Open Access

Synthesis of Antimony Nanotubes via Facile Template-Free Solvothermal Reactions

  • Ruxue Li1,
  • Xiaohua Wang1Email author,
  • Xinwei Wang2Email author,
  • Haoran Zhang1,
  • Jingxin Pan1,
  • Jilong Tang1,
  • Dan Fang1,
  • Xiaohui Ma1,
  • Yongfeng Li3, 4,
  • Bin Yao3, 4,
  • Jie Fan1 and
  • Zhipeng Wei1
Nanoscale Research Letters201611:486

https://doi.org/10.1186/s11671-016-1697-x

Received: 1 July 2016

Accepted: 21 October 2016

Published: 3 November 2016

Abstract

Uniform antimony (Sb) nanotubes were successfully synthesized via a facile solvothermal method without the need for any surfactants or templates. The Sb nanotubes are confirmed to be pure rhombohedral phase and have better crystallinity. These nanotubes show middle-hollow and open-ended structures, as well as multi-walled structures with the wall thickness of about 10 nm. Also, they have an average size of the diameter of about 50 nm and the length of about 350 nm. On the basis of the structural and morphological studies, a possible rolling mechanism is proposed to explain the formation of Sb nanotubes. It is expected that uniform Sb nanotubes can further be used in wide applications.

Keywords

Sb nanotubes Solvothermal synthesis Rolling mechanism

Background

Since the discovery of carbon nanotubes, one-dimensional nanotubes have attracted much attention due to their peculiar physical properties and promising applications as interconnect and functional units in fabricating electronic, optoelectronic, thermoelectric, and electromechanical nanodevices and so on [14]. So far, a large number of reports have focused on the exploring whether other layered materials also can form tubular or similar nanostructures. Through constant efforts, various nanotubes have been successfully synthesized by means of their two-dimensional layer structure, such as boron nitride (BN), titanium dioxide (TiO2), tungsten disulfide (WS2), bismuth sulfide (Bi2S3), bismuth (Bi), and so on [59]. All the above mentioned reports indicate that substance possessing lamellar structures might be able to form nanotubes under favorable conditions. Similar to that of Bi, semimetallic antimony (Sb) has also a pseudolamellar structure and has interesting features such as low conduction band, effective mass, and high electron mobility [1013]. In particular, the effective mass components of the electron ellipsoids in Sb are much larger than those in Bi, while the effective mass components of the hole ellipsoids of Sb are of the same order of magnitude as those in Bi [14]. Thus, the particular transport properties of the electron can be expected in one-dimensional nanostructures of Sb, which make it become an interesting system for studying quantum confinement effects [15]. Among them, Sb nanowires have exhibited the interesting electronic properties, such as surface superconductivity, extremely large magnetoresistance, and high efficiency thermoelectricity generation [16, 17]. Recently, Sb nanowires have been synthesized by the pulsed electrodeposition and vapor phase deposition in anodic alumina templates [18, 19], self-assembly on graphite templates [20], and surfactant-assisted solvothermal synthesis [21, 22]. In addition, Sb nanotubes have been synthesized via the reduction acetylacetone-assisted antimony complexes process [23]. To the best of our knowledge, the template-assisted or the surfactant-assisted methods are the most popular synthetic strategies for the synthesis of one-dimensional nanostructures of Sb, which can control the oriented growth or uniform dispersal of nanomaterials. Unfortunately, the removal of the templates will give rise to poorly defined nanostructures from complex procedure, or the existence of organic surfactant will affect the properties of the Sb nanomaterials, which consequently have limited their large-scale production and further potential applications. However, there have been very few literature reports on the syntheses of Sb nanotubes by using without template-assisted or surfactant-assisted method. Therefore, it is highly desirable and significant, as well as a big challenge, to develop a facile route to directly synthesize the relatively straight and uniformly dispersed nanotubes of Sb.

Herein, we have synthesized relatively straight and uniform Sb nanotubes via a facile solvothermal method without any surfactants or templates. The synthesized Sb nanotubes are confirmed to be pure rhombohedral phase and show better crystallinity. The Sb nanotubes have middle-hollow, open-ended structures, and an average size of the diameter of about 50 nm and the length of about 350 nm. Based on the morphologies and structures, the formation mechanism of Sb nanotubes is discussed.

Methods

Synthesis of Antimony Nanotubes

All the chemical reagents used in this experiment are analytical grade. In our synthetic system, antimony chloride (SbCl3) as the Sb source was reduced to form Sb nanotubes via a solvothermal reduction by Zn powder at 200 °C for 10 h. Toluene was selected as the solvent because it is stable and can dissolve SbCl3. In a typical process, SbCl3 (521 mg) was dispersed in toluene (40 ml) under vigorous stirring at 5000 rad/min for 30 min. Subsequently, the mixed solution was transferred into a Teflon-lined stainless steel autoclave (50 mL), followed closely by the addition of zinc powers (75 mg). The autoclave was filled with the mixed solution up to 80 % of its total capacity, then sealed and maintained at 200 °C for 10 h. When the reaction was finished, the resultants were filtered off and rinsed with absolute alcohol, dilute hydrochloric acid, and deionized water for three times, respectively, then dried at 50 °C under vacuum.

Characterization

The XRD patterns of the products were collected on a Bruker (AXS D8) X-ray diffractometer with Cu Kα radiation (λ = 1.5406 Å). An accelerating voltage of 40 kV and emission current of 30 mA were adopted for the measurements. The morphologies of as-synthesized samples were characterized by field emission scanning electron microscope (FE-SEM, Hitachi-4800, Japan) and high-resolution transmission electron microscope (TEM, FEI Tecnai G2 F20, 200 kV). The local chemical compositions of the samples were examined by energy-dispersive X-ray spectroscopy (EDX) performed in the transmission electron microscope.

Results and Discussion

The XRD patterns of the powder samples are shown in Fig. 1a. All the diffraction peaks can be assigned to pure rhombohedral phase of Sb with lattice constants a = b = 4.307 Å, and c = 11.273 Å (JCPDS 85-1324), which is indicative of the formation of the Sb product from the complete reduction of Sb3+ by the Zn powder as reductant. And these peaks are sharp and well defined for the sample confirming the existence of pure phase crystalline Sb products. Furthermore, the EDX is performed to detect the chemical composition of as-obtained sample (Fig. 1b). From the spectrum, we can see that only Sb peaks are observed together with the Cu peak from the copper grid. And the mass ratio of Sb is 99.12 at.%, which also confirms the formation of the Sb and the purity of product.
Fig. 1

a The XRD pattern and b the EDX analysis of Sb nanotubes after filtered and rinsed

To observe the morphologies of as-synthesized samples, SEM images are shown in Fig. 2. The original sample without the unfiltered and unrinsed process shows not only the coexisting structures of tubular and lamellar Sb but also the clustered structures from unreacted Zn powers (Fig. 2a). The chemical composition of the sample also is detected by the EDX (Fig. 2a, insert), which indicates the original sample is composed of Sb (95.58 at.%) and Zn (2.44 at.%). Note that a half-rolling structure is displayed (the red dashed box in Fig. 2a), which suggests that the formation of Sb nanotube mainly depends on its lamellar structure. The similar results have been previously reported [69]. Compared with the original sample, the filtered and rinsed sample exhibits relatively neat and uniform tubular structures without the clustered phenomenon in Fig. 2b. The nanotubes have an average size of diameters of about 50 nm and lengths of about 350 nm. The above results illustrate that the filtered and rinsed post-processes are an important procedure for the purity of Sb nanotubes; thus, all of the samples have been precisely performing the post-processes before the characterization and analysis.
Fig. 2

SEM images of a the original sample and b the sample with filtered and rinsed for Sb nanotubes, in which the inset in a shows the EDX pattern of the original sample

TEM and HRTEM are used to further investigation of the detailed structure of the Sb nanotubes. The TEM image of Sb also demonstrate that the coexisting structures of tubular and lamellar of Sb (Fig. 3a), and the average size of Sb nanotubes is about 50 × 350 nm. To clearly observe tubular structure, the TEM image of an individual nanotube is selected (Fig. 3b), in which Sb nanotube has a middle-hollow, open-ended, and multi-walled structure. The wall thickness of Sb nanotube is about 10 nm. These morphologies indicate that Sb nanotube can be formed through the rolling up of regularly ordered molecular layers during the solvothermal treatment process, in which toluene as a solvent plays the role of a structure-directing agent and should provide a possible driving force to facilitate the rolling of lamellar structures at 200 °C for 10 h [20]. The selected area electron diffraction (SAED) pattern for the Sb nanotubes (Fig. 3b, insert) shows that brighter dots on the less bright ring can be indexed as the diffraction of (012) planes, indicative of the [012] radial direction of the Sb nanotubes. In addition, the HRTEM image of the enlarge corresponding area of the top of individual nanotube clearly exhibits that the interlayer spacing of the lattice planes for the Sb nanotube is about 0.311 nm (Fig. 3c, d), which is consistent with the previous reports [24].
Fig. 3

