherry stones5200[44]
Carbon sheet from banana fiber0.1310[45]
Table
Table 2. Performance comparison of different carbon nanospheres.
Table 2. Performance comparison of different carbon nanospheres.
Carbon Nanospheres TypeParticle Size/nmSpecific Area/m2 g−1C RateSpecific Capacity/mA h g−1Reference
Hollow nanospheres50–150369.440.2489[46]
Hollow microspheres1000–3000309.90.27475[47]
Hollow-in-hollow3501190.10.27973[48]
Nanoporous microspheres7002798.91.08780[49]

Share and Cite

MDPI and ACS Style

Yu, K.; Wang, J.; Song, K.; Wang, X.; Liang, C.; Dou, Y. Hydrothermal Synthesis of Cellulose-Derived Carbon Nanospheres from Corn Straw as Anode Materials for Lithium ion Batteries. Nanomaterials 2019, 9, 93. https://doi.org/10.3390/nano9010093

AMA Style

Yu K, Wang J, Song K, Wang X, Liang C, Dou Y. Hydrothermal Synthesis of Cellulose-Derived Carbon Nanospheres from Corn Straw as Anode Materials for Lithium ion Batteries. Nanomaterials. 2019; 9(1):93. https://doi.org/10.3390/nano9010093

Chicago/Turabian Style

Yu, Kaifeng, Jingjing Wang, Kexian Song, Xiaofeng Wang, Ce Liang, and Yanli Dou. 2019. "Hydrothermal Synthesis of Cellulose-Derived Carbon Nanospheres from Corn Straw as Anode Materials for Lithium ion Batteries" Nanomaterials 9, no. 1: 93. https://doi.org/10.3390/nano9010093

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop