Next Article in Journal
Observation of Cu Spin Fluctuations in High-Tc Cuprate Superconductor Nanoparticles Investigated by Muon Spin Relaxation
Next Article in Special Issue
Process Optimization for Manufacturing Functional Nanosurfaces by Roll-to-Roll Nanoimprint Lithography
Previous Article in Journal
The Effect of Silicon Grade and Electrode Architecture on the Performance of Advanced Anodes for Next Generation Lithium-Ion Cells
Previous Article in Special Issue
Degradation of Acid Red 1 Catalyzed by Peroxidase Activity of Iron Oxide Nanoparticles and Detected by SERS
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Nanomaterials
Volume 11
Issue 12
10.3390/nano11123449
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

Ti3Si0.75Al0.25C2 Nanosheets as Promising Anode Material for Li-Ion Batteries

by
Jianguang Xu
*,
Qiang Wang
,
Boman Li
,
Wei Yao
and
Meng He
*
School of Materials Science and Engineering, Yancheng Institute of Technology, Yancheng 224051, China
*
Authors to whom correspondence should be addressed.
Nanomaterials 2021, 11(12), 3449; https://doi.org/10.3390/nano11123449
Submission received: 27 November 2021 / Revised: 15 December 2021 / Accepted: 17 December 2021 / Published: 20 December 2021
(This article belongs to the Special Issue Nanotechnologies and Nanomaterials: Selected Papers from CCMR)
Browse Figures
Versions Notes

Abstract

:
Herein we report that novel two-dimensional (2D) Ti3Si0.75Al0.25C2 (TSAC) nanosheets, obtained by sonically exfoliating their bulk counterpart in alcohol, performs promising electrochemical activities in a reversible lithiation and delithiation procedure. The as-exfoliated 2D TSAC nanosheets show significantly enhanced lithium-ion uptake capability in comparison with their bulk counterpart, with a high capacity of ≈350 mAh g−1 at 200 mA g−1, high cycling stability and excellent rate performance (150 mAh g−1 after 200 cycles at 8000 mA g−1). The enhanced electrochemical performance of TSAC nanosheets is mainly a result of their fast Li-ion transport, large surface area and small charge transfer resistance. The discovery in this work highlights the uniqueness of a family of 2D layered MAX materials, such as Ti3GeC2, Ti3SnC2 and Ti2SC, which will likely be the promising choices as anode materials for lithium-ion batteries (LIBs).

1. Introduction

Since they were first reported, lamellar ternary carbides and nitrides have been named “MAX phases” or “Mn+1AXn phases (n = 1, 2 or 3)”, where M represents an early transition metal, A is an element of ⅢA to VIA groups and X is carbon or nitrogen. They have attracted great attention because of their special combination of metallic and ceramic properties [1]. For example, due to their inherent layered structure with alternately arranged MX and A layers, the MAX phases display a superior resistance to oxidation, thermal energy and corrosion, very good electrical conductivity, high strength and elastic modulus and excellent machinability [2,3,4,5,6]. Owing to their lamellar structure and excellent conductivity, MAX phases show great potential in lithium-ions storage for a Li-ion battery (LIB) or capacitor [7,8,9,10,11,12,13,14]. However, the reported capacities of MAX phases are relatively low, particularly in the initial few charge–discharge cycles, which may restrict their real application in LIB. Thus, it is important to optimize the lithium-ion uptake property of MAX phases. It has been well accepted that the nanoscale materials, particularly the ultrathin two-dimensional (2D) nanosheets, have improved properties compared to their corresponding bulk counterparts [15,16,17,18]. For instance, the reversible capacity of free-standing graphene nanosheet (GNS) was found to be 540 mAh g−1 [19], and that of N-GNS even reached a high value of 684 mAh g−1 [20], both of which are over the theoretical reversible capacity of graphite. In that case, it is anticipated that MAX nanosheets can exhibit an enhanced lithium-ion storage property compared to their bulk materials.
Unfortunately, unlike the inorganic graphene analog (IGA) with weak van der Waals force between its layers, the MAX phases have relatively robust connections between the MX and A layers, and it seems difficult to exfoliate the bulk MAX materials into ultrathin nanosheets by a facile sonic exfoliation process [21]. Particularly, most of the Ti3SiC2 and Ti2SC particles were broken into small species instead of being delaminated to ultrathin nanosheets by increasing the power of sonication [10]. To overcome this limitation, we developed an available substitutional-solid-solution-based exfoliation process for the large-scale fabrication of ultrathin nanosheets of A-layer-activated MAX phases. As a result, ultrathin Ti3Si0.75Al0.25C2 (TSAC) nanosheets with a very thin thickness of 4 nm were prepared based on this strategy, which can be used as a promising filler for polymer composites [22,23].
Herein, we extend the application of these TSAC nanosheets to the electrode for LIBs because the size and morphology of MAX phases promise improvements on their electrochemical performance for LIBs [9,10,11]. The Ti3Si0.75Al0.25C2 nanosheets have very thin thickness, so it can be expected that Li ions can easily be intercalated into the TSAC nanosheets layers. In addition, the electrical conductivity of a MAX phase is normally higher than its MXene counterpart, which usually has excellent conductivity [24], because the A-group layer increases the metallic properties of the material for the improvement of their overall electrochemical properties [1]. Hence, per the diagram in Figure 1, combining the large surface area and excellent conductivity with Ti3Si0.75Al0.25C2 nanosheets, high performance can be anticipated for the Ti3Si0.75Al0.25C2 nanosheets electrode.

2. Experimental Section

2.1. Materials

Titanium powder (300 mesh, 99.9 wt.%) was purchased from Guangzhou metallurgy (Guangzhou, China). Silicon powder (200 mesh, 99.0 wt.%), aluminum (Al) powder (200 mesh, 99.0 wt.%), graphite powder (30 μm, 99.85 wt.%) and absolute alcohol (AR) were purchased from Sinopharm (Shanghai, China).

2.2. Preparation of Ti3Si0.75Al0.25C2 Powder

The Ti3Si0.75Al0.25C2 powder (bulk TSAC) was synthesized via a self-propagation high-temperature synthesis (SHS) process. In detail, 14.3 g Ti powder, 4.21 g Si powder, 0.68 g Al powder and 2.4 g graphite powder were blended using a QM-BP Ball Mill at 300 rpm for 2 h, in which the molar ratio of Ti: Si: Al: C was about 3:1.5:0.25:2. The as-received mixture was then put into a self-propagation high-temperature reactor, and then ignited by a tungsten filament under the protection of pure Ar gas. After combustion, a gray product was collected for further processing. The atomic ratio of the Ti, Si, Al and C of the as-received powder is about 3:0.75:0.25:2, which was determined by X-ray fluorescence spectroscopy (XRF) in our previous work [22].

2.3. Preparation of Ultrathin Ti3Si0.75Al0.25C2 Nanosheets

The Ti3Si0.75Al0.25C2 nanosheets (TSAC nanosheets) were obtained by the liquid exfoliation of TSAC powder in absolute alcohol via sonication. In detail, 2 g bulk TSAC powder was dispersed in 0.2 L absolute alcohol, and then sonicated for 24 h. After sonication, the resulting dispersion liquid was then centrifuged at 2000 rpm for 20 min to remove most residual large-size particles. Finally, TSAC nanosheets were dried and collected for the following tests through vacuum filtration of the resulting supernatant.

2.4. Preparation of Electrodes

The electrochemical behaviors of TSAC nanosheets and bulk TSAC were studied using CR-2032 coin-cell with lithium metal as the counter electrode and reference electrode. The batteries were based on Li metal (−) | | TSAC (+) with liquid electrolyte (1M solution of LiPF6 in ethyl carbonate (EC)-dimethyl carbonate (DMC)-ethyl methyl carbonate (EMC) (1:1:1, v/v/v)). Microporous polypropylene membrane (Celgard2500) was used as a separator. Next, 80 wt.% TSAC nanosheets or bulk TSAC, 10 wt.% acetylene black and 10 wt.% polyvinylidene fluoride (PVDF) were dispersed in N-methylpyrrolidone (NMP) and uniformly mixed into a viscous slurry. Then, the slurry was deposited on a copper foil current collector. The electrodes were then vacuum dried for 12 h at 120 °C, followed by electrochemical evaluation. The loading of active material was about 0.65~0.85 mg cm−2. Finally, the cells were assembled in a glove box filled with 99.99 wt.% Ar gas.

2.5. Characterization

The TSAC powder was characterized by X-ray powder diffraction (XRD) with a Japan Rigaku Dmax X-ray diffractometer (Tokyo, Japan) equipped with graphite monochromatized high-intensity Cu-Kα radiation (λ = 1.54178 Å). The field emission scanning electron microscopy (FE-SEM) images were performed using a FEI Nova NanoSEM 450 scanning electron microscope (Hillsboro, OR, USA). The transmission electron microscopy (TEM) images were taken on a JEM-2100F field emission electron microscope (Tokyo, Japan) with X-MaxN 80T IE250 Energy Disperse Spectroscopy (UK). The Brunauer–Emmett–Teller (BET) specific surface areas of the samples were determined using a Micromeritics TriStar II 3020 system (Norcross, GA, USA). X-ray photoelectron spectroscopy (XPS, Thermo Fisher ESCALAB 250Xi, Waltham, MA, USA) was utilized to explore the electron-binding energy of TSAC nanosheets. The Raman spectra of the samples were recorded by a Renishaw inVia Reflex system (Gloucestershire, UK) equipped with an argon ion Laser with a wavelength of 633 nm. The cells were charged and discharged galvanostatically in a fixed voltage window from 0.001 to 3 V on a Shenzhen Neware battery cycler (Shenzhen, China) at room temperature. All the gravimetric capacity data related to as-prepared samples were based on the mass of TSAC nanosheets or bulk TSAC. Cyclic voltammetry and electrochemical impedance spectroscopy (EIS, frequency range: 0.1–105 Hz, amplitude: 5 mV) analysis were carried out by a Zahner-Zennium electrochemical workstation (Kronach, Germany).