TEM images of a the coexisting with tubular and lamellar structures and b single nanotube for Sb. c, d HRTEM images of enlarge corresponding area of the top for single Sb nanotube, in which the inset in b shows the SAED pattern of the single Sb nanotube

Considering the coexisting of lamellar and tubular structures in our system, we propose that the formation of Sb nanotubes might also involve the rolling of its pseudolamellar structure, as shown in Fig. 4; the formation processes are as follows: First, some primary Sb atoms are formed by solvothermal reductive reaction at certain temperature and pressure. Second, the collision of these Sb atoms may provide the opportunity that each Sb atom is connected with three closest neighbors and thus forms trigonal pyramids by covalent bonds. These trigonal pyramids further form a folded Sb lamellar structure driven by the anisotropic growth tendency of Sb [10, 21]. In addition, the structures of these layers are puckered due to the presence of “lone pairs,” responsible for a weak van der Waals interaction between the adjacent layers [21]. When shaking in solvent, the Zn ions or solvent molecules may be intercalated into the adjacent layers to reduce van der Waals interaction at the edges of the layers and expand the spacing of neighboring layers during the heating process. As a result, the turbostratic restacked lamellar structures will become very easily cleaved into individual layer and roll into nanotube structures through driving force (Fig. 4c, d), similar to the formation of carbon nanotubes and other inorganic nanotubes for Bi, BN, and WS2 with the lamellar structures [59]. The driving force for the rolling of the layers can be generated due to one or more of the following reasons: (1) The asymmetric structures caused by hydrogen deficiency in surface layers, which may generate a asymmetric surface tension to drive the surface layer to cleave from the turbostratic restacked layers and to roll into tubular structures [25, 26]. (2) The thermal stress may initiate the rolling of the layers with reduced interlayer forces at the edges at high temperature [27]. (3) The mechanical tensions generated in the process of dissolution/crystallization of layers may be another driving force for the rolling of layers at high temperature and pressure. The difference of width between the layers can induce excess surface energy during the growth and crystallization of layers. In order to decrease the excess surface energy, the rolling structures of cleaved layers are formed [28, 29]. Since no template or other chemical surfactant was introduced in our study, the driving force may be in good agreement with (3) or (4) or the combined action of (3) and (4) at high temperature and pressure. As direct experimental evidences, the nanotube structures of half-rolled and wholly rolled lamellar layers can fully support the rolling formation of Sb nanotube from the above images of SEM and TEM. The formula of solvothermal reactions may be expressed as follows:
Fig. 4

The schematic depiction of proposed formation mechanism for Sb nanotubes

$$ 2{\mathrm{SbCl}}_3 + 3\mathrm{Z}\mathrm{n} = 2\mathrm{S}\mathrm{b} + 3{\mathrm{ZnCl}}_2 $$

However, our understanding of the formation mechanism for Sb nanotubes is limited during the solvothermal process. Therefore, further investigations would be necessary to clarify in detail the mechanism.

Conclusions

Sb nanotubes were successfully synthesized via a facile solvothermal process without the need for any surfactants or templates. In the synthetic system, antimony chloride as the Sb source was reduced to form Sb nanotubes by using Zn powder in toluene solvent at 200 °C for 10 h. The XRD analysis confirms that the Sb nanotubes are pure rhombohedral phase. The images of SEM and TEM reveal that the samples are the coexisting structures of lamellar and tubular Sb, in which uniform Sb nanotubes have a middle-hollow, open-ended, and multi-walled structure. And the Sb nanotubes have an average size of about 50 × 350 nm and the wall thickness of about 10 nm. On the basis of the structural and morphological studies, a possible rolling formation mechanism is proposed to explain the formation of Sb nanotubes. It is expected that uniform Sb nanotubes can further be used in wide applications.

