Hierarchical Nanosheet-Based MS2 (M=Re, Mo, W) Nanotubes

Subscriber access provided by University of Sunderland

Functional Nanostructured Materials (including low-D carbon)

Hierarchical Nanosheet-Based MS2 (M=Re, Mo, W) Nanotubes Prepared by Templating Sacrificial Te Nanowires with Superior Lithium and Sodium Storage Capacity Sheng Liu, Wanwan Lei, Yan Liu, Qiquan Qiao, and Wen-Hua Zhang ACS Appl. Mater. Interfaces, Just Accepted Manuscript • DOI: 10.1021/acsami.8b14976 • Publication Date (Web): 05 Oct 2018 Downloaded from http://pubs.acs.org on October 7, 2018

Just Accepted “Just Accepted” manuscripts have been peer-reviewed and accepted for publication. They are posted online prior to technical editing, formatting for publication and author proofing. The American Chemical Society provides “Just Accepted” as a service to the research community to expedite the dissemination of scientific material as soon as possible after acceptance. “Just Accepted” manuscripts appear in full in PDF format accompanied by an HTML abstract. “Just Accepted” manuscripts have been fully peer reviewed, but should not be considered the official version of record. They are citable by the Digital Object Identifier (DOI®). “Just Accepted” is an optional service offered to authors. Therefore, the “Just Accepted” Web site may not include all articles that will be published in the journal. After a manuscript is technically edited and formatted, it will be removed from the “Just Accepted” Web site and published as an ASAP article. Note that technical editing may introduce minor changes to the manuscript text and/or graphics which could affect content, and all legal disclaimers and ethical guidelines that apply to the journal pertain. ACS cannot be held responsible for errors or consequences arising from the use of information contained in these “Just Accepted” manuscripts.

is published by the American Chemical Society. 1155 Sixteenth Street N.W., Washington, DC 20036 Published by American Chemical Society. Copyright © American Chemical Society. However, no copyright claim is made to original U.S. Government works, or works produced by employees of any Commonwealth realm Crown government in the course of their duties.

Page 1 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

ACS Applied Materials & Interfaces

Hierarchical Nanosheet-Based MS2 (M=Re, Mo, W) Nanotubes Prepared by Templating Sacrificial Te Nanowires with Superior Lithium and Sodium Storage Capacity Sheng Liu,† Wanwan Lei,† Yan Liu,† Qiquan Qiao,*,‡ and Wen-Hua Zhang*,† †

Sichuan Research Center of New Materials, Institute of Chemical Materials, China Academy of

Engineering Physics, Chengdu 610200, China. E-mail: [email protected] (Prof. W.-H. Zhang). ‡

Department of Electrical Engineering and Computer Sciences, South Dakota State University,

Brookings, SD 57007, USA. E-mails: [email protected] (Prof. Q. Qiao)

KEYWORDS: transition metal dichalcogenides; hierarchical nanotubes; template; lithium-ion batteries; sodium-ion batteries.

ACS Paragon Plus Environment

1

ACS Applied Materials & Interfaces 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Page 2 of 30

ABSTRACT: Hierarchical nanosheet-based nanotubes are very attractive due to that their unique structure endows them with large surface areas and exposes massive active sites for functional applications. We herein demonstrate a facile one-pot hydrothermal approach to fabricating the hierarchical nanosheet-based MS2 (M=Re, Mo, W) nanotubes by using Te nanowires as sacrificical templates. The hierarchical nanotubes show tube channels of ~30 nm and hierarchical channel walls with tunable thickness of up to ~50 nm. As exemplified for application in Li-ion and Na-ion batteries, the ReS2 hierarchical nanotubes exhibit excellent specific capacities (1137 mA h g-1 for Li-ion batteries and 375 mA h g-1 for Na-ion batteries at 0.1 A g-1 after 100 cycles), good cycling stabilities and high rate capabilities, demonstrating their application promise in the rechargeable batteries. This work may open up new opportunities for further exploration of new types of hierarchical nanostructures for applications, e.g., in catalysis, energy chemistry, and gas adsorption and separation.


2

Page 3 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


Inorganic compound nanotubes (NTs) are of great research significance from the point of view of fundamental science and practical applications, due to their unique structural features of a one-dimensional (1D) cylindrical interior cavity.1-8 Due to the wide availability of versatile templates, template-directed growth has been demonstrated to be an effective strategy for obtaining hollow nanostructures.9 However, the selective removal of the templates is quite tedious, and special care is often necessary to avoid the collapse of the external shells.9-11 Sacrificing template strategy is a potentially useful approach for overcoming this obstacle because the templates can be self-depleted during the synthetic process while retaining the merits of the templating method.10, 12-19 However, it is highly challenging to fabricate NTs of inorganic compounds such as the very attractive few-layered two-dimensional (2D) semiconducting materials (e.g., ReS2, MoS2 and WS2)20-28 via the sacrificing template strategies. 2D transition metal dichalcogenides (TMDs) such as MoS2 and WS2 have been revealed to be promising candidates for use in electrochemical energy storage compared to commercial graphite.29-35 Moreover, numerous studies have demonstrated that compared to the conventional NTs with smooth tube walls, the hierarchical nanotubes with few-layered nanosheets (HNTsFLNS) as tube walls exhibit higher specific surface areas and more abundant active edge sites, both of which are very favorable for achieving a superior electrochemical performance.14, 26-27, 3639

It is therefore imperative to design an efficient, universal synthetic strategy for obtaining

HNTs-FLNS.11 Benefiting from their outstanding electro-optics, chemical and structural anisotropy properties,40-46 the newly emerging ReS2 has been proved to be promising electrode material for use in lithium-sulfur batteries (LSBs),45 lithium-ion batteries (LIBs),41-44, 47 sodiumion batteries (SIBs),44 and potassium-ion batteries (KIBs).44 Despite the advances in the field of ReS2/C nanocomposites, the pure ReS2 still suffers from the restacking or aggregation during the


3


Page 4 of 30

intercalation/deintercalation process, which hinders its further development in rechargeable batteries. Herein, we have exploited a facile one-pot hydrothermal approach to the fabrication of MS2 (M=Re, Mo, W) HNTs-FLNS by using of Te nanowires (NWs) as sacrificing templates. In fact, Te NWs have been widely used as an efficient hard template to produce functional nanomaterials due to their facile synthesis on a large scale, easy processing, and high reactivity.48 To the best of our knowledge, this is the first success so far in obtaining sulfide hollow nanostructures via the sacrificing strategy of Te templates without a tedious post-treatment step for removing Te templates.48-52 Because ReS2 has been much less explored than MoS2 and WS2, it is chosen as the model system in this study to assess the applicability of such HNTs-FLNS for use in LIBs and SIBs. RESULTS AND DISCUSSION Experimentally, Te NW templates were fabricated by a reduction of Na2TeO3 with the environmentally benign ascorbic acid according to the reported process.53-55 The as-obtained Te NWs show a diameter of ~30 nm and a length more than 5 µm (Figure S1). The growth of ReS2 uniform shells around Te NW templates was realized through the hydrothermal reaction of ammonium perrhenate, thiourea and Te NW templates at 200 oC, and subsequently the Te NW templates were self-depleted at 240 oC in the one-pot hydrothermal process owing to the simultaneous Te-etching by thiourea.11, 56-60 Consequently, the intermediate product of Te/ReS2 core-shell NWs were transformed to ReS2 HNTs-FLNS without a tedious post-treatment step for removing Te NW templates.


4

Page 5 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


The scanning electron microscopy (SEM) image of the as-prepared ReS2 HNTs-FLNS in Figure 1a shows the uniform 1D morphology with the typical lengths more than 5 µm. As shown in the enlarged SEM image (Figure 1b), the tube walls of 1D nanostructures are constructed from the randomly aligned nanosheets and the open ends of 1D nanostructures are clearly indicative of the hollow interior nature (see more SEM images in Figure S2a-c). The transmission electron microscopy (TEM) image in Figure 1c shows the core-shell feature of the Te/ReS2 intermediate products, revealing that Te nanowires are firstly coated by few-layered ReS2 nanosheets at 200 o

C. As observed in Figure 1d, the tube channel and wall thickness of the ReS2 HNTs-FLNS are

~30 and ~50 nm, respectively. Considering the 30 nm diameter of the Te NW templates, the similar internal diameter and the remarkably increased external diameter of the ReS2 HNTsFLNS demonstrate the faithful coating of ReS2 shells around the Te NW templates. It is noted that the shell thickness can be easily tailored by changing the hydrothermal duration at 200 oC. The high-resolution transmission electron microscopy (HRTEM) image of the ReS2 HNTs-FLNS in Figure 1e reveals the layered nature of the ultrathin ReS2 nanosheets. Also, the number of the indicated layers is ~7 and the (002) interlayer spacing is ~0.61 nm, consistent with that of the bulk ReS2. Figure 1f shows the dark-field scanning transmission electron microscopy (STEM) image and the resultant energy dispersive X-ray spectroscopy (EDS) elemental mappings of Re and S, indicating the uniform distribution of both elements.


5


Page 6 of 30

Figure 1. (a, b) SEM images of the ReS2 HNTs-FLNS, (c) TEM image of the Te/ReS2 core-shell NWs. The ReS2 HNTs-FLNS: (d) TEM image, (e) HRTEM image, (f) the dark-field STEM image and the resultant EDS elemental mappings of Re and S.

To demonstrate the robustness of the sacrificing template strategy in this study, syntheses of other kinds of TMD HNTs-FLNS such as MoS2 and WS2 were performed. When the Re precursor (ammonium perrhenate) was replaced by the Mo (ammonium molybdate) or W (ammonium tungstate) precursors, the Te/MoS2 core/shell NWs (Figure 2a-b) and MoS2 HNTsFLNS (Figure 2c-d) or the Te/WS2 core/shell NWs (Figure 2f-g) and WS2 HNTs-FLNS (Figure 2h-i) with morphologies very similar to those of the Te/ReS2 core/shell NWs (Figure 1c) and ReS2 HNTs-FLNS (Figure 1d) were obtained under the hydrothermal conditions identical to those used for the growth of the ReS2 NT-FLNS. In the meantime, the results of XRD patterns


6

Page 7 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


confirm the cystal structures of MoS2 (JCPDS 75-1539, Figure 2e) and WS2 (JCPDS 84-1398, Figure 2j). Thus, the present work provides an efficient and universal templating strategy for the synthesis of 2D compound hierarchical nanotubes by templating sacrificial Te nanowires without a tedious post-treatment step for removing Te templates.

Figure 2. TEM images of (a, b) the Te/MoS2 core/shell NWs and (c, d) the MoS2 HNTs-FLNS; (e) XRD patterns of the Te/MoS2 core/shell NWs and MoS2 HNTs-FLNS. TEM images of (f, g) the Te/WS2 core/shell NWs and (h, i) the WS2 HNTs-FLNS; (j) XRD patterns of the Te/MoS2 core/shell NWs and MoS2 HNTs-FLNS.

Due to highly similarity in structural features for ReS2, MoS2 and WS2 HNTs-FLNS in this work, and the mush less studies on ReS2 in comparison with MoS2 and WS2 to date, we


7


Page 8 of 30

finally take the ReS2 HNTs-FLNS as a model system to study the crystal structure, composition and growth mechanism, and evaluate the electrochemical performance of the as-obtained ReS2 HNTs-FLNS as the potential LIB and SIB anodes. The powder X-ray diffraction (XRD) pattern in Figure 3a matches well with the triclinic ReS2 crystal phase (JCPDS 89-0341). The prominent peak at the 2θ angle of 14.5o corresponds to the (002) crystal plane of ReS2. Moreover, no diffraction related to the Te crystal structure appears, showing the complete removal of the Te NW templates. The EDS spectrum in Figure 3b shows the existence of S and Re elements (the atomic ratio of S/Re is ~2.07) but does not exhibit the signal of the Te element, demonstrating the formation of ReS2 and the complete removal of the Te templates. The survey X-ray photoelectron spectroscopy (XPS) measurements (Figure S3) further confirm the high purity of the obtained ReS2 HNTs-FLNS, in agreement with the XRD and EDS results discussed above. Figure 3c-d show the high-resolution Re 4f and S 2p spectra, which clearly indicate the formation of ReS2 without the inherent oxides. The ReS2 HNTs-FLNS show a BET specific surface area of ~10.9 m2 g-1 and a total pore volume of 0.06 cm3 g-1 (Figure S4a-b).


8

Page 9 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


Figure 3. The ReS2 HNTs-FLNS: (a) XRD pattern, (b) EDS spectrum, and the high-resolution XPS spectra of (c) Re 4f and (d) S 2p.

The temperature- and time-dependent products (designated by Roman letters I-IX in Figure 4a) were collected to investigate the evolution of the morphologies and crystal phases from the intermediate Te/ReS2 core/shell NWs to the final ReS2 HNTs-FLNS. Under hydrothermal duration of 2 h at 200 oC, some ReS2 nanosheets emerged on the surface of the Te NWs (product I in Figure 4b and S5). When the duration was increased to 8 h, a complete shell


9


Page 10 of 30

of ReS2 nanosheets was formed around the Te NW cores, leading to the faithful core/shell nanostructure (product II in Figure 4b and S6). The morphologies of the Te NWs of product I to II are essentially identical while the intensity of the (002) diffraction peak of ReS2 in the XRD patterns increased from product I to product II (Figure 4c), suggesting the good preservation of Te NW templates and the gradual growth of ReS2 shells during the initial hydrothermal process at 200 oC. When the hydrothermal temperature was raised from 200 to 240 oC within 0.5 h, the ReS2 shell became thicker (product III in Figure 4b and S7). Interestingly, a narrow and long interior cavity appeared within the Te NW templates, suggesting the self-etching of Te NWs, and thereby revealing the close relationship between Te self-etching and the hydrothermal temperature. When the hydrothermal process was carried out at 240 oC for another 1 h, the major part of Te NWs disappeared, and accordingly, the intensity of the Te diffraction peaks became much weaker (product IV in Figure 4b-c and S8). Simultaneously, the thickness of the ReS2 shell increased further. After 2 h at 240 oC (product V), most of the Te NW template was absent, resulting in the formation of a nanostructure with a completely hollow interior cavity observed in the TEM image (product V in Figure 4b and S9), whereas a very weak diffraction peak of Te was still observed in the XRD pattern (indicted by an asterisk in Figure 4c). Upon further prolonging the hydrothermal treatment to 4 h at 240 oC, no signal of the Te phase was found in the XRD pattern (product VI in Figure S10), demonstrating the complete removal of Te cores in this case. Therefore, it is concluded that the thickness of the ReS2 shells increases monotonically during the entire hydrothermal process (at both 200 and 240 oC) while the Te NW templates were barely etched at 200 oC and were dramatically etched and finally depleted at 240 oC. Additionally, control experiments were conducted as follows to reveal the Te selfdepletion mechanism of the Te/ReS2 core-shell NWs. a) The reaction temperature. When the


10

Page 11 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


hydrothermal reaction was performed at 200 oC for 24 h, a very small fraction of Te NW cores were etched for the Te/ReS2 core-shell NWs (product VIII in Figure S11). However, when the hydrothermal reaction was performed at 240 oC for more than 1 h, the Te/ReS2 core-shell NWs cannot be formed, and only an irregular particulate product was obtained (e.g., product IX for 6 h in Figure S12). XRD diffraction analysis cannot detect any Te signal, while the presence of ReS2 was clearly revealed. These results demonstrate that the growth of the Te/ReS2 core-shell NWs can only be obtained at lower hydrothermal temperatures (e.g., 150-200 oC), while the selfetching rate of the Te NW cores is much larger than the growth rate of the ReS2 shells at the higher hydrothermal temperatures (e.g., 240 oC). To summarize, the growth of the ReS2 shells was dominant in the initial hydrothermal process at 200 oC and the self-depletion of the Te NW cores became dominant during the subsequent hydrothermal process at 240 oC. b) The amount of thiourea. Experiments further revealed that the concentration of thiourea also played a critical role in the etching of Te NWs. When the feeding amount of thiourea decreased sharply to ¼ of the amount based on the parameters for the product VII (Figure 1c), Te NW cores could not be completely removed (Figure S13). In other words, only a sufficient amount of thiourea can deplete the Te NWs completely in this reaction system. c) The role of each reactant. To further elucidate the role of thiourea in the Te etching, several control experiments were performed using Te/C core/shell NWs. If only glucose and Te NWs were present during the hydrothermal process at 240 oC, Te NWs that were uniformly coated by thick shells of carbon were obtained (Figure S14a-b). For the above hydrothermal process, no change occurred after adding (Figure S14c-d). By contrast, the removal of Te NW cores and the formation of carbon nanotubes were clearly observed after adding Te core templates, glucose, and thiourea during the hydrothermal process (Figure S14e-f). These results provided strong evidence for the role of thiourea in the


11


Page 12 of 30

etching of Te NWs. d) The product of the Te-etching reaction. To determine the product of the Te-etching reaction, AgNO3 was intentionally added into the clear supernatant of product VII to precipitate the Te-containing ions. The XRD pattern of the precipitate (Figure S15) showed that the precipitate consisted of Ag2TeS3, AgSCN, Ag2S and NH4NO3. Therefore, it was deduced that solid Te NW cores were transformed to the aqueous thiotellurite solution (TeS32-) by the polysulfides, resulting in the self-depleting of Te NW cores and the formation of the ReS2 HNTsFLNS. e) The replacement of thiourea. To further confirm the above-mentioned Te-etching reaction caused by the polysulfides, the sulfur precursor of thiorea was replaced by other organic sulfides such as thioacetamide and L-cysteine. As expected, the ReS2 HNTs-FLNS with the similar morphlogy were successfully obtained (Figure S16). To summarize, ReS2 HNTs-FLNS have been fabricated through the simultaneous thiourea etching11,

56-60

during the one-pot

hydrothermal process.


12

Page 13 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


Figure 4. (a) The temperature- and time-dependent products (I-IX). (b) TEM images (all the scale bars are 50 nm) and (c) XRD patterns of the products (I-V). The Roman letters denote the products obtained with different hydrothermal temperature and duration. Namely, 200 oC kept for I) 2 h or II) 8 h; 200 oC kept for 8 h and then ramped to 240 oC within 0.5 h and 240 oC kept


13


Page 14 of 30

for III) 0 h, IV) 1 h, V) 2 h, VI) 4 h, or VII) 8 h; VIII) 200 oC kept for 24 h; IX) 240 oC kept for 6 h.