3. Results and Discussion

The feasibility of using bulk TSAC and exfoliated TSAC nanosheets as electrodes for LIBs was investigated. The XRD pattern and SEM image of a bulk TSAC are shown in Figure 2. The primary phase of this product is very close to the pattern of Ti3SiC2 (JCPDS card No. 89-1356). A small blue shift also appears (Figure 2a), indicating the formation of a solid solution Ti3Si0.75Al0.25C, as discussed in our previous work [22]. In addition, a small amount of TiC is also found in the XRD pattern of bulk TSAC, in most situations which is generated with the formation of Ti3SiC2 [25]. The micrograph of the product (Figure 2b) shows a distinct lamellar structure, which is in agreement with the crystal structure of Ti3SiC2. As shown in Figure 1, the crystal structure of Ti3SiC2 is composed of Ti3C2 layer and Si layer along c-direction. Because the connection between the Ti3C2 layer and the Si layer is relatively low and can be exfoliated, Ti3SiC2 and other MAX phase compounds generally display a lamellar appearance.
The microstructure of the TSAC nanosheets is shown in Figure 3. The sample exhibits a sheet-like morphology with a size from around 100 to 1000 nm. According to a TEM image of the nanosheets (Figure 3b), most of them exhibit ultrathin sheet-like structures, which render them transparent or semitransparent. Moreover, it could be detected from a magnified nanosheet in Figure 3c that TSAC nanosheets are composed of only a few layers, indicating that bulk TSAC has been delaminated successfully and the crystal structure of Ti3Si0.75Al0.25C2 (inserted in Figure 3c) is well maintained during sonication. The BET results further confirmed the exfoliated sheet-like structure. Compared with the bulk TSAC, the specific surface area (SSA) of the TSAC nanosheets increased from 4.25 m2 g−1 to 11.68 m2 g−1. In addition, on the basis of EDX analysis in Figure 3d, the atomic ratios of Ti:(Si + Al):C and Si:Al are close to 3:1:2 and 3:1, respectively, suggesting that the composition of Ti3Si0.75Al0.25C2 particles has no obvious change after delamination.
Figure 4a–e show the high resolution XPS spectra of TSAC nanosheets. The XPS spectra of Ti 2p and C 1s are similar to those spectra of Ti3C2 MXene [24,26,27], which also includes Ti–C, Ti–O, TiO2, C–C, C–O and O–C=O bonds, indicating both Ti3C2 and TSAC nanosheets have similar intralayer and surface structure of MX layer. In addition, based on the existence of Ti–O, C–O, Si–O and Al–O bonds [28], it can be deduced there is an oxide layer covered on the surface of TSAC nanosheets, which is in agreement with previous reports of MAX phases [28]. In the spectra of Si 2p and Al 2p in Figure 4b,c, Si metal and Al metal bonds are detected [29], suggesting weak connections between the MX layer and the A layer in TSAC MAX phase nanosheets. Thus, bulk TSAC particles have the possibility to be exfoliated into thin nanosheets. The Raman spectra of bulk TSAC and TSAC nanosheets in Figure 4f further proved the layered structure of TSAC MAX phase, because both samples show distinct Raman peaks of Ti3SiC2 as in previous reports [30,31]. After delamination, these peaks of the received TSAC nanosheets exhibit small red shifts, which may be caused by the expanding crystal structure of the MAX phase [10]. Hence, by combining the results of SEM, TEM, XPS and Raman of TSAC nanosheets, it can be concluded that the exfoliated products are mainly composed of Ti3Si0.75Al0.25C2 phase and the layered structure of Ti3Si0.75Al0.25C2 phase has been well maintained during sonication.
The cyclic voltammetry (CV) and galvanostatic charge–discharge cycling (GV) of bulk TSAC and TSAC nanosheets were tested in this work. In Figure 5a,b, both TSAC nanosheets and bulk TSAC exhibit similar CV behaviors, except there is an additional cathodic peak of TSAC nanosheets around 2.4 V, showing that the exfoliated TSAC nanosheets perform a special Li+ deintercalation process. During the first reduction process of both electrodes, there is an obvious peak located at about 1.2 V associated with the generation of a solid electrolyte interphase (SEI) film [32]. This peak then practically disappears during the following reduction process, which can be ascribed to the isolation between the TSAC anode and electrolyte by the dense SEI film formed on the surface of the TSAC anode in the first reduction process. Then, a peak around 0.75 V is detected and kept at the following cycles, where the reaction of Li+ with TSAC nanosheets such as Ti3C2 probably occurs [32]. In the following cycles, two broad redox reversible peaks at 1.8 and 2.4 V corresponding to the reaction between Li+ and titanium oxide on the surface of TSAC nanosheets appear, because similar pairs were also observed in Ti2C and Ti3C2 nanosheets [32,33,34,35]. Interestingly, during the second and third cycles of TSAC nanosheets, a small cathodic peak at 0.1 V and two anodic peaks at 0.15 and 0.5 V can be observed, probably corresponding to lithiation process of Si and delithiation of LixSi [36]. Meanwhile, for bulk TSAC, these redox peaks are not obvious because there are less exposed Si atoms in bulk TSAC particles. This alloying procedure of exposed “A” layer of MAX phases is also found in those Sn-containing MAX phases, such as Ti2SnC, Nb2SnC and V2SnC [7,8,9]. In addition, the differences in the CV profiles between these initial two cycles and the similarity in the second and the third cycles indicates that the irreversible capacity losses of TSAC nanosheets and bulk TSAC mainly take place in the first cycle.
The CV profiles of TSAC nanosheets in Figure 5a also show no obvious charge and discharge capacity at potential higher than 3 V vs. Li/Li+. Thus, the lithium-ion storage tests for TSAC were performed from 0.001 to 3 V. The voltage profile for TSAC nanosheets at 80 mA g−1 (Figure 6a) delivers a beginning charge capacity (lithiation) of 862 mAh g−1. This capacity is much bigger than that of bulk TSAC with only 215 mAh g−1 (Figure 6b). It can also be detected from the charge profile in Figure 6a that more than three-quarters of the capacity are under 1.5 V, indicating that TSAC nanosheets could function better as anode materials for LIBs. Figure 6c shows the lithium-ion storage behavior of bulk TSAC and TSAC nanosheets with charge/discharge cycles at 200 mA g−1. The coulomb efficiency of TSAC nanosheets at the first cycle is 47.2%, which then increases rapidly and reaches 93.1% at the fifth cycle. The reason for the irreversibility in the initial cycles could be attributed to the formation of solid electrolyte interphase (SEI) or because of some irreversible reactions of Li ions with the surface groups and/or water molecules in TSAC nanosheets. On the whole, this irreversibility could be minimized by tailoring the surface structure of TSAC nanosheets or by prelithiating the electrode material as mentioned in other materials [37]. Then the reversible performance becomes stable after the first few lithiation/delithiation cycles. A stable cycle capacity of TSAC nanosheets is around 350 mAh g−1 at a current density of 200 mA g−1 and higher than the maximum theoretical capacity of f-Ti3C2 predicted by Tang et al. [38]. In addition, TSAC nanosheets show very good reversibility and stability, and a reversible capacity of 350 mAh g−1 is still kept after 100 cycles while it is only around 70 mAh g−1 for bulk TSAC.
Rate-capability tests were also performed to further assess the electrochemical activities of TSAC nanosheets. As shown in Figure 6d, both TSAC nanosheets and bulk TSAC anodes manifest excellent cycling stability at various current densities. After 10 cycles at 80, 200, 400, 800, 1600 and 4000 mA g−1, TSAC nanosheets deliver delithiation capacities of 410, 353, 312, 279, 240 and 181 mAh g−1, while that of bulk TSAC is only 108, 85, 80, 62, 46 and 26 mAh g−1, respectively, suggesting a better rate performance for TSAC nanosheets at various rates. Even at a high rate of 8000 mA g−1, the TSAC nanosheets anode is capable of maintaining a discharge capacity of 150 mAh g−1 after 200 cycles (Figure 7a), which equals to that of the third cycle. In addition, the coulombic efficiency of TSAC nanosheets at 8000 mA g−1 is between 98–100% after the first five cycles, indicating a relatively stable SEI formation and negligible side reactions of the electrode. The superior rate performances suggest that TSAC nanosheets can be promising anode materials for LIBs, particularly in high-power applications. For instance, lithium titanate is well known due to its capability to handle high cycling rates, even at 10 C, and the capacity of Li4Ti5O12 is around 108 mAh g−1 [39]. Moreover, after hybridizing with graphene and Ag, high capacities of 133 and 156 mAh g−1 at 10 C are achieved for the resulting LTO/graphene and LTO/Ag, respectively [40,41]. In addition, MXenes with similar laminar structure are also capable of handling high cycling rates, such as V2CTx (110 mAh g−1 at 10 C), Nb2CTx (125 mAh g−1 at 10 C), annealed Nb2CTx (342 mAh g−1 at 2 A g−1), f-T3C2 (110 mAh g−1 at 36 C) and porous T3C2Tx foam (101 mAh g−1 at 18 A g−1) [42,43,44,45].
Through Figure 6 and Figure 7, compared with bulk TSAC, TSAC nanosheets exhibited enhanced electrochemical properties as anode materials for LIB. According to the studies of lithium-ion uptake of other MAX phases, both MX and A layers show a possible redox reaction capability with lithium-ion [7,8,9]. In addition, after etching A layer from MAX phases, the resulting MXenes also show promising lithium-ion storage ability [44,46,47,48]. Compared to bulk TSAC, TSAC nanosheets can provide larger active surface area and more exposed Si atoms to promote the redox reactions of Ti3C2-Li and Si-Li; thus, the specific capacity of TSAC nanosheets is superior to that of bulk TSAC. The specific surface area (SSA) calculated using the BET equation for the TSAC nanosheets is 11.68 m2 g−1. This value is about three times higher than the bulk TSAC powders measured at around 4.25 m2 g−1. Moreover, TSAC nanosheets electrodes have better conductivity from their 2D graphene-like nanostructure, which can effectively promote the electron transfer and shorten the Li+ ions diffusion distance and the polarization, resulting in the improvement of their electrochemical performance. It is obvious that the semicircular arc of the electrochemical impedance spectroscopy (EIS) of TSAC nanosheets is smaller than that of bulk TSAC (Figure 7b), indicating that it has smaller charge transfer resistance. Specially, it can be anticipated that the electrochemical performance of TSAC nanosheets would be enhanced by optimizing and engineering the materials’ surfaces, structures and compositions, and/or by introducing additives as reported for other 2D materials, such as graphene [41,49,50,51], MoS2 [52,53,54] et al.

4. Conclusions

In this work, novel Ti3Si0.75Al0.25C2 ultrathin nanosheets as promising anode material for LIB are successfully developed by facile sonic exfoliating in alcohol. The nanosheets have a high capacity of ≈350 mAh g−1 at 200 mA g−1, high cycling stability and excellent rate performance (150 mAh g−1 after 200 cycles at 8000 mA g−1), which enhances the lithium-ion uptake capability in comparison with their bulk counterparts. It is noted that the reversible capacity of the nanosheets is about six times higher than the pristine bulk Ti3Si0.75Al0.25C2. In addition, more than 100 compounds have been found in the MAX family to date, and they all have similar potential due to their superior electrical conductivity, lamellar structure, very good stability even under severe environments and activated “A” layers for using as LIBs electrodes. Thus, our findings in this work are opening the door for the study on 2D MAX compounds as valuable LIBs electrodes, particularly for high power applications.

Author Contributions

Conceptualization, J.X. and M.H.; formal analysis, Q.W. and W.Y.; investigation, B.L.; writing—original draft preparation, J.X.; writing—review and editing, J.X. and M.H.; supervision, J.X. and M.H.; project administration, J.X. and M.H.; funding acquisition, J.X. and W.Y. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by National Natural Science Foundation of China, grant number 21671167 and 51602277. This research was also supported by Qinglan Project of Jiangsu Province.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

No new data were created or analyzed in this study. Data sharing is not applicable to this article.

Acknowledgments

The authors would like to thank Shiyanjia Lab (www.shiyanjia.com, accessed on 15 December 2021) for the support of Raman analysis.