Declarations

Acknowledgements

This work is supported by the National Natural Science Foundation of China (61307045, 61404009, 61474010, 61574022, 61504012, 61205038, 11404219, 11404161, 11574130, and 11274135), the Foundation of State Key Laboratory of High Power Semiconductor Lasers, the Developing Project of Science and Technology of Jilin Province (20130101026JC, 20160101255JC, 20160519007JH), the Project of Jilin Province Development and Reform (2014Y110), and the Project of Changchun Science and Technology (14KG018).

Authors’ Contributions

A task of the work was formulated by ZPW and XHW. RXL and XWW provided the idea and drafted the manuscript. JXP and HRZ carried out the synthesis of antimony nanotubes. XHM and YFL analyzed the X-ray diffraction patterns of the antimony nanotubes. JLT and DF participated in the SEM studies. BY and JF participated in the TEM studies. All authors read and approved the final manuscript.

Authors’ Information

Doctor RX L is a student of Changchun University of Science and Technology. His major research area is in nanomaterial science.

Competing Interests

The authors declare that they have no competing interests.

Open AccessThis article is distributed under the terms of the Creative Commons Attribution 4.0 International License (http://creativecommons.org/licenses/by/4.0/), which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.

Authors’ Affiliations

(1)
State Key Laboratory of High Power Semiconductor Laser, School of Science, Changchun University of Science and Technology
(2)
State Key Laboratory of High Power Semiconductor Laser, School of Materials Science and Engineering, Changchun University of Science and Technology
(3)
State Key Laboratory of Superhard Materials and College of Physics, Jilin University
(4)
Key Laboratory of Physics and Technology for Advanced Batteries (Ministry of Education), College of Physics