The electrochemical performances of the ReS2 HNTs-FLNS and the reference ReS2 microsphere anodes in Li-ion batteries were evaluated in the coin-type cells. The cyclic voltammetry (CV) curves of the ReS2 HNTs-FLNS are shown in Figure 5a. During the first cycle, the pronounced reduction peak at ~0.8 V is assigned to the reduction of LixReS2 to Li2S and Re and/or the formation of the solid electrolyte interphase (SEI) layers.41-44, 61-62 For the later cycles, the prominent reduction/oxidation peaks at 1.7-1.8/2.3-2.4 V are attributed to the Li2S/S redox pair.41-45 The oxidation peak at ~1.7 V is ascribed to the conversion reaction of Re and S to ReS2. The similar plateau regions in the discharge-charge profiles of the ReS2 HNTs-FLNS are shown in Figure S17a, c. The nearly overlapping discharge-charge profiles and CV curves indicate the superior cyclability of the ReS2 HNT-FLNS electrode. For reference, CV curves of the ReS2 microspheres in LIBs are provided in Figure S17b (SEM and TEM images in Figure S2d-f, XRD pattern in Figure S2g; N2 adsorption-desorption isotherm and corresponding pore size distribution plot in Figure S4c-d). Figure 5b compares the rate capabilities of the ReS2 HNTs-FLNS with that of the reference ReS2 microspheres. The ReS2 HNTs-FLNS electrode delivers the excellent rate capacities of 1087, 982, 878, 735 and 515 mA h g-1 at the current densities of 0.2, 0.5, 1, 2 and 5 A g-1, respectively. Notably, the rate performance of the ReS2 HNTs-FLNS in this work is superior to those of many previously reported ReS2-based nanostructures (Figure S18b).36, 41-44, 47 Once the current rate returns to 0.2 A g-1, the corresponding excellent capacity resumes after cycling at high rates. By contrast, the reference ReS2 microsphere electrode exhibits much lower


14

Page 15 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


rate capacities under the same measurement conditions. Figure 5c shows the cycling performances at 0.1 A g-1. The reference ReS2 microsphere electrode has the final charge capacity of 431 mA h g-1 after 100 cycles. Despite the decay in the initial several cycles, the capacity of the ReS2 HNTs-FLNS electrode gradually increases, and then becomes stable and delivers a very high reversible capacity of 1137 mA h g-1 after 100 cycles. The increase of the capacity during the cycling process may be related to the unique structure of the hierarchical nanosheet-based ReS2 nanotubes and the continuous formation of SEI layers.63 The Coulombic efficiency of ~99% indicates negligible side reactions during each discharge-charge cycle. The high cycling capacity of the ReS2 HNTs-FLNS electrode should be ascribed to the distinct structure of hierarchical nanosheet-based NTs with abundant active sites. A good cycling performance is also demonstrated at a relatively high rate of 1 A g-1 (Figure S18a). Electrochemical impedance spectroscopy (EIS) measurements of the newly assembled cells and the cycled cells at 0.1 A g-1 for 100 cycles were conducted to reveal the electron transport properties (Figure S19a-b). The ReS2 HNTs-FLNS electrode shows a decreased diameter of the semicircle in the high-to-medium frequency region, suggestive of lower resistance. As observed in the TEM images of the ReS2 HNTs-FLNS after LIB cycling test at 0.1 A g-1 for 100 cycles, the robust tubular structures are well preserved (Figure S19c-d). In brief, the excellent lithium storage capability of the ReS2 HNT-FLNS can be attributed to the unique structure of hierarchical nanosheet-based nanotubes with abundant active sites. To further exploit the application potentials of the present ReS2 HNTs-FLNS in energy storage, the sodium storage performance of the ReS2 HNTs-FLNS anodes and the reference ReS2 microsphere anodes were evaluated in the coin-type cells. The CV curves of the ReS2 HNTsFLNS in Figure 5d show a dominant peak at ~0.4 V in the first cathodic scan, which is assigned


15


Page 16 of 30

to the reduction of NaxReS2 to Na2S and Re and/or the formation of the solid electrolyte interphase (SEI) layers.44, 64-66 In the following cycles, the prominent reduction/oxidation peaks at 1.5-1.7/1.8 V are attributed to the reversible Na2S/S redox pair.44, 64 The discharge-charge profiles of the ReS2 HNTs-FLNS in SIBs shows the similar plateau regions (Figure S20a, c). For reference, CV curves of the ReS2 microspheres in SIBs are provided in Figure S20b. The results of rate capability measurements are shown in Figure 5e. When the current density changes stepwise from 0.2 to 0.5, 1, 2 and 5 A g-1, the ReS2 HNTs-FLNS electrode exhibits the reversibe capacities of 368, 341, 321, 299 and 250 mA h g-1, corresponding to the high capacity retention rates of 100%, 93%, 87%, 81% and 67%, respectively. Importantly, the high reversibe capacities can recover when the rate returns from high rates to 0.2 A g-1, indicating outstanding rate capability of the ReS2 HNTs-FLNS. For comparison, the reference ReS2 microsphere electrode shows much lower reversibe capacities at all current densities. Further, the cycling stability for 100 cycles at 0.1 A g-1 are dipicted in Figure 5f. The ReS2 HNTs-FLNS electrode delivers much better cycling performance (375 mA h g-1) than the reference ReS2 microsphere electrode (84 mA h g-1). Apparently, the superior lithium and sodium storage performance of the ReS2 HNTsFLNS is attributed to the fascinating 1D hollow nanostructure constructed from the few-layered ReS2 nanosheets. On the one hand, the 1D hierarchical structure effectively alleviates the restacking and aggregation of the ReS2 few-layers while the hollow interior efficiently accommodates the volume variation during the lithiation/delithiation process. On the other hand, the porous shells assembled from the randomly aligned ReS2 nanosheets broaden the electrolyteelectrode interface and offer abundant active sites as lithium-ion and sodium-ion reservoirs. Therefore, the ReS2 HNTs-FLNS exhibit excellent specific capacity, cycling stability and rate capability in rechargeable alkali (Li and Na) ion batteries.


16

Page 17 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


Figure 5. Electrochemical performance in lithium-ion batteries: (a) CV curves of the first five cycles at a scan rate of 0.1 mV s-1 for the ReS2 HNTs-FLNS electrodes, (b) rate capability and (c) cycling performances at a current density of 100 mA g-1 for the ReS2 HNTs-FLNS and microsphere electrodes. Electrochemical performance in sodium-ion batteries: (d) CV curves of the first five cycles at a scan rate of 0.1 mV s-1 for the ReS2 HNTs-FLNS electrodes, (e) rate


17


Page 18 of 30

capability and (f) cycling performances at a current density of 100 mA g-1 for the ReS2 HNTsFLNS and microsphere electrodes. CONCLUSIONS In summary, an efficient sacrificing Te template strategy has been developed for design of MS2 (M=Re, Mo, W) hierarchical nanotubes constructed from few-layered MS2 nanosheets. The uniform coating of the MS2 shells on Te NWs and the subsequent gradual self-depleting of the Te cores during one-pot hydrothermal synthesis have been clearly demonstrated. Owing to their distinct 1D hollow structural features, the ReS2 HNTs-FLNS exhibit excellent reversible capacities, cyclabilities and rate capabilities when evaluated as LIB and SIB anodes, and the application promise of these hierarchical nanotubes is clearly demonstrated.