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Eklund, P.; Beckers, M.; Jansson, U.; Högberg, H.; Hultman, L. The Mn+1AXn phases: Materials science and thin-film processing. Thin Solid Films 2010, 518, 1851–1878. [Google Scholar] [CrossRef] [Green Version]
  2. Wang, X.H.; Zhou, Y.C. Layered Machinable and Electrically Conductive Ti2AlC and Ti3AlC2 Ceramics: A Review. J. Mater. Sci. Technol. 2010, 26, 385–416. [Google Scholar] [CrossRef]
  3. Fu, L.; Xia, W. MAX Phases as Nanolaminate Materials: Chemical Composition, Microstructure, Synthesis, Properties, and Applications. Adv. Eng. Mater. 2021, 23, 2001191. [Google Scholar] [CrossRef]
  4. Sokol, M.; Natu, V.; Kota, S.; Barsoum, M.W. On the Chemical Diversity of the MAX Phases. Trends Chem. 2019, 1, 210–223. [Google Scholar] [CrossRef]
  5. Gupta, S.; Barsoum, M.W. On the tribology of the MAX phases and their composites during dry sliding: A review. Wear 2011, 271, 1878–1894. [Google Scholar] [CrossRef]
  6. Sun, Z.M. Progress in research and development on MAX phases: A family of layered ternary compounds. Int. Mater. Rev. 2013, 56, 143–166. [Google Scholar] [CrossRef]
  7. Wu, H.; Zhu, J.; Liu, L.; Cao, K.; Yang, D.; Gong, C.; Lei, H.; Hang, H.; Yao, W.; Xu, J. Intercalation and delamination of Ti2SnC with high lithium ion storage capacity. Nanoscale 2021, 13, 7355–7361. [Google Scholar] [CrossRef] [PubMed]
  8. Zhao, S.; Agnese, Y.D.; Chu, X.; Zhao, X.; Gogotsi, Y.; Gao, Y. Electrochemical Interaction of Sn-Containing MAX Phase (Nb2SnC) with Li-Ions. ACS Energy Lett. 2019, 4, 2452–2457. [Google Scholar] [CrossRef]
  9. Li, Y.; Ma, G.; Shao, H.; Xiao, P.; Lu, J.; Xu, J.; Hou, J.; Chen, K.; Zhang, X.; Li, M.; et al. Electrochemical Lithium Storage Performance of Molten Salt Derived V2SnC MAX Phase. Nano-Micro Lett. 2021, 13, 158. [Google Scholar] [CrossRef]
  10. Xu, J.; Zhao, M.-Q.; Wang, Y.; Yao, W.; Chen, C.; Anasori, B.; Sarycheva, A.; Ren, C.E.; Mathis, T.; Gomes, L.; et al. Demonstration of Li-Ion Capacity of MAX Phases. ACS Energy Lett. 2016, 1, 1094–1099. [Google Scholar] [CrossRef]
  11. Sengupta, A.; Rao, B.V.B.; Sharma, N.; Parmar, S.; Chavan, V.; Singh, S.K.; Kale, S.; Ogale, S. Comparative evaluation of MAX, MXene, NanoMAX, and NanoMAX-derived-MXene for microwave absorption and Li ion battery anode applications. Nanoscale 2020, 12, 8466–8476. [Google Scholar] [CrossRef] [PubMed]
  12. Luan, S.; Zhou, J.; Xi, Y.; Han, M.; Wang, N.; Gao, J.; Hou, L.; Gao, F. High Lithium-Ion Storage Performance of Ti3SiC2 MAX by Oxygen Doping. ChemistrySelect 2019, 4, 5319–5321. [Google Scholar] [CrossRef]
  13. Chen, X.; Zhu, Y.; Zhu, X.; Peng, W.; Li, Y.; Zhang, G.; Zhang, F.; Fan, X. Partially Etched Ti3AlC2 as a Promising High-Capacity Lithium-Ion Battery Anode. ChemSusChem 2018, 11, 2677–2680. [Google Scholar] [CrossRef] [PubMed]
  14. Zhu, J.; Chroneos, A.; Wang, L.; Rao, F.; Schwingenschlögl, U. Stress-enhanced lithiation in MAX compounds for battery applications. Appl. Mater. Today 2017, 9, 192–195. [Google Scholar] [CrossRef]
  15. Sun, Y.; Cheng, H.; Gao, S.; Sun, Z.; Liu, Q.; Liu, Q.; Lei, F.; Yao, T.; He, J.; Wei, S.; et al. Freestanding Tin Disulfide Single-Layers Realizing Efficient Visible-Light Water Splitting. Angew. Chem. Int. Ed. 2012, 51, 8727–8731. [Google Scholar] [CrossRef] [PubMed]
  16. Stark, M.S.; Kuntz, K.L.; Martens, S.J.; Warren, S.C. Intercalation of Layered Materials from Bulk to 2D. Adv. Mater. 2019, 31, 1808213. [Google Scholar] [CrossRef]
  17. Li, Z.; Zhang, X.; Cheng, H.; Liu, J.; Shao, M.; Wei, M.; Evans, D.G.; Zhang, H.; Duan, X. Confined Synthesis of 2D Nanostructured Materials toward Electrocatalysis. Adv. Energy Mater. 2019, 10, 1900486. [Google Scholar] [CrossRef]
  18. Tao, P.; Yao, S.; Liu, F.; Wang, B.; Huang, F.; Wang, M. Recent advances in exfoliation techniques of layered and non-layered materials for energy conversion and storage. J. Mater. Chem. A 2019, 7, 23512–23536. [Google Scholar] [CrossRef]
  19. Yoo, E.; Kim, J.; Hosono, E.; Zhou, H.-S.; Kudo, T.; Honma, I. Large Reversible Li Storage of Graphene Nanosheet Families for Use in Rechargeable Lithium Ion Batteries. Nano Lett. 2008, 8, 2277–2282. [Google Scholar] [CrossRef]