References

  1. Chiu P, Shih I (2004) A study of the size effect on the temperature-dependent resistivity of bismuth nanowires with rectangular cross-sections. Nanotechnology 11:1489–1492View ArticleGoogle Scholar
  2. Li L, Yang YW, Huang XH, Li GH, Ang R, Zhang LD (2006) Fabrication and electronic transport properties of Bi nanotube arrays. Appl Phys Lett 10:103119View ArticleGoogle Scholar
  3. Liang L, Xu Y, Wang C, Wen L, Fang Y, Mi Y et al (2015) Large-scale highly ordered Sb nanorod array anodes with high capacity and rate capability for sodium-ion batteries. Energy Environ Sci 10:2954–2962View ArticleGoogle Scholar
  4. Mo MS, Zeng JH, Liu XM, Yu WC, Zhang SY, Qian YT (2002) Controlled hydrothermal synthesis of thin single-crystal tellurium nanobelts and nanotubes. Adv Mater 14(22):1658–1662View ArticleGoogle Scholar
  5. Siria A, Poncharal P, Biance AL, Fulcrand R et al (2013) Giant osmotic energy conversion measured in a single transmembrane boron nitride nanotube. Nature 7438:455–458View ArticleGoogle Scholar
  6. Close T, Tulsyan G, Diaz CA, Weinstein SJ, Richter C (2015) Reversible oxygen scavenging at room temperature using electrochemically reduced titanium oxide nanotubes. Nat Nanotechnol 5:418–422View ArticleGoogle Scholar
  7. O’Neal KR, Cherian J, Zak A, Tenne R, Liu Z, Musfeldt JL (2016) High pressure vibrational properties of WS2 nanotubes. Nano Lett 2:993–999View ArticleGoogle Scholar
  8. Wang D, Xie T, Li Y (2009) Nanocrystals: solution-based synthesis and applications as nanocatalysts. Nano Res 1:30–46View ArticleGoogle Scholar
  9. Boldt R, Kaiser M, Köhler D, Krumeich F, Ruck M (2009) High-yield synthesis and structure of double-walled bismuth-nanotubes. Nano Lett 1:208–210View ArticleGoogle Scholar
  10. Mntungwa N, Khan M, Mlowe S, Revaprasadu N (2015) A simple route to alkylamine capped antimony nanoparticles. Mater Lett 145:239–242View ArticleGoogle Scholar
  11. Liu X, Du YC, Xu X, Zhou XS, Dai ZH, Bao JC (2016) Enhancing the anode performance of antimony through nitrogen-doped carbon and carbon nanotubes. J Phys Chem C 120:3214–3220View ArticleGoogle Scholar
  12. Hu LY, Zhu XS, Du YC, Li YF, Zhou XS, Bao JC (2015) A chemically coupled antimony/multilayer graphene hybrid as a high-performance anode for sodium-ion batteries. Chem Mater 27:8138–8145View ArticleGoogle Scholar
  13. Zhou XS, Liu X, Xu Y, Liu YX, Dai ZH, Bao JC (2014) An SbOx/reduced graphene oxide composite as a high-rate anode material for sodium-ion batteries. J Phys Chem C 118:23527–23534View ArticleGoogle Scholar
  14. Kim H, Cho J (2008) Template synthesis of hollow Sb nanoparticles as a high-performance lithium battery anode material. Chem Mater 20:1679–1681View ArticleGoogle Scholar
  15. Duan NQ, Tan Y, Yan D, Jia L, Chi B, Pu J et al (2016) Biomass carbon fueled tubular solid oxide fuel cells with molten antimony anode. Appl Energy 165:983–989View ArticleGoogle Scholar
  16. Heremans JP, Thrush CM, Morelli DT, Wu MC (2002) Thermoelectric power of bismuth nanocomposites. Phys Rev Lett 21:216801View ArticleGoogle Scholar
  17. Yang F, Liu K, Hong K, Reich D, Searson P, Chien C (1999) Large magnetoresistance of electrodeposited single-crystal bismuth thin films. Science 5418:1335–1337View ArticleGoogle Scholar
  18. Zhang Y, Li G, Wu Y, Zhang B, Song W, Zhang L (2002) Antimony nanowire arrays fabricated by pulsed electrodeposition in anodic alumina membranes. Adv Mater 17:1227–1230View ArticleGoogle Scholar
  19. Barati M, Chow J, Ummat P, Datars W (2001) Temperature dependence of the resistance of antimony nanowire arrays. J Phys Condens Mat 13:2955–2962View ArticleGoogle Scholar
  20. Wang X-S, Kushvaha S, Yan Z, Xiao W (2006) Self-assembly of antimony nanowires on graphite. Appl Phys Lett 23:233105Google Scholar
  21. Wang YW, Hong BH, Lee JY, Kim JS, Kim GH, Kim KS (2004) Antimony nanowires self-assembled from Sb nanoparticles. J Phys Chem B 43:16723–16726View ArticleGoogle Scholar
  22. Zhang W, Xu L, Xi G, Yu W, Qian Y (2004) Large-scale growth of hollow Sb microspheres. Chem Lett 11:1476–1477View ArticleGoogle Scholar
  23. Hu H, Mo M, Yang B, Shao M, Zhang S, Li Q et al (2003) A rational complexing-reduction route to antimony nanotubes. New J Chem 8:1161–1163View ArticleGoogle Scholar
  24. Wang DB, Yu DB, Peng YY, Meng ZY, Zhang SY, Qian YT (2003) Formation of antimony nanotubes via a hydrothermal reduction process. Nanotechnology 14:748–751View ArticleGoogle Scholar
  25. Zhang S, Peng LM, Chen Q, Du GH, Dawson G, Zhou WZ (2003) Formation mechanism of H2Ti3O7 nanotubes. Phys Rev Lett 91:256103View ArticleGoogle Scholar
  26. Xu FF, Hu J, Bando Y (2005) Tubular configurations and structure-dependent anisotropic strains in GaS multi-walled sub-microtubes. J Am Chem Soc 127:16860–16865View ArticleGoogle Scholar
  27. Li DP, Zheng Z, Lei Y, Yang FL et al (2011) From nanoplates to microtubes and microrods: a surfactant-free rolling mechanism for facile fabrication and morphology evolution of Ag2S films. Chem Eur J 17:7694–7700View ArticleGoogle Scholar
  28. Nakahira A, Kubo T, Numako C (2010) Formation mechanism of TiO2-derived titanate nanotubes prepared by the hydrothermal process. Inorg Chem 49:5845–5852View ArticleGoogle Scholar
  29. Kim JY, Kim KH, Kim HK, Park SH, Roh KC, Kim KB (2015) Template-free synthesis of ruthenium oxide nanotubes for high-performance electrochemical capacitors. ACS Appl Mater Interfaces 7(30):16686–16693View ArticleGoogle Scholar

Copyright

© The Author(s). 2016