EXPERIMENTAL SECTION Synthesis of Te nanowires: Te nanowires with a diameter of ~30 nm and length more than 5 µm (Figure S1) were fabricated through a previously reported hydrothermal reduction of Na2TeO3 with the environmentally benign ascorbic acid.54-55 Typically, 1.0 g of ascorbic acid (AA, 99%, Macklin, China) and 0.1 g of cetyltrimethylammonium bromide (CTAB, 99%, Aladdin, China) were added to a glass beaker filled with 30 mL of distilled water. Then, 0.052 g of Na2TeO3 (97%, Aladdin, China) was added to the solution, which was magnetically stirred for 30 min. Lastly, the solution was transferred to a 50 mL Teflon-lined autoclave and maintained at 90 ºC in an electric oven for 24 h. The as-obtained Te nanowire suspension was centrifugated under 10000 rpm for 10 min, and then re-dispersed in 10 mL of distilled water to form the Tetemplating dispersion for the following process.


18

Page 19 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


Synthesis of the MS2 (M=Re, Mo, W) HNTs-FLNS: The MS2 HNTs-FLNS were synthesized via a facile one-pot hydrothermal method. In brief, 6 mmol of NH2CSNH2 (thiourea, Alfa Aesar, 99%) and 0.33 mmol of NH4ReO4 (ammonium perrhenate, Wengjiang Chemical Reagent Co. Ltd., China, 98%) or (NH4)6Mo7O24•4H2O (ammonium molybdate tetrahydrate, Alfa Aesar, 99%) or (NH4)6W12O39•xH2O (ammonium tungstate oxide hydrate, Alfa Aesar, 99%) were added into 12 mL of deionized water. Then, the above solution was poured into a polypropylene (PPL) lined stainless autoclave (total volume: 25 mL) and 2 mL of the Tetemplating dispersion was added. The sealed autoclave was kept at 200 ºC in an electric oven for 8 h with subsequent ramping to 240 ºC within 0.5 h and keeping for another 8 h. After reaction, the autoclave was naturally cooled to room temperature. Through centrifuging and washing with distilled water for several times, the final powders were collected. For the reference ReS2 microspheres, the same procedures were followed whereas no Te-templating dispersion was added. Characterization: Transmission electron microscopy (TEM) images were acquired on a Hitachi HT-7700 (100 kV) microscope. Field emission scanning electron microscopy (FE-SEM) images were obtained on Zeiss Sigma HD instrument (15 kV), which equips with an energy dispersive X-ray spectroscopy (EDS) detector. High-resolution transmission electron microscopy was performed on a Zeiss LIBRA 200FE microscope using an accelerating voltage of 200 kV. Powder X-ray diffraction (XRD) patterns were taken on a PANalytical EMPYREAN diffractometer using Cu Kα radiation (λ=1.5418 Å). X-ray photoelectron spectra (XPS) were recorded on a Thermo Scientific ESCALAB 250Xi spectrometer using Al Kα radiation (hv=1486.6 eV). The specific surface area, total pore volume and pore size distribution were


19


Page 20 of 30

collected at 77 K on a basis of the nitrogen adsorption-desorption isotherms using a BrunauerEmmett-Teller (BET) analyzer (Micromeritics ASAP 2460 sorptometer). Electrochemical measurements: The coin-type half cells (CR2032) were assembled in a glove box filled with high-purity argon. The work electrodes were fabricated by coating a slurry mixture of active materials (70 wt.%), carbon black (20 wt.%) and sodium carboxyl methyl cellulose binder (CMC, 10 wt.%) onto a Cu foil. Subsequently, the work electrodes were dried overnight at 80 ºC in a vacuum oven. For LIBs, lithium foils were used as the counter electrode; Celgard 2400 polypropylene (PP) as the separator; 1.0 M LiPF6 in a solvent mixture of ethylene carbonate (EC), diethyl carbonate (DEC) and dimethyl carbonate (DMC) (volume ratio of 1:1:1) as the electrolyte. For SIBs, sodium foils were served as the counter electrode; glass fiber membranes as the separator; 1.0 M NaClO4 in EC and DEC (volume ratio of 1:1) with 10 wt.% fluoroethylene carbonate (FEC) additive as the electrolyte. The loading mass remained at about 1.0 mg cm-2. An electrochemical workstation (Bio-Logic VMP3) was adopted to measure the cyclic voltammetry (CV) curves at a sweep rate of 0.1 mV s-1 over a potential range of 0.01-3 V, and the Nyquist impedance (EIS) plots with a frequency between 100 kHz and 10 mHz. Galvanostatic charge/discharge measurements were executed by a battery tester (Land CT2001A, China).

ASSOCIATED CONTENT Supporting Information The following files are available free of charge.


20

Page 21 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


Survey XPS, BET, XRD, SEM and TEM images, galvanostatic charge-discharge profile, cycling performance at 1 A g-1, and EIS Nyquist impedance of the ReS2 HNTs-FLNS. (PDF) AUTHOR INFORMATION Corresponding Author *E-mails: [email protected] (Prof. Q. Qiao) and [email protected] (Prof. W.-H. Zhang). Notes The authors declare no competing financial interest. ACKNOWLEDGMENT This research was supported by the National Natural Science Foundation of China (51402242, 21701158) and the National Postdoctoral Program for Innovative Talents (BX201600138). QQ acknowledges financial support from NASA EPSCoR (NNX14AN22A) and NSF-MRI (Grant 1428992).

REFERENCES (1) Remškar, M. Inorganic Nanotubes. Adv. Mater. 2004, 16, 1497-1504. (2) Tenne, R. Inorganic Nanotubes and Fullerene-like Nanoparticles. Nat. Nanotechnol. 2006, 1, 103-111. (3) Rao, C. N. R.; Govindaraj, A. Synthesis of Inorganic Nanotubes. Adv. Mater. 2009, 21, 42084233. (4) Višić, B.; Panchakarla, L. S.; Tenne, R. Inorganic Nanotubes and Fullerene-Like