  20. Li, X.; Geng, D.; Zhang, Y.; Meng, X.; Li, R.; Sun, X. Superior cycle stability of nitrogen-doped graphene nanosheets as anodes for lithium ion batteries. Electrochem. Commun. 2011, 13, 822–825. [Google Scholar] [CrossRef]
  21. Naguib, M.; Mashtalir, O.; Carle, J.; Presser, V.; Lu, J.; Hultman, L.; Gogotsi, Y.; Barsoum, M.W. Two-Dimensional Transition Metal Carbides. ACS Nano 2012, 6, 1322–1331. [Google Scholar] [CrossRef]
  22. Zhang, X.; Xu, J.; Wang, H.; Zhang, J.; Yan, H.; Pan, B.; Zhou, J.; Xie, Y. Ultrathin Nanosheets of MAX Phases with Enhanced Thermal and Mechanical Properties in Polymeric Compositions: Ti3Si0.75Al0.25C2. Angew. Chem. Int. Ed. 2013, 52, 4361–4365. [Google Scholar] [CrossRef]
  23. Xu, J.; Yan, H.; Gu, D. Friction and wear behavior of polytetrafluoroethene composites filled with Ti3SiC2. Mater. Des. 2014, 61, 270–274. [Google Scholar] [CrossRef]
  24. Xu, J.; Zhu, J.; Gong, C.; Guan, Z.; Yang, D.; Shen, Z.; Yao, W.; Wu, H. Achieving high yield of Ti3C2Tx MXene few-layer flakes with enhanced pseudocapacior performance by decreasing precursor size. Chin. Chem. Lett. 2020, 31, 1039–1043. [Google Scholar] [CrossRef]
  25. Fan, X.; Yin, X.; Wang, L.; Greil, P.; Travitzky, N. Synthesis of Ti3SiC2-based materials by reactive melt infiltration. Int. J. Refract. Met. Hard Mater. 2014, 45, 1–7. [Google Scholar] [CrossRef]
  26. Schultz, T.; Frey, N.C.; Hantanasirisakul, K.; Park, S.; May, S.J.; Shenoy, V.B.; Gogotsi, Y.; Koch, N. Surface Termination Dependent Work Function and Electronic Properties of Ti3C2Tx MXene. Chem. Mater. 2019, 31, 6590–6597. [Google Scholar] [CrossRef] [Green Version]
  27. Han, F.; Luo, S.; Xie, L.; Zhu, J.; Wei, W.; Chen, X.; Liu, F.; Chen, W.; Zhao, J.; Dong, L.; et al. Boosting the Yield of MXene 2D Sheets via a Facile Hydrothermal-Assisted Intercalation. ACS Appl. Mater. Interfaces 2019, 11, 8443–8452. [Google Scholar] [CrossRef]
  28. Chen, K.; Qiu, N.; Deng, Q.; Kang, M.; Yang, H.; Baek, J.; Koh, Y.; Du, S.; Huang, Q.; Kim, H. Cytocompatibility of Ti3AlC2, Ti3SiC2, and Ti2AlN: In Vitro Tests and First-Principles Calculations. ACS Biomater. Sci. Eng. 2017, 3, 2293–2301. [Google Scholar] [CrossRef]
  29. Guo, W.; Posadas, A.B.; Demkov, A.A. Deal–Grove-like thermal oxidation of Si (001) buried under a thin layer of SrTiO3. J. Appl. Phys. 2020, 127, 055302. [Google Scholar] [CrossRef]
  30. Spanier, J.E.; Gupta, S.; Amer, M.; Barsoum, M.W. Vibrational behavior of the Mn+1AXn phases from first-order raman scattering (M = Ti, V, Cr, A = Si, X = C, N). Phys. Rev. B 2005, 71, 012103.1–012103.4. [Google Scholar] [CrossRef] [Green Version]
  31. Presser, V.; Naguib, M.; Chaput, L.; Togo, A.; Hug, G.; Barsoum, M.W. First-order Raman scattering of the MAX phases: Ti2AlN, Ti2AlC0.5N0.5, Ti2AlC, (Ti0.5V0.5)2AlC, V2AlC, Ti3AlC2, and Ti3GeC2. J. Raman Spectrosc. 2012, 43, 168–172. [Google Scholar] [CrossRef]
  32. Liu, Y.; Wang, W.; Ying, Y.; Wang, Y.; Peng, X. Binder-free layered Ti3C2/CNTs nanocomposite anodes with enhanced capacity and long-cycle life for lithium-ion batteries. Dalton Trans. 2015, 44, 7123–7126. [Google Scholar] [CrossRef] [PubMed]
  33. Pourali, Z.; Sovizi, M.; Yaftian, M. Two-Dimensional Ti3C2TX/CMK-5 nanocomposite as high performance anodes for lithium batteries. J. Alloy. Compd. 2018, 738, 130–137. [Google Scholar] [CrossRef]
  34. Lin, Z.; Sun, D.; Huang, Q.; Yang, J.; Barsoum, M.W.; Yan, X. Carbon nanofiber bridged two-dimensional titanium carbide as a superior anode for lithium-ion batteries. J. Mater. Chem. A 2015, 3, 14096–14100. [Google Scholar] [CrossRef]
  35. Naguib, M.; Come, J.; Dyatkin, B.; Presser, V.; Taberna, P.-L.; Simon, P.; Barsoum, M.W.; Gogotsi, Y. MXene: A promising transition metal carbide anode for lithium-ion batteries. Electrochem. Commun. 2012, 16, 61–64. [Google Scholar] [CrossRef] [Green Version]
  36. Shao, R.; Niu, J.; Zhu, F.; Dou, M.; Zhang, Z.; Wang, F. A facile and versatile strategy towards high-performance Si anodes for Li-ion capacitors: Concomitant conductive network construction and dual-interfacial engineerin. Nano Energy 2019, 63, 103824. [Google Scholar] [CrossRef]
  37. Wang, F.; Wang, B.; Li, J.; Wang, B.; Zhou, Y.; Wang, D.; Liu, H.; Dou, S. Prelithiation: A Crucial Strategy for Boosting the Practical Application of Next-Generation Lithium Ion Battery. ACS Nano 2021, 15, 2197–2218. [Google Scholar] [CrossRef]