21


Page 22 of 30

Nanoparticles at the Crossroads Between Solid-State Chemistry and Nanotechnology. J. Am. Chem. Soc. 2017, 139, 12865-12878. (5) Yu, X.-Y.; Yu, L.; Lou, X. W. Metal Sulfide Hollow Nanostructures for Electrochemical Energy Storage. Adv. Energy Mater. 2016, 6, 1501333. (6) Yu, L.; Yu, X. Y.; Lou, X. W. D. The Design and Synthesis of Hollow Micro-/Nanostructures: Present and Future Trends. Adv. Mater. 2018, 30, 1800939. (7) Yu, L.; Hu, H.; Wu, H. B.; Lou, X. W. Complex Hollow Nanostructures: Synthesis and Energy-Related Applications. Adv. Mater. 2017, 29, 1604563. (8) Liu, D.-H.; Li, W.-H.; Zheng, Y.-P.; Cui, Z.; Yan, X.; Liu, D.-S.; Wang, J.; Zhang, Y.; Lü, H.Y.; Bai, F.-Y.; Guo, J.-Z.; Wu, X.-L. In Situ Encapsulating α-MnS into N,S-Codoped NanotubeLike Carbon as Advanced Anode Material: α → β Phase Transition Promoted Cycling Stability and Superior Li/Na-Storage Performance in Half/Full Cells. Adv. Mater. 2018, 30, 1706317. (9) Wang, X.; Feng, J.; Bai, Y.; Zhang, Q.; Yin, Y. Synthesis, Properties, and Applications of Hollow Micro-/Nanostructures. Chem. Rev. 2016, 116, 10983-11060. (10) Zhang, Q.; Wang, W.; Goebl, J.; Yin, Y. Self-templated Synthesis of Hollow Nanostructures. Nano Today 2009, 4, 494-507. (11) Cong, L.; Xie, H.; Li, J. Hierarchical Structures Based on Two-Dimensional Nanomaterials for Rechargeable Lithium Batteries. Adv. Energy Mater. 2017, 7, 1601906. (12) Yu, L.; Wu, H. B.; Lou, X. W. D. Self-Templated Formation of Hollow Structures for Electrochemical Energy Applications. Acc. Chem. Res. 2017, 50, 293-301. (13) Fang, X.; Zhao, X.; Fang, W.; Chen, C.; Zheng, N. Self-templating Synthesis of Hollow Mesoporous Silica and Their Applications in Catalysis and Drug Delivery. Nanoscale 2013, 5,


22

Page 23 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


2205-2218. (14) Hu, H.; Yu, L.; Gao, X.; Lin, Z.; Lou, X. W. Hierarchical Tubular Structures Constructed from Uultrathin TiO2(B) Nanosheets for Highly Reversible Lithium Storage. Energy Environ. Sci. 2015, 8, 1480-1483. (15) Shen, L.; Yu, L.; Yu, X.-Y.; Zhang, X.; Lou, X. W. Self-Templated Formation of Uniform NiCo2O4 Hollow Spheres with Complex Interior Structures for Lithium-Ion Batteries and Supercapacitors. Angew. Chem. Int. Ed. 2015, 54, 1868-1872. (16) Hou, L.; Lian, L.; Zhang, L.; Pang, G.; Yuan, C.; Zhang, X. Self-Sacrifice Template Fabrication of Hierarchical Mesoporous Bi-Component-Active ZnO/ZnFe2O4 Sub-Microcubes as Superior Anode Towards High-Performance Lithium-Ion Battery. Adv. Funct. Mater. 2015, 25, 238-246. (17) Zhao, J.; Zou, Y.; Zou, X.; Bai, T.; Liu, Y.; Gao, R.; Wang, D.; Li, G.-D. Self-template Construction of Hollow Co3O4 Microspheres from Porous Ultrathin Nanosheets and Efficient Noble Metal-free Water Oxidation Catalysts. Nanoscale 2014, 6, 7255-7262. (18) Zou, F.; Hu, X.; Li, Z.; Qie, L.; Hu, C.; Zeng, R.; Jiang, Y.; Huang, Y. MOF-Derived Porous ZnO/ZnFe2O4/C Octahedra with Hollow Interiors for High-Rate Lithium-Ion Batteries. Adv. Mater. 2014, 26, 6622-6628. (19) Li, R.; Yuan, Y.-P.; Qiu, L.-G.; Zhang, W.; Zhu, J.-F. A Rational Self-Sacrificing Template Route to Metal-Organic Framework Nanotubes and Reversible Vapor-Phase Detection of Nitroaromatic Explosives. Small 2012, 8, 225-230. (20) Hu, J.; Huang, B.; Zhang, C.; Wang, Z.; An, Y.; Zhou, D.; Lin, H.; Leung, M. K. H.; Yang, S. Engineering Stepped Edge Surface Structures of MoS2 Sheet Stacks to Accelerate the Hydrogen Evolution Reaction. Energy Environ. Sci. 2017, 10, 593-603.


23


Page 24 of 30

(21) Liu, G.; Robertson, A. W.; Li, M. M.-J.; Kuo, W. C. H.; Darby, M. T.; Muhieddine, M. H.; Lin, Y.-C.; Suenaga, K.; Stamatakis, M.; Warner, J. H.; Tsang, S. C. E. MoS2 Monolayer Catalyst Doped with Isolated Co Atoms for the Hydrodeoxygenation Reaction. Nat. Chem. 2017, 9, 810816. (22) Si, M.; Su, C.-J.; Jiang, C.; Conrad, N. J.; Zhou, H.; Maize, K. D.; Qiu, G.; Wu, C.-T.; Shakouri, A.; Alam, M. A.; Ye, P. D. Steep-slope Hysteresis-free Negative Capacitance MoS2 Transistors. Nat. Nanotechnol. 2018, 13, 24-28. (23) Zhang, J.; Wu, M.-H.; Shi, Z.-T.; Jiang, M.; Jian, W.-J.; Xiao, Z.; Li, J.; Lee, C.-S.; Xu, J. Composition and Interface Engineering of Alloyed MoS2xSe2(1–x) Nanotubes for Enhanced Hydrogen Evolution Reaction Activity. Small 2016, 12, 4379-4385. (24) Zhang, J.; Kang, W.; Jiang, M.; You, Y.; Cao, Y.; Ng, T.-W.; Yu, D. Y. W.; Lee, C.-S.; Xu, J. Conversion of 1T-MoSe2 to 2H-MoS2xSe2−2x Mesoporous Nanospheres for Superior Sodium Storage Performance. Nanoscale 2017, 9, 1484-1490. (25) Xu, J.; Zhang, J.; Zhang, W.; Lee, C.-S. Interlayer Nanoarchitectonics of Two-Dimensional Transition-Metal Dichalcogenides Nanosheets for Energy Storage and Conversion Applications. Adv. Energy Mater. 2017, 7, 1700571. (26) Shi, Z.-T.; Kang, W.; Xu, J.; Sun, Y.-W.; Jiang, M.; Ng, T.-W.; Xue, H.-T.; Yu, D. Y. W.; Zhang, W.; Lee, C.-S. Hierarchical Nanotubes Assembled from MoS2-carbon Monolayer Sandwiched Superstructure Nanosheets for High-performance Sodium Ion Batteries. Nano Energy 2016, 22, 27-37. (27) Shi, Z.-T.; Kang, W.; Xu, J.; Sun, L.-L.; Wu, C.; Wang, L.; Yu, Y.-Q.; Yu, D. Y. W.; Zhang, W.; Lee, C.-S. In Situ Carbon-Doped Mo(Se0.85S0.15)2 Hierarchical Nanotubes as Stable Anodes for High-Performance Sodium-Ion Batteries. Small 2015, 11, 5667-5674.


24

Page 25 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


(28) Kang, W.; Wang, Y.; Xu, J. Recent Progress in Layered Metal Dichalcogenide Nanostructures as Electrodes for High-performance Sodium-ion Batteries. J. Mater. Chem. A 2017, 5, 7667-7690. (29) Yun, Q.; Lu, Q.; Zhang, X.; Tan, C.; Zhang, H. Three‐Dimensional Architectures

Constructed from Transition‐Metal Dichalcogenide Nanomaterials for Electrochemical Energy Storage and Conversion. Angew. Chem. Int. Ed. 2018, 57, 626-646. (30) Manzeli, S.; Ovchinnikov, D.; Pasquier, D.; Yazyev, O. V.; Kis, A. 2D Transition Metal Dichalcogenides. Nat. Rev. Mater. 2017, 2, 17033. (31) Wang, S.; Guan, B. Y.; Yu, L.; Lou, X. W. Rational Design of Three-Layered TiO2@Carbon@MoS2 Hierarchical Nanotubes for Enhanced Lithium Storage. Adv. Mater. 2017, 29, 1702724. (32) Lin, H.; Yang, L.; Jiang, X.; Li, G.; Zhang, T.; Yao, Q.; Zheng, G. W.; Lee, J. Y. Electrocatalysis of Polysulfide Conversion by Sulfur-deficient MoS2 Nanoflakes for LithiumSulfur Batteries. Energy Environ. Sci. 2017, 10, 1476-1486. (33) Ghazi, Z. A.; He, X.; Khattak, A. M.; Khan, N. A.; Liang, B.; Iqbal, A.; Wang, J.; Sin, H.; Li, L.; Tang, Z. MoS2/Celgard Separator as Efficient Polysulfide Barrier for Long-Life LithiumSulfur Batteries. Adv. Mater. 2017, 29, 1606817. (34) Deng, Z.; Jiang, H.; Hu, Y.; Liu, Y.; Zhang, L.; Liu, H.; Li, C. 3D Ordered Macroporous MoS2@C Nanostructure for Flexible Li-Ion Batteries. Adv. Mater. 2017, 29, 1603020. (35) Chen, Y. M.; Yu, X. Y.; Li, Z.; Paik, U.; Lou, X. W. Hierarchical MoS2 Tubular Structures Internally Wired by Carbon Nanotubes as a Highly Stable Anode Material for Lithium-ion Batteries. Sci. Adv. 2016, 2, e1600021.


25


Page 26 of 30

(36) Zhuo, S.; Xu, Y.; Zhao, W.; Zhang, J.; Zhang, B. Hierarchical Nanosheet-Based MoS2 Nanotubes Fabricated by an Anion-Exchange Reaction of MoO3-Amine Hybrid Nanowires. Angew. Chem. Int. Ed. 2013, 52, 8602-8606. (37) Zhang, J.; Wu, M.; Liu, T.; Kang, W.; Xu, J. Hierarchical Nanotubes Constructed from Interlayer-expanded MoSe2 Nanosheets as A Highly Durable Electrode for Sodium Storage. J. Mater. Chem. A 2017, 5, 24859-24866. (38) Wang, J.; Liu, J.; Yang, H.; Chen, Z.; Lin, J.; Shen, Z. X. Active Sites-enriched Hierarchical MoS2 Nanotubes: Highly Active and Stable Architecture for Boosting Hydrogen Evolution and Lithium Storage. J. Mater. Chem. A 2016, 4, 7565-7572. (39) Ma, F. X.; Wu, H. B.; Xia, B. Y.; Xu, C. Y.; Lou, X. W. Hierarchical β‐Mo2C Nanotubes Organized by Ultrathin Nanosheets as a Highly Efficient Electrocatalyst for Hydrogen Production. Angew. Chem. Int. Ed. 2015, 54, 15395-15399. (40) Rahman, M.; Davey, K.; Qiao, S.-Z. Advent of 2D Rhenium Disulfide (ReS2): Fundamentals to Applications. Adv. Funct. Mater. 2017, 27, 1606129. (41) Zhang, Q.; Tan, S.; Mendes, R. G.; Sun, Z.; Chen, Y.; Kong, X.; Xue, Y.; Rümmeli, M. H.; Wu, X.; Chen, S.; Fu, L. Extremely Weak van der Waals Coupling in Vertical ReS2 Nanowalls for High-Current-Density Lithium-Ion Batteries. Adv. Mater. 2016, 28, 2616-2623. (42) Qi, F.; Chen, Y.; Zheng, B.; He, J.; Li, Q.; Wang, X.; Yu, B.; Lin, J.; Zhou, J.; Li, P.; Zhang, W. 3D Chrysanthemum-like ReS2 Microspheres Composed of Curly Few-layered Nanosheets with Enhanced Electrochemical Properties for Lithium-ion Batteries. J. Mater. Sci. 2017, 52, 3622-3629. (43) Qi, F.; He, J.; Chen, Y.; Zheng, B.; Li, Q.; Wang, X.; Yu, B.; Lin, J.; Zhou, J.; Li, P.; Zhang, W.; Li, Y. Few-layered ReS2 Nanosheets Grown on Carbon Nanotubes: A Highly Efficient Anode