  38. Tang, Q.; Zhou, Z.; Shen, P. Are MXenes Promising Anode Materials for Li Ion Batteries? Computational Studies on Electronic Properties and Li Storage Capability of Ti3C2 and Ti3C2X2 (X = F, OH) Monolayer. J. Am. Chem. Soc. 2012, 134, 16909–16916. [Google Scholar] [CrossRef]
  39. Michalska, M.; Krajewski, M.; Ziolkowska, D.; Hamankiewicz, B.; Andrzejczuk, M.; Lipinska, L.; Korona, K.P.; Czerwinski, A. Influence of milling time in solid-state synthesis on structure, morphology and electrochemical properties of Li4Ti5O12 of spinel structure. Powder Technol. 2014, 266, 372–377. [Google Scholar] [CrossRef]
  40. Michalska, M.; Krajewski, M.; Hamankiewicz, B.; Ziolkowska, D.; Korona, K.P.; Jasinski, J.B.; Kaminska, M.; Lipinska, L.; Czerwinski, A. Li4Ti5O12 modified with Ag nanoparticles as an advanced anode material in lithium-ion batteries. Powder Technol. 2014, 266, 372–377. [Google Scholar] [CrossRef]
  41. Yan, H.; Yao, W.; Fan, R.; Zhang, Y.; Luo, J.; Xu, J. Mesoporous Hierarchical Structure of Li4Ti5O12/Graphene with High Electrochemical Performance in Lithium-Ion Batteries. ACS Sustain. Chem. Eng. 2018, 6, 11360–11366. [Google Scholar] [CrossRef]
  42. Mashtalir, O.; Naguib, M.; Mochalin, V.N.; Agnese, Y.D.; Heon, M.; Barsoum, M.W.; Gogotsi, Y. Intercalation and delamination of layered carbides and carbonitrides. Nat. Commun. 2013, 4, 1716. [Google Scholar] [CrossRef] [PubMed]
  43. Naguib, M.; Halim, J.; Lu, J.; Cook, K.M.; Hultman, L.; Gogotsi, Y.; Barsoum, M.W. New Two-Dimensional Niobium and Vanadium Carbides as Promising Materials for Li-Ion Batteries. J. Am. Chem. Soc. 2013, 135, 15966–15969. [Google Scholar] [CrossRef]
  44. Zhao, J.; Wen, J.; Xiao, J.; Ma, X.; Gao, J.; Bai, L.; Gao, H.; Zhang, X.; Zhang, Z. Nb2CTx MXene: High capacity and ultra-long cycle capability for lithium-ion battery by regulation of functional groups. J. Energy Chem. 2021, 53, 387–395. [Google Scholar] [CrossRef]
  45. Zhao, Q.; Zhu, Q.; Miao, J.; Zhang, P.; Wan, P.; He, L.; Xu, B. Flexible 3D Porous MXene Foam for High-Performance Lithium-Ion Batteries. Small 2019, 15, 1904293. [Google Scholar] [CrossRef]
  46. Come, J.; Naguib, M.; Rozier, P.; Barsoum, M.W.; Gogotsi, Y.; Taberna, P.-L.; Morcrette, M.; Simon, P. A Non-Aqueous Asymmetric Cell with a Ti2C-Based Two-Dimensional Negative Electrode. J. Electrochem. Soc. 2012, 159, A1368–A1373. [Google Scholar] [CrossRef] [Green Version]
  47. Hui, X.; Zhao, D.; Wang, P.; Di, H.; Ge, X.; Zhang, P.; Yin, L. Oxide Nanoclusters on Ti3C2 MXenes to Deactivate Defects for Enhanced Lithium Ion Storage Performance. Small 2021, 2104439. [Google Scholar] [CrossRef] [PubMed]
  48. Liu, F.; Zhou, J.; Wang, S.; Wang, B.; Shen, C.; Wang, L.; Hu, Q.; Huang, Q.; Zhou, A. Preparation of High-Purity V2C MXene and Electrochemical Properties as Li-Ion Batteries. J. Electrochem. Soc. 2017, 164, A709–A713. [Google Scholar] [CrossRef]
  49. Li, Y.; Ou, C.; Zhu, J.; Liu, Z.; Yu, J.; Li, W.; Zhang, H.; Zhang, Q.; Guo, Z. Ultrahigh and Durable Volumetric Lithium/Sodium Storage Enabled by a Highly Dense Graphene-Encapsulated Nitrogen-Doped Carbon@Sn Compact Monolith. Nano Lett. 2020, 20, 2034–2046. [Google Scholar] [CrossRef] [PubMed]
  50. Xu, X.; Zeng, H.; Han, D.; Qiao, K.; Xing, W.; Rood, M.J.; Yan, Z. Nitrogen and Sulfur Co-Doped Graphene Nanosheets to Improve Anode Materials for Sodium-Ion Batteries. ACS Appl. Mater. Interfaces 2018, 10, 37172–37180. [Google Scholar] [CrossRef]
  51. Zhao, J.; Zhang, Y.; Zhang, F.; Liang, H.; Ming, F.; Alshareef, H.N.; Gao, Z. Partially Reduced Holey Graphene Oxide as High Performance Anode for Sodium-Ion Batteries. Adv. Energy Mater. 2018, 9, 1803215. [Google Scholar] [CrossRef]
  52. Wang, J.; Luo, C.; Gao, T.; Langrock, A.; Mignerey, A.C. An Advanced MoS2/Carbon Anode for High-Performance Sodium-Ion Batteries. Small 2015, 11, 473–481. [Google Scholar] [CrossRef] [PubMed]
  53. Jiang, H.; Ren, D.; Wang, H.; Hu, Y.; Guo, S.; Yuan, H.; Hu, P.; Zhang, L.; Li, C. 2D Monolayer MoS2-Carbon Interoverlapped Superstructure: Engineering Ideal Atomic Interface for Lithium Ion Storage. Adv. Mater. 2015, 27, 3687–3695. [Google Scholar] [CrossRef] [PubMed]
  54. Xu, X.; Fan, Z.; Yu, X.; Ding, S.; Yu, D.; Lou, X.W.D. A Nanosheets-on-Channel Architecture Constructed from MoS2 and CMK-3 for High-Capacity and Long-Cycle-Life Lithium Storage. Adv. Energy Mater. 2014, 4, 1400902. [Google Scholar] [CrossRef]
Nanomaterials 11 03449 g001 550
Figure 1. Schematic illustration of the advantages by using TSAC nanosheets-based electrode for Li-ion battery.
Figure 1. Schematic illustration of the advantages by using TSAC nanosheets-based electrode for Li-ion battery.
Nanomaterials 11 03449 g001
Nanomaterials 11 03449 g002 550
Figure 2. (a) XRD pattern and (b) SEM micrograph of the product synthesized by SHS.
Figure 2. (a) XRD pattern and (b) SEM micrograph of the product synthesized by SHS.
Nanomaterials 11 03449 g002
Nanomaterials 11 03449 g003 550
Figure 3. (a) SEM and (b,c) TEM images of the exfoliated TSAC nanosheets. (d) Energy-dispersive X-ray spectroscopy (EDX) analysis of TSAC nanosheets, performed on the center of the nanosheet in Figure 3c.
Figure 3. (a) SEM and (b,c) TEM images of the exfoliated TSAC nanosheets. (d) Energy-dispersive X-ray spectroscopy (EDX) analysis of TSAC nanosheets, performed on the center of the nanosheet in Figure 3c.
Nanomaterials 11 03449 g003
Nanomaterials 11 03449 g004 550
Figure 4. High resolution XPS spectra of TSAC nanosheets: (a) Ti 2p; (b) C 1s; (c) O1s; (d) Si 2p; (e) Al 2p; (f) Raman spectra of bulk TSAC and TSAC nanosheets.
Figure 4. High resolution XPS spectra of TSAC nanosheets: (a) Ti 2p; (b) C 1s; (c) O1s; (d) Si 2p; (e) Al 2p; (f) Raman spectra of bulk TSAC and TSAC nanosheets.
Nanomaterials 11 03449 g004
Nanomaterials 11 03449 g005 550
Figure 5. CV curves of (a) TSAC nanosheets and (b) bulk TSAC at a scan rate of 0.1 mV s−1.
Figure 5. CV curves of (a) TSAC nanosheets and (b) bulk TSAC at a scan rate of 0.1 mV s−1.
Nanomaterials 11 03449 g005
Nanomaterials 11 03449 g006 550
Figure 6. (a) The galvanostatic charge/discharge lithiation/delithiation curves of TSAC nanosheets; (b) the galvanostatic lithiation/delithiation curves of bulk TSAC; (c) specific delithiation (discharge) capacities of TSAC nanosheets and bulk TSAC vs. cycle number. The tests were carried at a current density of 200 mA g−1; (d) specific delithiation (discharge) capacities of TSAC nanosheets and bulk TSAC electrodes cycled at various current densities.
Figure 6. (a) The galvanostatic charge/discharge lithiation/delithiation curves of TSAC nanosheets; (b) the galvanostatic lithiation/delithiation curves of bulk TSAC; (c) specific delithiation (discharge) capacities of TSAC nanosheets and bulk TSAC vs. cycle number. The tests were carried at a current density of 200 mA g−1; (d) specific delithiation (discharge) capacities of TSAC nanosheets and bulk TSAC electrodes cycled at various current densities.
Nanomaterials 11 03449 g006
Nanomaterials 11 03449 g007 550
Figure 7. (a) Specific discharge capacity of TSAC nanosheets vs. cycle number at a current density of 8000 mA g−1; (b) Nyquist plots of bulk TSAC and TSAC nanosheets.
Figure 7. (a) Specific discharge capacity of TSAC nanosheets vs. cycle number at a current density of 8000 mA g−1; (b) Nyquist plots of bulk TSAC and TSAC nanosheets.
Nanomaterials 11 03449 g007
Publisher’s Note: MDPI stays neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Share and Cite

MDPI and ACS Style

Xu, J.; Wang, Q.; Li, B.; Yao, W.; He, M. Ti3Si0.75Al0.25C2 Nanosheets as Promising Anode Material for Li-Ion Batteries. Nanomaterials 2021, 11, 3449. https://doi.org/10.3390/nano11123449

AMA Style

Xu J, Wang Q, Li B, Yao W, He M. Ti3Si0.75Al0.25C2 Nanosheets as Promising Anode Material for Li-Ion Batteries. Nanomaterials. 2021; 11(12):3449. https://doi.org/10.3390/nano11123449

Chicago/Turabian Style

Xu, Jianguang, Qiang Wang, Boman Li, Wei Yao, and Meng He. 2021. "Ti3Si0.75Al0.25C2 Nanosheets as Promising Anode Material for Li-Ion Batteries" Nanomaterials 11, no. 12: 3449. https://doi.org/10.3390/nano11123449

APA Style

Xu, J., Wang, Q., Li, B., Yao, W., & He, M. (2021). Ti3Si0.75Al0.25C2 Nanosheets as Promising Anode Material for Li-Ion Batteries. Nanomaterials, 11(12), 3449. https://doi.org/10.3390/nano11123449

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