26

Page 27 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


for High-performance Lithium-ion Batteries. Chem. Eng. J. 2017, 315, 10-17. (44) Mao, M.; Cui, C.; Wu, M.; Zhang, M.; Gao, T.; Fan, X.; Chen, J.; Wang, T.; Ma, J.; Wang, C. Flexible ReS2 Nanosheets/N-doped Carbon Nanofibers-Based Paper as a Universal Anode for Alkali (Li, Na, K) Ion Battery. Nano Energy 2018, 45, 346-352. (45) Gao, J.; Li, L.; Tan, J.; Sun, H.; Li, B.; Idrobo, J. C.; Singh, C. V.; Lu, T.-M.; Koratkar, N. Vertically Oriented Arrays of ReS2 Nanosheets for Electrochemical Energy Storage and Electrocatalysis. Nano Lett. 2016, 16, 3780-3787. (46) Hafeez, M.; Gan, L.; Saleem Bhatti, A.; Zhai, T. Rhenium Dichalcogenides (ReX2, X=S or Se): An Emerging Class of TMDs Family. Mater. Chem. Front. 2017, 1, 1917-1932. (47) Wang, H.; Yang, X.; Chai, Y.; Liu, S.; Yuan, R. Ultrathin ReS2 Nanosheets Growing on Ordered Microporous Carbon for High Capacity Lithium Ion Batteries. J. Alloys Compd. 2018, 767, 204-209. (48) He, Z.; Yang, Y.; Liu, J.-W.; Yu, S.-H. Emerging Tellurium Nanostructures: Controllable Synthesis and Their Applications. Chem. Soc. Rev. 2017, 46, 2732-2753. (49) Liang, H. W.; Liu, S.; Gong, J. Y.; Wang, S. B.; Wang, L.; Yu, S. H. Ultrathin Te Nanowires: An Excellent Platform for Controlled Synthesis of Ultrathin Platinum and Palladium Nanowires/Nanotubes with Very High Aspect Ratio. Adv. Mater. 2009, 21, 1850-1854. (50) Zhang, G.; Yu, Q.; Yao, Z.; Li, X. Large Scale Highly Crystalline Bi2Te3 Nanotubes through Solution Phase Nanoscale Kirkendall Effect Fabrication. Chem. Commun. 2009, 45, 2317-2319. (51) Wang, K.; Liang, H.-W.; Yao, W.-T.; Yu, S.-H. Templating Synthesis of Uniform Bi2Te3 Nanowires with High Aspect Ratio in Triethylene Glycol (TEG) and Their Thermoelectric Performance. J. Mater. Chem. 2011, 21, 15057-15062. (52) Chai, Z.; Wang, H.; Suo, Q.; Wu, N.; Wang, X.; Wang, C. Thermoelectric Metal Tellurides


27


Page 28 of 30

with Nanotubular Structures Synthesized by the Kirkendall Effect and Their Reduced Thermal Conductivities. Crystengcomm 2014, 16, 3507-3514. (53) Yang, H.; Finefrock, S. W.; Caballero, J. D. A.; Wu, Y. Environmentally Benign Synthesis of Ultrathin Metal Telluride Nanowires. J. Am. Chem. Soc. 2014, 136, 10242-10245. (54) Xi, G.; Liu, Y.; Wang, X.; Liu, X.; Peng, Y.; Qian, Y. Large-scale Synthesis, Growth Mechanism, and Photoluminescence of Ultrathin Te Nanowires. Cryst. Growth Des. 2006, 6, 2567-2570. (55) Li, H.; Ren, C.; Xu, S.; Wang, L.; Yue, Q.; Li, R.; Zhang, Y.; Xue, Q.; Liu, J. Te-template Approach to Aabricating Ternary TeCuPt Alloy Nanowires with Enhanced Catalytic Performance towards Oxygen Reduction Reaction and Methanol Oxidation Reaction. J. Mater. Chem. A 2015, 3, 5850-5858. (56) Shaw, W. H. R.; Walker, D. G. The Decomposition of Thiourea in Water Solutions. J. Am. Chem. Soc. 1956, 78, 5769-5772. (57) Rio, L. G.; Munkley, C. G.; Stedman, G. Kinetic Study of the Stability of (NH2)2CSSC(NH2)22+. J. Chem. Soc., Perkin Trans. 2 1996, 0, 159-162. (58) Timchenko, V. P.; Novozhilov, A. L.; Slepysheva, O. A. Kinetics of Thermal Decomposition of Thiourea. Russ. J. Gen. Chem. 2004, 74, 1046-1050. (59) Babo, J. M.; Wolff, K. K.; Schleid, T. Two New Cesium Thiotellurates: Cs2[TeS2] and Cs2[TeS3]. Z. Anorg. Allg. Chem. 2013, 639, 2875-2881. (60) Gerl, H.; Eisenmann, B.; Roth, P.; Schäfer, H. Zur Darstellung und Kristallstruktur der Thiotellurite BaTeS3 · 2H2O und (NH4)2TeS3. Z. Anorg. Allg. Chem. 1974, 407, 135-143. (61) Wang, H.-C.; Cui, Z.; Fan, C.-Y.; Liu, S.-Y.; Shi, Y.-H.; Wu, X.-L.; Zhang, J.-P. 3 D Porous CoS2 Hexadecahedron Derived from MOC toward Ultrafast and Long-Lifespan Lithium Storage.


28

Page 29 of 30 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


Chem.-Eur. J. 2018, 24, 6798-6803. (62) Yu, L.; Yang, J. F.; Lou, X. W. Formation of CoS2 Nanobubble Hollow Prisms for Highly Reversible Lithium Storage. Angew. Chem. Int. Ed. 2016, 55, 13422-13426. (63) Zhang, S.; Chowdari, B. V. R.; Wen, Z.; Jin, J.; Yang, J. Constructing Highly Oriented Configuration by Few-Layer MoS2: Toward High-Performance Lithium-Ion Batteries and Hydrogen Evolution Reactions. ACS Nano 2015, 9, 12464-12472. (64) Gao, Z.; Yu, X.; Zhao, J.; Zhao, W.; Xu, R.; Liu, Y.; Shen, H. Synthesis of Long Hierarchical MoS2 Nanofibers Assembled from Nanosheets with an Expanded Interlayer Distance for Achieving Superb Na-ion Storage Performance. Nanoscale 2017, 9, 15558-15565. (65) Hou, B.-H.; Wang, Y.-Y.; Guo, J.-Z.; Ning, Q.-L.; Xi, X.-T.; Pang, W.-L.; Cao, A.-M.; Wang, X.; Zhang, J.-P.; Wu, X.-L. Pseudocapacitance-boosted Ultrafast Na Storage in A Pie-like FeS@C Nanohybrid as An Advanced Anode Material for Sodium-ion Full Batteries. Nanoscale 2018, 10, 9218-9225. (66) Hou, B.-H.; Wang, Y.-Y.; Guo, J.-Z.; Zhang, Y.; Ning, Q.-L.; Yang, Y.; Li, W.-H.; Zhang, J.P.; Wang, X.-L.; Wu, X.-L. A Scalable Strategy To Develop Advanced Anode for Sodium-Ion Batteries: Commercial Fe3O4-Derived Fe3O4@FeS with Superior Full-Cell Performance. ACS Appl. Mater. Interfaces 2018, 10, 3581-3589.


29


Page 30 of 30

For Table of Content Only


30

Hierarchical Nanosheet-Based MS2 (M=Re, Mo, W) Nanotubes

Recommend Documents